high strength steel sheet and high strength zinc coated steel sheet which have excellent ductility a

专利摘要:
high strength steel sheet and high strength zinc coated steel sheet which have excellent ductility and stretch-flanging ability and method of manufacture thereof. The present invention relates to a high strength steel plate which includes by weight percentage: 0.05 to 0.4% c; 0.1 to 2.5% of itself; 1.0 to 3.5% min; 0.001 to 0.03 wt%; 0.0001 to 0.01% s; 0.001 to 2.5% al; 0.0001 to 0.01% n; 0.0001 to 0.008% of o; and a remaining iron compound and unavoidable impurities, wherein a sheet steel structure contains by volume fraction 10 to 50% of a ferrite phase, 10 to 50% of a hardened martensite phase, and a remaining hard phase, where a hardness of 98% is 1.5 or more times as high as a hardness of 2% in a range from 1/8 to 3/8 of a sheet steel thickness, where a kurtosis k * of the Hardness distribution between 2% hardness and 98% hardness is -1.2 to -0.4, and where an average crystal grain size in the steel plate structure is 10 <109> m or less.
公开号:BR112013006143B1
申请号:R112013006143-0
申请日:2011-09-16
公开日:2018-12-18
发明作者:Hiroyuki Kawata；Naoki Maruyama；Akinobu Murasato；Naoki Yoshinaga；Chisato Wakabayashi；Noriyuki Suzuki
申请人:Nippon Steel & Sumitomo Metal Corporation；
IPC主号:

专利说明:

Invention Patent Description Report for CHAPA
HIGH-RESISTANCE STEEL AND STEEL PLATE COATED WITH HIGH-RESISTANCE ZINC THAT HAVE EXCELLENT DUCTILITY AND STRETCH-FLANGE CAPACITY AND METHOD OF MANUFACTURING THE SAME ”.
Field of technique [001] The present invention relates to a high-strength steel sheet and a high-strength zinc-coated steel sheet that have excellent ductility and stretch-flanging capabilities and a method of manufacturing them.
[002] Priority is claimed in Japanese patent applications ²² . 2010-208329 and 2010-208330, deposited on September 16, 2010, the content of which is hereby incorporated by reference. Background to the technique [003] In recent years, there has been a growing demand for a high-strength steel sheet used in a vehicle, or the like, and a high-strength cold-rolled steel sheet with a maximum tensile strength of 900 MPa or more has also been used.
[004] Generally, as the strength of a steel sheet is optimized, ductility and stretch-flanging capacity are reduced, and workability is degraded. However, a high strength steel plate with sufficient workability has been required in recent years.
[005] As a conventional technique to optimize the ductility and stretch-flanging capacity of a high-strength steel sheet, a highly extensible galvanized steel sheet, which has a composition that contains by weight percentage, C: 0, 05 to 0.20%, Si: 0.3 to 1.8%, Mn: 1.0 to 3.0%, S: 0.005% or less, the remainder of Fe and unavoidable impurities, has a composite structure that includes ferrite, tempered martensite, retained austenite, and phase
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2/104 low temperature transformation, and contains by volume percentage 30% or more of ferrite, 20% or more of tempered martensite, 2% or more of retained austenite, in which the average crystal grain sizes of ferrite and tempered martensite is 10 pm or less, is an exemplary model (see Patent Document 1, for example).
[006] In addition, as a conventional technique to optimize the workability of a high-strength steel sheet, a highly extensible cold-rolled steel sheet, in which the amounts of C, Si, Μη, P, S, Al and N are adjusted, which additionally contain 3% or more of ferrite and a total of 40% or more of bainite containing carbide and martensite containing carbide as metal structures of the steel plate containing one or more of Ti, Nb, V, B, Cr, Mo, Cu, Ni and Ca, as needed, in which the total amount of ferrite, bainite and martensite is 60% or more, and which additionally has a structure in which the number of ferrite grains that contain cementite, martensite or austenite retained in it corresponds to 30% or more of the total number of ferrite grains and has tensile strength of 780 MPa or more, it is an exemplary model (see Patent Document 2, for example ).
[007] In addition, as a conventional technique to optimize the stretch-flanging ability of a high strength steel sheet, a steel sheet in which a difference in hardness between a hard part and a soft part of the steel sheet is reduced model consists of an example. For example, Patent Document 3 presents a technique in which the standard deviation of hardness in the steel sheet is reduced and uniform hardness is given for the entire steel sheet. Patent Document 4 presents a technique in which hardness in the hard part is reduced by heat treatment and the difference in its hardness in the soft part is reduced. Patent Document 5 presents a technique in which the difference in hardness of the soft part is
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3/104 reduced by setting the relatively soft bainite hard part.
[008] Additionally, as a conventional technique to optimize the stretch-flanging capacity of a high-strength steel plate, a steel plate, which has a structure that contains for an area ratio 40 to 70% tempered martensite and a remainder of ferrite, in which a ratio between an upper limit value and a lower limit value of Mn concentration in a cross section in a thickness direction of the steel plate is reduced (see Patent Document 6, for example ) can be exemplified.
Citation list
Patent Document
Patent Document 1 Patent application unexamined Japanese First Publication No. ^2. 2001-192768 [Patent Document 2] Patent application unexamined Japanese First Publication No. ^2. 2004-68050 [Patent Document 3] Patent application unexamined Japanese First Publication No. ^2. 2008-266779 [Patent Document 4] Patent application unexamined Japanese First Publication No. ^2. 2007-302918 [Patent Document 5] Patent application unexamined Japanese First Publication No. ^2. 2004-263270 [Patent Document 6] Patent application unexamined Japanese First Publication No. ^2. 2010-65307
Summary of the invention
Technique problem [009] According to conventional techniques, however, the workability of high strength steel sheet with a strength
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4/104 maximum traction of 900 MPa or more is insufficient, and it has been desired, in addition, to optimize ductility and stretch-flanging capacity and thus optimize workability.
[0010] The present invention is made in view of such circumstances and its objective is to provide a high strength steel sheet, which has excellent ductility and stretch-flanging capacity and has excellent workability, while the resistance is ensured in such a way that the maximum tensile strength becomes 900 MPa or more, and a method of manufacturing it. Solution to the problem [0011] The present inventor conducted an intensive study in order to solve the above problems. As a consequence of this, the present inventor has discovered that it is possible to ensure a maximum tensile strength as high as 900 MPa or more and to significantly optimize ductility and stretch-flanging capacity (orifice expansion property) by allowing the steel plate has a large difference in hardness by increasing a microdistribution of Mn within the steel plate and has a sufficiently small average grain size by controlling the dispersion in the hardness distribution.
[1] A high-strength steel plate that has excellent ductility and stretch-flanging capacity, which includes by weight percentage: 0.05 to 0.4% C; 0.1 to 2.5% Si; 1.0 to 3.5% Mn; 0.001 to 0.03% P; 0.0001 to 0.01% S; 0.001 to 2.5% Al; 0.0001 to 0.01% N; 0.0001 to 0.008% O; and a remainder composed of iron and unavoidable impurities, in which a steel plate structure contains by volume fraction 10a 50% of a ferrite phase, 10a 50% of a tempered martensite phase, and a remaining hard phase, in which when a plurality of measurement regions with diameters of 1 pm or less are adjusted in a range from 1/8 to 3/8 thickness
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5/104 of the steel plate, the hardness measurement values in the plurality of measurement regions are arranged in ascending order to obtain a hardness distribution, an integer NO, 02, which consists of a number obtained by multiplying a total number of the hardness measurement values by 0.02 and, if present, by rounding up a decimal number, a hardness of a measurement value is obtained which is an N0.02-th largest value from a hardness measurement value is considered to be a hardness of 2%, an integer NO, 98 which is a number obtained by multiplying the total number of hardness measurement values by 0.98 and, if present, by rounding down the decimal number is obtained, and a hardness of a measurement value consisting of a N0.98-th largest value from the lowest hardness measurement value is considered to be a 98% hardness, the 98% hardness is 1, 5 or more times as high as 2% hardness , where a K * kurtosis of the hardness distribution between the hardness of 2% and the hardness of 98% is equal to or greater than -1.2 and equal to or less than -0.4, and where an average grain size in the steel plate structure is 10 pm or less.
[2] The high-strength steel sheet that has excellent ductility and stretch-flanging capacity, according to [1], in which a difference between a maximum and a minimum value of the concentration of Mn in a base iron in a thickness range from 1/8 to 3/8 of the steel plate is equal to or greater than 0.4% and equal to or less than 3.5% when converted to the mass percentage.
[3] High-strength steel sheet that has excellent ductility and stretch-flanging capability, according to [1] or [2], where when a section from 2% hardness to 98% hardness is equally divided into 10 parts, and 10 1/10 sections are adjusted, a number of the hardness measurement values in each 1/10 section is 2 to 30% of a number of all measurement values.
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6/104 [4] The high strength steel plate that has excellent ductility and stretch-flanging capacity, according to any one of [1] to [3], where the hard phase includes either or both of them bainitic ferrite phase and a 10 to 45% bainite phase for a fraction by volume, and a fresh martensite phase of 10% or less.
[5] The high strength steel sheet which has excellent ductility and stretch-flanging capacity, according to any of [1] to [4], in which the steel sheet structure additionally includes 2 to 25 % of a phase of austenite retained.
[6] The high-strength steel sheet that has excellent ductility and stretch-flanging capability, according to any of [1] to [5], which additionally includes, by mass percentage one or more than 0.005 to 0.09% Ti; and 0.005 to 0.09% Nb.
[7] The high-strength steel sheet that has excellent ductility and stretch-flanging capability, according to any of [1] to [6], which additionally includes, by mass percentage one or more of: 0 .0001 to 0.01% B; 0.01 to 2.0% Cr; 0.01 to 2.0% Ni; 0.01 to 2.0% Cu; and 0.01 to 0.8% Mo.
[8] The high-strength steel sheet which has excellent ductility and stretch-flanging capacity, according to any of [1] to [7], which additionally includes, by mass percentage: 0.005 to 0.09 % of V.
[9] The high-strength steel sheet that has excellent ductility and stretch-flanging capacity, according to any of [1] to [8], which additionally includes one or more of Ca, Ce, Mg and ETR has 0.0001 to 0.5% by mass percentage in total.
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7/104 [10] A high-strength zinc-coated steel sheet that has excellent ductility and stretch-flanging capability, in which the high-strength zinc-coated steel sheet is produced by forming a layer coated with zinc on a high strength steel plate surface, according to any of [1] to [9].
[11] A method of manufacturing a high-strength steel plate that has excellent ductility and a stretch-flanging capacity, the method that includes: a hot rolling process in which a plate containing the chemical constituents according to with any one of [1] or [6] to [9] is heated up to 1050 ° C or more directly or after cooling once, a hot lamination is performed on it at a temperature greater than one within 800 ° C and one transformation point of Ar ₃ , and a winding is carried out in a temperature range of 750 ° C or less, in such a way that an austenite phase in a laminated material structure after lamination occupies 50% by volume or more; a cooling process in which the steel sheet after hot rolling is cooled from a coiling temperature at (the coiling temperature -100 ° C) at a rate of 20 ° C / hour or less, while an Equation next (1) is satisfied; and a process in which continuous annealing is performed on the steel sheet after cooling, in which in the process in which continuous annealing is performed, the steel sheet is annealed at a maximum heating temperature of 750 to 1000 ° C, a first cooling in which the steel plate is cooled from the maximum heating temperature to a ferrite transformation temperature range or less and maintained in the ferrite transformation temperature range for 20 to 1000 seconds is subsequently performed, a second cooling in which the steel plate is cooled at a cooling rate of 10 ° C / second or more,
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8/104 on average in a bainite transformation temperature range and cooling is stopped within a range from a martensite start temperature - 120 ° C at the martensite start temperature is subsequently performed, the steel plate after the second cooling is kept in a range from a second cooling stop temperature to the start temperature of martensite transformation for 2 to 1000 seconds, the steel plate is subsequently reheated to a stop temperature of reheating, which is equal to or greater than a start temperature of bainite transformation -100 ° C, at a temperature increase rate of 10 ° C / second or more, on average in the bainite transformation temperature range, and a third cooling in which the steel plate after reheating is cooled from the reheat stop temperature to a temperature that is less than the bainite transformation temperature range and maintained in the bainite transformation temperature range for 30 seconds or more, is performed:
Equation 1
where t (T) in Equation (1) represents maintenance time (seconds) of the steel sheet at a temperature T ° C in the cooling process after winding.
[12] The method of manufacturing high-strength steel sheet that has excellent ductility and stretch-flanging capability, according to [11], where the winding temperature after hot rolling is equal to or greater than one point Bs and less than or equal to 750 ° C.
[13] The method of manufacturing high-strength steel sheet
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9/104 that has excellent ductility and stretch-flanging capacity, according to [11] or [12], which additionally includes between the cooling process and the continuous annealing process: a cold rolling process in the which the steel plate is subjected to acid pickling and cold rolling in reduced rolling from 35 to 80%.
[14] The method of manufacturing high-strength steel sheet that has excellent ductility and stretch-flanging capability, according to any of [11] to [13], in which a sum of a time during which steel sheet is kept in the bainite transformation temperature range in the second cooling and a time during which the steel sheet is kept in the bainite transformation temperature range in reheating is 25 seconds or less.
[15] A method of fabricating a high-strength zinc-coated steel sheet that has excellent ductility and stretch-flanging capability, in which the steel sheet is immersed in a zinc plating bath for reheating in the sheet fabrication high strength steel based on the manufacturing method according to any of [11] to [14].
[16] A method of fabricating a high-strength zinc-coated steel sheet that has excellent ductility and stretch-flanging capability, in which the steel sheet is immersed in a zinc plating bath in the transformation temperature range of bainite in the third cooling in the manufacture of high-strength steel plate based on the manufacturing method according to any of [11] to [14].
[17] A method of manufacturing a steel sheet coated with high-strength zinc that has excellent ductility and stretch-flanging capability, in which an electroplating of
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10/104 zinc is performed after the fabrication of high strength steel sheet based on the manufacturing method according to any of [11] to [14], [18] A method of fabricating a steel sheet coated with high-strength zinc that has excellent ductility and stretch-flanging capability, where hot-dip zinc plating is performed after the manufacture of the high-strength steel sheet based on the manufacturing method according to any of [ 11] to [14].
Advantageous effects of the invention [0012] The high strength steel sheet of the present invention contains predetermined chemical constituents, when a plurality of measurement regions with diameters of 1 pm or less are adjusted in a range from 1/8 to 3 / 8 of a thickness of the steel plate, the hardness measurement values in the plurality of measurement regions are arranged in ascending order to obtain a hardness distribution, in whole number NO, 02, which is a number obtained by multiplying a total number of hardness measurement values by 0.02 and, if present, by rounding up a decimal number, a hardness of a measurement value is obtained which consists of a N0.02-th largest value from lowest hardness measurement value is considered to be a 2% hardness, an integer N0.98, which consists of a number obtained by multiplying the total number of hardness measurement values by 0.98 and, if pr This, rounded down to a decimal number, is obtained, and a hardness of a measured value consisting of a N0.98-th largest value from the lowest hardness measurement value is considered to be a 98% hardness , the 98% hardness is 1.5 or more times as high as the 2% hardness, a K * kurtosis of the hardness distribution between the 2% hardness and the 98% hardness is equal to or less than -0, 40, a size of
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11/104 average grain in the steel plate structure is 10pm or less, and therefore the steel plate which has excellent ductility and stretch-flanging capacity is obtained, while the tensile strength which is as high as 900 MPa or more is ensured.
[0013] In addition, a microdistribution of Mn within the steel sheet increases by winding the steel sheet after hot rolling around a coil at 750 ° C and cooling the steel sheet from the winding temperature a (the winding temperature -100 ° C) at a cooling rate of 20 ° C / hour or less, while Equation (1) above is satisfied, in the process for producing a hot rolled coil from the plate which contains the chemical constituents predetermined in the method of manufacturing the high-strength steel sheet according to the present invention.
[0014] In addition, since the process in which continuous annealing is performed on the steel plate with increased Mn distribution includes a heating process in which the steel plate is annealed at a maximum heating temperature of 750 to 1000 ° C, a first cooling process in which the steel sheet is cooled from the maximum heating temperature to a ferrite transformation temperature range or less and maintained in a ferrite transformation temperature range for 20 to 1000 seconds, a second cooling process in which the steel plate after the first cooling process is cooled at a cooling rate of 10 ° C / second or more, averaging over a bainite transformation temperature range and the cooling is stopped within a range from a martensite transformation start temperature - 120 ° C to a martensite transformation start temperature, a maintenance process tion in which the steel sheet after the second cooling process is kept in a range from a
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12/104 second cooling stop temperature to the point of Ms or less for 2 to 1000 seconds, a reheating process in which the steel plate after the maintenance process is reheated to a reheating stop temperature, which is equal or greater than a start temperature of bainite transformation - 80 ° C, at a temperature rise rate of 10 ° C / second or more, on average in the bainite transformation temperature range, and a third cooling process in the which the steel sheet after the reheat process is cooled from the reheat stop temperature to a temperature that is less than the bainite transformation temperature range and kept in the bainite transformation temperature range for 30 seconds or furthermore, the steel sheet structure is controlled in such a way that the difference in hardness within the steel sheet is large and the average grain size is small enough, and it is possible ble to obtain the steel sheet rolled high strength cold ductility and which has excellent ability to estiramentoflangeamento (hole expansion property), and has excellent workability, while ensuring a maximum tensile strength of 900 MPa or more.
[0015] Additionally, it is possible to obtain the steel sheet coated with high strength zinc which has excellent ductility and stretch-flanging capability (orifice expansion property) and has excellent workability, while ensuring the maximum tensile strength so high as much as 900 MPa or more, by adding the process for forming the zinc-plated layer. Brief description of the drawings [0016] FIG. 1 is a graph showing a relationship between the hardness classified in a plurality of levels and a number of measured values at each level, which is obtained by converting each
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13/104 measured value, while a difference between a maximum hardness measurement value and a minimum hardness measurement value is considered to be 100%, compared to an example of a high-strength steel plate according to present invention.
[0017] FIG. 2 is a diagram for comparing the hardness distribution in the high-strength steel sheet according to the present invention with a normal distribution.
[0018] FIG. 3 is a graph that shows schematically a relationship between a transformation rate and elapsed time of transformation treatment when the difference between a maximum and a minimum value of Mn concentration in base iron is relatively large.
[0019] FIG. 4 is a graph that shows schematically a relationship between a transformation rate and the elapsed time of transformation treatment when a difference between a maximum and a minimum value of Mn concentration in base iron is relatively small.
[0020] FIG. 5 is a graph that illustrates the temperature history of a cold rolled steel sheet when the sheet is made to pass through a continuous annealing line, which shows a relationship between the temperature of the cold rolled steel sheet and the time. Description of the modalities [0021] The high-strength steel sheet according to the present invention consists of a steel sheet, which includes predetermined chemical components, in which an average grain size in the structure of the same is 10 pm or less , the 98% hardness is 1.5 or more times as high as the 2% hardness in a hardness distribution when a plurality of measurement regions with diameters of 1 pm or less is adjusted in a thickness range from 1/8 to 3/8 of the same, and the hardness measurement values in the plurality of
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14/104 measurement regions are aligned in an order from a lower measurement value, and the K * kurtosis of the hardness distribution between the 2% hardness region and the 98% hardness region is -0, 40 or less. An example of the hardness distribution on the high strength steel plate according to the present invention is shown in FIG.1. (Definition of Hardness) [0022] Later in this document, the definition of hardness will be described, and the hardness of 2% and the hardness of 98% will be described first. The hardness measurement values are obtained in the plurality of measurement regions adjusted in a thickness range from 1/8 to 3/8 of the steel plate, and an integer N0.02, which consists of a obtained number by multiplying the total number of hardness measurement values by 0.02 and, if present, by rounding up a decimal number, it is obtained. In addition, when a number obtained by multiplying the total number of hardness measurement values by 0.98 includes a decimal number, an integer N0.98 is obtained by rounding down the decimal number. Therefore, the hardness of a N0.02-th largest measurement value from the minimum hardness measurement value in the plurality of measurement regions is considered to be a 2% hardness. In addition, a hardness of a N0.98th largest measured value from the minimum hardness measured value in the plurality of measuring regions is considered to be 98% hardness. In the high-strength steel sheet of the present invention, the hardness of 98% is preferably 1.5 or more times as high as the hardness of 2%, and the K * kurtosis of the hardness distribution between the hardness of 2 % and the hardness of 98% is preferably -0.40 or less. [0023] Each diameter of the measurement regions is limited to 1 pm or less in adjusting the plurality of measurement regions in order to accurately assess the hardness dispersion that results from a steel plate structure that includes a ferrite phase , a phase of bainite, a
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15/104 martensite phase, and the like. Since the average grain size in the steel plate structure is 10 pm or less in the high strength steel plate of the present invention, it is necessary to obtain hardness measurement values in measurement regions narrower than the size of medium grain in order to accurately assess the hardness dispersion that results from the steel plate structure, and specifically, it is necessary to adjust regions with diameters of 1 pm or less as the measurement regions. When hardness is measured using a standard Vickers tester, an indentation size is too large to accurately assess the hardness dispersion that results from the structure.
[0024] Consequently, the hardness measurement value in the present invention represents a value evaluated based on the following method. That is, a measurement value obtained by measuring hardness under an indentation load of 1 g using a dynamic microhardness tester equipped with a three-sided pyramid inductor of the Berkovich type based on a measurement method Indentation depth is used for the high strength steel plate of the present invention. The hardness measurement position is adjusted to a range from 1/8 to 3/8 around 1/4 of a plate thickness in the cross section of the plate thickness that is parallel to a lamination direction of the plate. steel. In addition, the total number of hardness measurement values is in a range from 100 to 10000, and is preferably equal to or greater than 1000. The indentation size thus measured has a diameter of 1 pm or least with the conviction that the indentation format is a circular format. When the indentation shape is a rectangular shape or a triangular shape in addition to the circular shape, the dimension of the indentation shape in the longitudinal direction can be 1 pm or less.
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16/104 [0025] In addition, the average grain size in the present invention represents the size measured by the following method. That is, a grain size measured based on an EBSD method (backscattered electron diffraction - Electron BackScattering Diffraction) is preferably used for the high strength steel plate of the present invention. A grain size observation surface is in the range from 1/8 to 3/8 around 1/4 of the thickness of the sheet in the cross section of the sheet thickness that is parallel to the rolling direction of the sheet steel . In addition, it is preferred to calculate the average grain size by applying an intercept method to a grain boundary map for the observation surface obtained considering a limit, in which a difference in crystal orientation between the adjacent measuring points in a bcc crystal orientation becomes 15 ° or more, as a grain boundary.
[0026] In order to obtain a steel sheet that has excellent ductility, it is important to use a structure, such as ferrite, that has excellent ductility, such as the steel sheet structure. However, the structure which has excellent ductility is soft. Consequently, it is necessary to employ a steel sheet structure that contains a soft structure and a hard structure, such as martensite, in order to obtain a steel sheet with high ductility, while having sufficient strength.
[0027] In the steel plate with the steel plate structure that includes both the soft and the hard structure, the stress caused by the deformation is more easily accumulated in the soft part and is not easily distributed to the hard part, when a difference of hardness between the soft part and the hard part is greater and, therefore, the ductility is optimized.
[0028] Since the hardness of 98% is 1.5 or more times as high as the hardness of 2% on the high strength steel plate of this
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17/104 invention, the difference in hardness between the soft part and the hard part is sufficiently large and therefore it is possible to obtain sufficiently high ductility. In order to obtain the additionally greater ductility, the hardness of 98% is preferably 3.0 or more times as high as the hardness of 2%, more preferably more than 3.0 times, even more preferably, 3.1 or more times, more preferably, 4.0 or more times, and most preferably, 4.2 or more times. When the 98% hardness measurement value is 1.5 times less than the 2% hardness measurement value, the difference in hardness between the soft part and the hard part is not large enough and therefore the ductility it is insufficient. However, the 98% hardness measurement value is 4.2 or more times the 2% hardness measurement value, the difference in hardness between the soft part and the hard part is sufficiently large, and both the ductility and a Orifice expansion properties are further optimized, which is preferred.
[0029] As described above, the difference in hardness between the soft part and the hard part is preferably greater from the point of view of ductility. However, if the regions with the great difference of coming into contact with each other are, an interval of tension caused by the deformation of the steel sheet occurs at the edge part, and a micro-crack is easily generated. Since the micro-crack can become a starting point for cracking, the stretch-flanging ability is degraded. In order to suppress the degradation of stretching-flanging capacity resulting from the large difference in hardness between the soft and the hard part, it is effective to reduce the number of edges on which the regions with the great difference in hardness are in contact with each other. the others and decrease the length of each edge in which the regions with the greatest difference in hardness are in contact with each other.
[0030] Since the average grain size of the steel sheet of
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18/104 high strength of the present invention, which is measured by the EBSD method, is 10 pm or less, the edge, on which the regions with the greatest difference in hardness are in contact with each other, on the steel plate is decreased, the degradation of the stretch-flanging capacity that results from the large difference in hardness between the soft part and the hard part is suppressed and the excellent stretch-flanging capacity can be obtained. In order to obtain, in addition, excellent stretch-flanging capacity, the average grain size is preferably 8 pm or less, and more preferably 5 pm. If the average grain size exceeds 10 pm, the edge reduction effect, in which the regions with the greatest difference in hardness are in contact with each other, on the steel plate is not sufficient and it is not possible to sufficiently suppress the degradation stretch-flanging capacity.
[0031] In addition, in order to reduce the number of edges on which the regions with the greatest difference in hardness are in contact with each other, the steel plate structure which has a variety of narrow distribution of hardness, in the where the dispersion of the hardness distribution on the steel plate is small, it can be used. [0032] According to the high strength steel plate of the present invention, the dispersion in the hardness distribution in the steel plate is reduced by adjusting the K * kurtosis of the hardness distribution to be -0.40 or less, it is possible to reduce the edges at which the regions with the greatest difference in hardness are in contact with each other and thus obtain excellent stretching-flanging capacity. In order to obtain, in addition, excellent stretch-flanging capacity, K * kurtosis is preferably 0.50 or less, and more preferably -0.55 or less. Although the effects of the present invention can be achieved without particularly determining the lower limit of K * kurtosis, it is difficult to adjust K * as
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19/104 less than -1.20 and, therefore, this value is considered as the lower limit.
[0033] Furthermore, K * kurtosis is a value that can be obtained by the following Equation (2) based on the hardness distribution and is a numerical value obtained as a consequence of the evaluation of the hardness distribution by comparing the hardness distribution normal distribution. A case in which kurtosis is a negative value denotes that a hardness distribution curve is relatively flat, and a large absolute value denotes that the hardness distribution deviates further from the normal distribution.
Equation 2
(^ 0.9¾ ~ N1.02 + 0 (^ 0.98 ~ ^jV 0.Ü2 + 2) 1 (^ 0.9S - ^ 0.112 - ¹ X ^ 0.98 - ^ ϋ.ΟΪ - 2} “(2)
Hi: hardness of an i-th largest measuring point from a minimum hardness measuring value
H *: average hardness of N0.02-th largest measuring point from minimum hardness to N0.98-th largest measuring point s *: standard deviation of N0.02-th largest measuring point from minimum hardness at N0.98-th largest measuring point [0034] Furthermore, when the K * kurtosis exceeds -0.40, the steel plate structure does not consist of a structure that has a sufficiently narrow enough distribution of hardness, the dispersion in the hardness distribution in the steel plate becomes larger, the number of edges on which the regions with the great difference in hardness are in contact with each other increases, and it is not possible to sufficiently suppress the degradation of the stretching capacity- flanging.
[0035] Next, the detailed description of the dispersion in the hardness distribution on the steel plate will be given with reference to FIG.1. FIG.1
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20/104 is a graph showing a relationship between hardness classified at a plurality of levels and a number of measured values at each level, which is obtained by converting each measured value, while a difference between a value of maximum hardness measurement and a minimum hardness measurement value is considered to be 100%, in relation to an example of a high-strength steel plate according to the present invention. In the graph shown in FIG. 1, the horizontal geometric axis represents the hardness and the vertical geometric axis represents a number of measured values at each level. In addition, a solid line from the graph shown in FIG. 1 is obtained by connecting the point that represents the numbers of the measured values at each level.
[0036] In the high-strength steel plate of the present invention, it is preferred that all the numbers of the measured values in divided bands D, which are obtained by dividing the band evenly from the hardness of 2% to 98% hardness in 10 parts, in the graph shown in FIG. 1 is within a range from 2% to 30% of the number of all measured values.
[0037] In such a high-strength steel plate, the line joining the numbers of the measured values in the levels becomes a smooth curve like no high peaks and valleys in the graph shown in FIG.1, and the dispersion in the hardness distribution on the steel plate is significantly reduced. Consequently, such a high-strength steel sheet has fewer edges on which the regions with a large difference in hardness are in contact with each other, and excellent stretch-flanging capacity can be obtained.
[0038] Furthermore, if any of the numbers of the measured values in a divided range D, which has been equally divided into 10 parts, is out of range from 2% to 30% of the number of total measured values in the graph shown in FIG. 1, the line joining the
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21/104 numbers of the measured values in the levels can easily include a high peak or a valley, and an effect that the stretch-flanging capacity is optimized due to the low dispersion in the hardness distribution in the steel plate is reduced.
[0039] Specifically, for example, when only a number of measured values in a divided range D near the center exceeds 30% of the number of all measured values between the 10 equally divided regions D, the line joining the numbers of the Measurement numbers at levels have a peak in the split range D near the center.
[0040] Furthermore, if only a number of the measured values in the divided range D near the center is less than 2% of the number of all the measured values, the line joining the numbers of the measured values in the levels has a valley in the split strip D close to the center, and many structures have large differences in hardness, in which the hardness in different split stripes D arranged on both sides of the valley are included.
[0041] On the high strength steel plate of the present invention, all the numbers of the measured values in the divided range D are preferably 25% or less of the number of all the measured values, and more preferably, 20 % or less, in order to additionally optimize the stretch-flanging capacity. In order to further optimize the stretch-flanging capacity, all the numbers of the measured values in the divided ranges D are preferably 4% or more of the number of all the measured values, and more preferably, 5% or more.
[0042] The hardness distribution in the high strength steel plate of the present invention will be compared with a general normal distribution and described in detail. K * kurtosis of the normal distribution is generally considered to be 0. On the other hand, kurtosis of the distribution of
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22/104 hardness in the steel sheet according to the present invention is -0.4 or less and, therefore, it is obvious that the distribution is different from the normal distribution. The hardness distribution on the steel sheet according to the present invention is flatter and has a broader bottom as compared to the normal distribution, as shown in FIG. 2. Since the high-strength steel sheet of the present invention has such a hardness distribution, and the hardness ratio of 98% to hardness of 2%, which correspond to both sides of the bottom of the distribution, is 1 , 5 or more times, which is extremely large, the difference in hardness between the soft part and the hard part in the steel sheet structure is sufficiently large, and high ductility can be obtained. That is, the present inventor has found that the orifice expansion property is further optimized when the ratio between 98% hardness and 2% hardness is greater in the hardness distribution in which the kurtosis is -0.4 or less , in contrast to the conventional hardness distribution. On the other hand, the orifice expansion property is considered as additionally optimized as the hardness ratio in the structure is lower, according to the conventional technique. The conventional technique was based on the assumption of the hardness distribution that is close to the normal distribution, which is basically different from the technique proposed in the present invention.
(Mn distribution) [0043] In the high strength steel plate of the present invention, it is preferred that a difference between a maximum and a minimum value of Mn concentration in the base iron in a thickness starting from 1/8 the 3/8 of the steel plate is equal to or greater than 0.40% and equal to or less than 3.50%, when converted into a mass percentage, in order to obtain the aforementioned hardness distribution.
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23/104 [0044] The difference between the maximum value and the minimum value of the concentration of Mn in the base iron in the thickness from 1/8 to 3/8 of the steel plate is defined as 0.40% or more when converted into a mass percentage, due to the fact that the phase transformation proceeds more slowly during continuous annealing after cold rolling, as the difference between the maximum and the minimum value of the Mn concentration is greater and is it is possible to reliably generate each transformation product in a desired volume fraction and thus obtain the high-strength steel plate with the aforementioned hardness distribution. More specifically, it is possible to generate a transformation product with relatively high hardness, such as martensite, in place of a transformation product with relatively low hardness, such as ferrite, in a balanced way and, therefore, a sharp peak is not present in the hardness distribution on the high-strength steel plate, that is, the kurtosis decreases, and a flat hardness distribution curve as shown in FIG. 1 can be obtained. In addition, the width of the hardness distribution is increased by generating several transformation products in a balanced way and, in this way, it is possible to adjust the hardness from 98% to 1.5 or more times as high as the hardness of 2 %, preferably, 3.0 or more times, more preferably, greater than 3.0 times, more preferably still, 3.1 or more times, even more preferably, 4.0 or more times, and still more more preferably, 4.2 or more times.
[0045] For example, the transformation of a ferrite phase will be described as an example. In a heat treatment process to cause the transformation of the ferrite phase, the phase transformation from austenite to ferrite begins relatively early in a region where the Mn concentration is low. On the other hand, the phase transformation from austenite to ferrite starts relatively
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24/104 slow in the region where the concentration of Mn is high, as compared to the region where the concentration of Mn is low. Therefore, the phase transformation from austenite to ferrite proceeds more slowly in the steel plate as the concentration of Mn in the steel plate is more non-uniform and the difference in concentration is greater. In other words, a transformation rate, during a period when the volume percentage of the ferrite phase reaches, for example, 50% from 0%, becomes lower.
[0046] The above phenomenon occurs similarly in the tempered martensite phase and the remaining hard phase, as well as the ferrite phase.
[0047] FIG.3 shows schematically a relationship between the transformation rate and the elapsed time of the transformation treatment. In the case of phase transformation from austenite to ferrite, for example, the transformation rate represents a percentage by volume of ferrite in the steel plate structure, and the time elapsed from the transformation treatment represents the time elapsed from the heat treatment to cause the transformation of the ferrite. In the example of the present invention shown in FIG.3, the difference between the maximum and minimum values of the Mn concentration is relatively large, and a curve gradient showing the transformation rate across the steel plate is small (the transformation rate is low). On the other hand, in the comparative example shown in FIG. 4, the difference between the maximum value and the minimum value of the Mn concentration is relatively small, and the gradient of the curve showing the transformation rate across the steel sheet is large (the transformation rate is high). For this reason, although the transformation treatment can be completed for a period from x1 to x2 in order to control the transformation rate (percentage by volume) in a range from y1 to y2 (%) in the example shown in FIG.3, it is necessary to finish the transformation treatment for a period from x3 to x4 and it is difficult to control the time
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25/104 of treatment in the example shown in FIG. 4.
[0048] When the difference in Mn concentration is less than 0.40%, it is not possible to sufficiently suppress the transformation rate and achieve a sufficient effect and therefore this is adjusted as the lower limit. The difference in Mn concentration is preferably 0.60% or more, and more preferably 0.80% or more. Although the phase transformation can be more easily controlled as the difference in Mn concentration is greater, it is necessary to excessively increase the amount of Mn added to the steel plate so that the difference in Mn concentration exceeds 3.50%, and it is preferred that the difference in Mn concentration is 3.50% or less, since there is a concern of cracking a molded plate and degradation of a welding property. In view of the welding property, the difference in the concentration of Mn is, more preferably, 3.40% or less, and more preferably, 3.30% or less.
[0049] A method of determining a difference between the maximum value and the minimum value of Mn in thickness from 1/8 to 3/8 is as shown below. First, a sample is obtained, while a cross section of the sheet thickness that is parallel to the rolling direction of the steel sheet is considered as an observation surface. Then, the ΕΡΜΑ analysis is performed on a thickness range from 1/8 to 3/8 around a thickness of 1/4 to measure an amount of Μη. The measurement is performed, while a probe diameter is set to 0.2 to 1.0 pm and the measurement time by one point is set to 10 ms or greater, and the quantities of Mn are measured at 1000 or more points based on line analysis or surface analysis.
[0050] In measurement results, points at which the concentration of Mn exceeds three times the concentration of Mn added are considered as points at which inclusions, such as sulfide of
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26/104 manganese, are observed. In addition, points at which the concentration of Mn is less than 1/3 times the concentration of Mn added are considered to be the points at which inclusions, such as aluminum oxide, are observed. Since such Mn concentrations are unlikely to affect the phase transformation behavior in the base iron, the maximum and minimum values of the Mn concentration are respectively obtained after the inclusion measurement results are excluded from the measurement results. Then, the difference between the maximum and minimum values thus obtained from the Mn concentration is calculated.
[0051] The method of measuring the amount of Mn is not limited to the method above. For example, an EMA method or direct observation using a three-dimensional atomic probe (3D-AP) can be performed to measure the concentration of Mn.
(Steel plate structure) [0052] Furthermore, the steel plate structure of the high strength steel plate of the present invention includes 10 to 50% of a ferrite phase and 10 to 50% of a tempered martensite phase and a hard phase remaining by fractions of volume. In addition, the remaining hard phase includes 10 to 60% of one or both a bainitic ferrite phase and a bainite phase and 10% or less of a fresh martensite phase by volume fractions. In addition, the steel sheet structure can contain 2 to 25% of a retained austenite phase. When the high strength steel plate of the present invention has such a steel plate structure, the difference in hardness within the steel plate becomes much larger, the average grain size becomes small enough and therefore the steel plate high strength has additionally greater strength and excellent ductility and stretch-flanging capability (orifice expansion property).
Ferrite
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27/104 [0053] Ferrite is a structure that is effective in optimizing ductility and is preferably contained in the steel plate structure by 10 to 50% for a fraction by volume. The volume fraction of ferrite contained in the steel plate structure is preferably 15% or more, and more preferably 20% or more in view of the ductility. In addition, the volume fraction of ferrite contained in the steel sheet structure is preferably 45% or less, and more preferably 40% or less, in order to sufficiently optimize the tensile strength of the sheet metal. steel. When the volume fraction of ferrite is less than 10%, there is a concern that sufficient ductility may not be achieved. On the other hand, ferrite has a soft structure and therefore the elastic limit is lower in some cases when the volume fraction exceeds 50%.
Bainitic and Bainite Ferrite [0054] Bainitic and bainite ferrite are structures with a hardness between the hardness of soft ferrite and the hardness of hard tempered martensite and fresh martensite. The high strength steel sheet of the present invention can contain either one of bainite and bainite ferrite or it can contain both. In order to level the hardness distribution within the steel plate, a total amount of bainitic and bainite ferrite contained in the steel plate structure is preferably 10 to 45% per volume fraction. The sum of volume fractions of bainitic ferrite and bainite contained in the steel sheet structure is preferably 15% or more, and more preferably 20% or more, in view of the stretching-flanging capacity. In addition, the sum of the volume fractions of bainitic and bainite ferrite is preferably 40% or less, or more preferably, 35% or less, in order to obtain a satisfactory balance between ductility and elastic limit.
[0055] When the sum of the volume fractions of bainitic and bainite ferrite is less than 10%, the predisposition occurs in the distribution of
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28/104 hardness, and there is a concern that the stretch-flanging ability may be degraded. On the other hand, when the sum of the volume fractions of bainitic ferrite and bainite exceeds 45%, it is difficult to generate adequate amounts of tempered ferrite and martensite, and the balance between ductility and elastic limit is degraded, which is not preferred.
Tempered Martensite [0056] Tempered martensite is a structure that greatly optimizes the tensile strength and is preferably contained in the steel plate structure by 10 to 50% for a fraction by volume. When the volume fraction of tempered martensite contained in the steel sheet structure is less than 10%, there is a concern that sufficient tensile strength may not be achieved. On the other hand, when the volume fraction of tempered martensite contained in the steel sheet structure exceeds 50%, it becomes difficult to ensure the ferrite and retained austenite necessary to optimize ductility. In order to sufficiently optimize the ductility of the high strength steel sheet, the volume fraction of tempered martensite is preferably 45% or less, and more preferably 40% or less. In addition, in order to ensure tensile strength, the volume fraction of tempered martensite is preferably 15% or more, and more preferably 20% or more.
Retained austenite [0057] Retained austenite is a structure that is effective in optimizing ductility and is preferably contained in the steel plate structure by 2 to 25% for a fraction by volume. When the volume fraction of retained austenite contained in the steel sheet structure is 2% or more, the most sufficient ductility can be obtained. In addition, when the volume fraction of austenite retained is 25% or less, the welding property is optimized without a need for the addition of a
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29/104 large amount of austenite stabilizer, such as C or Mn. In addition, although it is preferred that the retained austenite be contained in the steel plate structure of the high strength steel sheet according to the present invention, since the retained austenite is effective in optimizing ductility, the retained austenite may not be contained when sufficient ductility can be obtained.
Fresh martensite [0058] Since fresh martensite acts as a starting point for fracture and degrades the stretch-flanging ability, although fresh martensite greatly optimizes the tensile strength, fresh martensite is preferably contained in the structure steel sheet by 10% or less for a fraction by volume. In order to optimize the stretch-flanging capacity, the volume fraction of fresh martensite is preferably 5% or less, and more preferably, 2% or less.
Others [0059] The steel plate structure of the high strength steel plate according to the present invention may contain structures such as perlite and coarse cementite in addition to the above structures. However, when large amounts of perlite and coarse cementite are contained in the steel plate structure of the high strength steel plate, the ductility is degraded. For this reason, the volume fraction of perlite and coarse cementite contained in the steel sheet structure is preferably 10% or less in total, and more preferably 5% or less.
[0060] The volume fraction of each structure contained in the steel plate structure of the high-strength steel plate according to the present invention can be measured based on the following method, for example.
[0061] Regarding the fraction of volume of austenite retained, the analysis
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30/104 X-rays are performed, while a surface with a thickness of 1/4, which is parallel to the sheet steel plate surface, is considered as an observation surface, a fraction of the area is calculated and the result of it can be mentioned as the volume fraction.
[0062] Regarding the volume fractions of ferrite, bainitic ferrite, bainite, tempered martensite and fresh martensite, a sample is obtained while a cross section of the plate thickness that is parallel to the rolling direction of the steel plate is considered as an observation surface, the observation surface is ground, subjected to nital recording, and observed with a field emission scanning electron microscope (FE-SEM) in a thickness range from 1/8 to 3/8 around 1/4 of the thickness of the plate to measure the area fractions, and the results of the same can be mentioned as the volume fractions.
[0063] In addition, an area of the observation surface observed with FE-SEM can be a square with sides of 30 pm, for example, and each structure on the observation surface can be differentiated from one another as follows.
[0064] Ferrite consists of a block of crystal grains and is a region within which iron carbide with a long diameter of 100 nm or more is not present. In addition, the ferrite volume fraction is a sum of the ferrite volume fraction remaining at the highest heating temperature and the ferrite volume fraction that is newly produced in a ferrite transformation temperature range. However, it is difficult to directly measure the volume fraction of ferrite during production. For this reason, a small piece of the cold-rolled steel sheet before passing through the continuous annealing line is cut, the small piece is annealed based on the same temperature history as that when the small piece is made to pass
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31/104 through the continuous annealing line, the dispersion in the volume of ferrite in the small part is measured and a numerical value calculated using the result is considered as the volume fraction in the present invention.
[0065] Furthermore, bainitic ferrite is a group of crystal grains in the shape of a slat and the iron carbide with a long diameter of 20 nm or more is not contained within the slat.
[0066] In addition, bainite is a group of slat-shaped crystal grains and a plurality of iron carbide compounds with a long diameter of 20 nm or more is contained within the slat, and the carbide belongs to a single variable, that is, a group of iron carbide that extends in the same direction. Here, the group of iron carbide which extends in the same direction denotes that differences in the iron carbide group extension direction are 5 within ^it.
[0067] In addition, tempered martensite is a group of slat-shaped crystal grains, a plurality of iron carbide compounds with a long diameter of 20 nm or more is contained within the slat, and the carbide belongs to a plurality of variables, that is, a plurality of groups of iron carbide that extend in different directions.
[0068] In addition, tempered bainite and martensite can be easily differentiated from one another by observing iron carbide within the clapboard crystal grain using FESEM and examining its extension directions.
[0069] In addition, fresh martensite and retained austenite are not sufficiently corroded by engraving with nital. Therefore, fresh martensite and retained austenite are apparently differentiated from the structures mentioned above (ferrite, bainite ferrite, bainite, tempered martensite) in the observation with FE-SEM.
[0070] Consequently, the volume fraction of fresh martensite
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32/104 is obtained as a difference between a fraction of an area observed with FE-SEM, which has not yet been corroded, and a fraction of retained austenite area measured with X-rays.
(Definition concerning Chemical Compositions) [0071] In the following, the description of chemical constituents (compositions) of the high strength steel sheet of the present invention will be given. In addition, [%] in the following description represents [% by mass].
C: 0.050 to 0.400% [0072] C is contained in order to optimize the strength of the high strength steel sheet. However, if the C content exceeds 0.400%, sufficient welding property is not achieved. In view of the welding property, the C content is preferably 0.350% or less, and more preferably 0.300% or less. On the other hand, if the C content is less than 0.050%, the strength is reduced, and it is not possible to ensure the maximum tensile strength of 900 MPa or more. In order to optimize the resistance, the C content is preferably 0.060% or more, and more preferably 0.080% or more.
Si: 0.10 to 2.50% [0073] Si is added in order to suppress softening by martensite quenching and to optimize the strength of the steel sheet. However, if the Si content exceeds 2.50%, the brittleness of the steel sheet is caused and the ductility is degraded. In view of ductility, the Si content is preferably 2.20% or less, and more preferably 2.00% or less. On the other hand, if the Si content is less than 0.10%, the hardness of tempered martensite is reduced to a great degree and it is not possible to ensure a maximum tensile strength of 900 MPa or more. In order to optimize the resistance, the lower limit value of Si is preferably 0.30% or more, and more preferably, 0.50% or more.
Mn: 1.00 to 3.50% [0074] Since Mn is an element that optimizes the resistance of the
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33/104 steel plate, and it is possible to control the hardness distribution in the steel plate by controlling the distribution of Mn in the steel plate, Mn is added to the steel plate of the present invention. However, if the Mn content exceeds 3.50%, a concentrated part of thick Mn is generated in the center in the sheet thickness of the steel sheet, brittleness occurs easily, and problems such as cracking of a shaped sheet occur. easily. In addition, if the Mn content exceeds 3.50%, the welding property is also degraded. For this reason, the Mn content must be 3.50% or less. In view of the welding property, the Mn content is preferably 3.20% or less, and more preferably 3.00% or less. On the other hand, if the Mn content is less than 1.00%, a large number of soft structures are formed during cooling after annealing, which makes it difficult to ensure the maximum tensile strength of 900 MPa or more and, therefore, it is necessary that the Mn content be 1.00% or more. In order to optimize the resistance, the Mn content is preferably 1.30% or more, and more preferably, 1.50% or more.
P: 0.001 to 0.030% [0075] P tends to be segregated in the center in the sheet thickness of the steel sheet and causes the fragility of a welded part. If the P content exceeds 0.300%, the significant fragility of the welded part occurs and, therefore, the P content is limited to 0.030% or less. Although the effects of the present invention can be achieved particularly without determining the lower limit of the P content, 0.001% is adjusted as the lower limit value, since the manufacturing costs increase greatly when the P content is less than 0.001 %.
S: 0.0001 to 0.0100% [0076] S adversely affects the welding property and ease of fabrication during casting and hot rolling. For this reason, the upper limit of the S content is adjusted to 0.0100% or
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34/104 less. In addition, since S is linked to Mn to form thick MnS and reduces the stretch-flanging capacity, S is preferably contained at 0.0050% or less, and more preferably contained at 0.0025% or less. Although the effects of the present invention can be achieved particularly without determining the lower limit of the S content, 0.0001% is adjusted as the lower limit value, since the manufacturing costs increase greatly when the S content is lower than than 0.0001%.
Al: 0.001% to 2.500% [0077] Al is an element that suppresses the production of iron carbide and optimizes the resistance. However, if an Al content exceeds 2.50%, a fraction of ferrite in the steel plate increases excessively, and the strength is preferably reduced, therefore, the upper limit of the Al content is adjusted to 2,500 %. The Al content is preferably 2,000% or less, and more preferably 1,600% or less. Although the effects of the present invention can be achieved particularly without determining the lower limit of the Al content, 0.001% is adjusted as the lower limit, since an effect as a deoxidizing agent can be obtained when the Al content is 0.001% or more. In order to obtain sufficient effect as the deoxidizing agent, the Al content is preferably 0.005% or more, and more preferably 0.010% or more.
N: 0.0001 to 0.0100% [0078] Since N forms coarse nitride and degrades the stretch-flanging capacity, it is necessary to suppress the added amount of it. If the N content exceeds 0.0100%, this trend is more evident and, therefore, the N content range is adjusted to 0.0100% or less. In addition, since N causes a bubble during welding in many cases, it is preferred that the amount of N is as small
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35/104 as possible. Although the effects of the present invention can be achieved particularly without determining the lower limit of the N content, 0.0001% is adjusted as the lower limit value, since the manufacturing costs increase greatly when the N content is less than 0.0001%.
Ό: 0.0001 to 0.0080% [0079] Since O forms the oxide and degrades the stretch-flanging capacity, it is necessary to suppress the added amount of it. If the O content exceeds 0.0080%, the degradation of the stretch-flanging capacity is more evident and, therefore, the upper limit of the O content is adjusted to 0.0080% or less. The O content is preferably 0.0070% or less, and more preferably 0.0060% or less. Although the effects of the present invention can be achieved particularly without determining the lower limit of the O content, 0.0001% is adjusted as the lower limit value, since the manufacturing costs increase greatly when the O content is less than 0.0001%.
[0080] The high-strength steel sheet of the present invention can additionally contain the following elements as needed.
Ti: 0.005 to 0.090% [0081] Ti is an element that contributes to the optimization of the strength of the steel sheet by reinforcing precipitation, reinforcing the fine grain by suppressing the growth of the ferrite crystal grains and strengthening the displacement by suppressing recrystallization. However, if the Ti content exceeds 0.090%, the number of carbonitride precipitates increases, the formability is degraded and, therefore, the Ti content is preferably 0.090% or less. In view of the formability, the Ti content is preferably 0.080% or less, and more preferably 0.70% or less. Although the effects of this
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36/104 invention can be achieved particularly without determining the lower limit of the Ti content, the Ti content is preferably 0.005% or more in order to sufficiently obtain the Ti effect which optimizes the resistance. In order to further optimize the strength of the steel sheet, the Ti content is preferably 0.010% or more, and more preferably 0.015% or more.
Nb: 0.005 to 0.090% [0082] Nb is an element that contributes to the optimization of the strength of the steel plate by reinforcing the precipitation, reinforcing the fine grain by suppressing the growth of the ferrite crystal grains and reinforcing the displacement by suppressing recrystallization. However, if the Nb content exceeds 0.090%, the number of carbonitride precipitates increases, the formability is degraded and, therefore, the Nb content is preferably 0.090% or less. In view of formability, the Nb content is preferably 0.070% or less, and more preferably 0.050% or less. Although the effects of the present invention can be achieved particularly without determining the lower limit of the Nb content, the Nb content is preferably 0.005% or more in order to sufficiently obtain the Nb effect which optimizes the strength. In order to further optimize the strength of the steel sheet, the Nb content is preferably 0.010% or more, and more preferably 0.015% or more.
V: 0.005 to 0.090% [0083] V is an element that contributes to the optimization of the strength of the steel sheet by reinforcing precipitation, reinforcing the fine grain by suppressing the growth of ferrite crystal grains and reinforcing the displacement by suppressing recrystallization. However, if the V content exceeds 0.090%, the number of carbonitride precipitates increases, the formability is degraded and, therefore, the Nb content is preferably 0.090% or less. Although the effects
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37/104 of the present invention can be achieved particularly without determining the lower limit of the V content, the V content is preferably 0.005% or more in order to sufficiently obtain the V effect which optimizes the strength.
B: 0.0001 to 0.0100% [0084] Since B delays the phase transformation of austenite in a cooling process after hot rolling, it is possible to effectively make the Mn distribution continue through the addition of B. If the B content exceeds 0.0100%, high temperature workability deteriorates, productivity is reduced and therefore the B content is preferably 0.0100% or less. In view of productivity, the B content is preferably 0.0050% or less, and more preferably 0.0030% or less. Although the effects of the present invention can be achieved particularly without determining the lower limit of the B content, the B content is preferably 0.0001% or more, in order to sufficiently obtain the B-delaying effect. phase transformation. In order to delay the phase transformation, the B content is preferably 0.0003% or more, and more preferably 0.0005% or more.
Mo: 0.01 to 0.80% [0085] Since Mo delays the phase transformation of austenite in a cooling process after hot rolling, it is possible to effectively make the Mn distribution continue by addition of Mo. If the Mo content exceeds 0.80%, workability at a high temperature deteriorates, productivity is reduced and therefore the Mo content is preferably 0.80% or less. Although the effects of the present invention can be achieved particularly without determining the lower limit of the Mo content, the Mo content is preferably 0.01% or more, in order to sufficiently obtain the Mo effect which slows down the phase transformation.
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38/104
Cr: 0.01 to 2.00% Ni: 0.01 to 2.00% Cu: 0.01 to 2.00% [0086] Cr, Ni and Cu are elements that optimize the contribution to resistance, and a , two or more types of the same can be added instead of a part of C and / or Si. If the content of each element exceeds 2.00%, the acid pickling property, the welding property, the workability at a high temperature, and the like, are degraded and therefore the content of Cr, Ni and Cu is preferably 2.00% or less, respectively. Although the effects of the present invention can be achieved particularly without determining the lower limit of the Cr, Ni and Cu content, the Cr, Ni and Cu content is preferably 0.10% or more, respectively, in order to the effect of optimizing the strength of the steel plate is
[0087] Total content of one, two or more types of Ca, Ce, Mg and ETR from 0.0001 to 0.5000% [0088] Ca, Ce, Mg and ETR are elements that are effective in optimizing formability , and you can add one, two or more types of them. However, if the total amount of one or more of Ca, Ce, Mg and ETR exceeds 0.5000%, there is a concern that the ductility may deteriorate, on the contrary, and therefore the total content of the elements is, preferably 0.5000% or less. Although the effects of the present invention can be achieved particularly without determining the lower limit of the content of one or more among Ca, Ce, Mg and ETR, the total content of the elements is preferably 0.0001% or more, in order sufficiently to obtain the effect of optimizing the formability of the steel sheet. In view of formability, the total content of one or more of Ca, Ce, Mg and ETR is preferably 0.0005% or more, and more preferably, 0.0010% or more. In addition, ETR is an abbreviation for rare earth metals and represents an element that belongs to the lanthanide series. In the present invention, ETR and Ce are added in the form
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39/104 of mixed metal in many cases, and there is a case in which the elements in the lanthanide series are contained in addition to La and Ce. Even if such elements in the lanthanide series in addition to La and Ce are included as unavoidable impurities, the effects of the present invention can be achieved. In addition, the effects of the present invention can be achieved even if the metal La and Ce are added.
[0089] In addition, the high-strength steel sheet of the present invention can be configured as a high-strength zinc-coated steel sheet by forming a zinc-plated layer or a zinc-plated layer with alloy over the surface. By forming the zinc-plated layer on the surface of the high-strength steel sheet, the high-strength steel sheet achieves excellent corrosion resistance. The high-strength steel plate has excellent resistance to corrosion and excellent adhesion of a coating can be obtained, since the layer plated with zinc with alloy is formed on its surface.
(High strength steel plate manufacturing method) [0090] The following describes a method for manufacturing the high strength steel plate of the present invention.
First, in order to manufacture the high-strength steel plate of the present invention, the plate containing the chemical constituents mentioned above (compositions) is first molded.
[0091] Like the plate subjected to hot rolling, the continuous casting plate or plate manufactured by a thin plate casting to be used. The method of manufacturing the high-strength steel sheet of the present invention can be adapted to a process, such as direct rolling-continuous casting (CC-DR), in which hot rolling is performed immediately after casting.
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40/104 [0092] In the hot rolling process, it is necessary that the heating temperature of the plate is 1050 ° C or more. If the heating temperature of the plate is excessively low, a finishing lamination temperature is below a transformation temperature of Ar ₃ , the two-phase region lamination of ferrite and austenite is performed, a hot-rolled plate structure if it makes a double grain structure in which non-uniform grains are mixed, the non-uniform structure remains even after cold rolling and annealing processes and, therefore, ductility and bending capacity are degraded. In addition, since the reduction of the finishing laminating temperature causes an excessive increase in the laminating load, and there is a concern that it may become difficult to perform the lamination or a shape of the steel sheet after lamination may be defective, it is necessary to that the plate heating temperature is 1050 ° C or more. Although the effects of the present invention can be achieved particularly without determining the upper limit of the heating temperature of the plate, it is preferred that the upper limit of the heating temperature of the plate is 1350 ° C or less, since the adjustment of a excessively high heating temperature is not economically preferred.
[0093] In addition, the temperature of Ar ₃ is calculated based on the following equation.
Ar ₃ = 901 - 325 x C + 33 x Si - 92 x (Mn + Ni / 2 + Cr / 2 + Cu / 2 + Mo / 2) + 52 x Al [0094] In the above equation, C, Si, Mn , Ni, Cr, Cu, Mo and Al represent content [% by mass] of the elements.
[0095] In relation to the finishing lamination temperature of the hot lamination, a higher temperature between 800 ° C and the point of Ar ₃ is adjusted as a lower limit of it, and 1000 ° C is adjusted as an upper limit of the same . If the laminating temperature of
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41/104 finishing is less than 800 ° C, the rolling load during finishing rolling increases, and there is a concern that it may be difficult to perform hot rolling or the shape of the hot rolled steel sheet obtained after hot rolling can be defective. In addition, if the finishing rolling temperature is lower than the Are point, the hot rolling becomes the two-phase region rolling of ferrite and austenite, and the hot rolled steel plate structure becomes a structure in which non-uniform grains are mixed.
[0096] On the other hand, although the effects of the present invention can be achieved particularly without determining the upper limit of the finishing laminating temperature, it is necessary to adjust the heating temperature of the board to an excessively high temperature when the finishing laminating temperature it is set to an excessively high temperature to ensure the finish laminating temperature. For this reason, it is preferred that the temperature of the upper limit of the finishing lamination temperature is 1000 ° C or less.
[0097] A coiling process after hot rolling and a cooling process before and after the coiling process are significantly important for distributing ο Μη. The distribution of Mn above in the steel plate can be obtained by making the microstructure during slow cooling, after winding, a biphasic structure of ferrite and austenite and carrying out processing thereon at a high temperature for a long time. time to make Mn diffuse from ferrite to austenite.
[0098] In order to control the distribution of the concentration of Mn in the base iron in the thickness from 1/8 to 3/8 of the steel plate, it is necessary that the volume fraction of austenite be 50% or
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42/104 more in thickness from 1/8 to 3/8 when the steel sheet is wound. If the volume fraction of austenite in the thickness from 1/8 to 3/8 is less than 50%, austenite disappears immediately after winding, due to the progression of the phase transformation and, therefore, the Mn distribution does not proceeds sufficiently, and the concentration of Mn distribution above on the steel plate cannot be obtained. For the distribution of Mn to proceed effectively, the volume fraction of austenite is preferably 70% or more, and more preferably 80% or more. On the other hand, if the volume fraction of austenite is 100%, the phase transformation proceeds after winding, the ferrite is produced, the Mn distribution is initiated and, therefore, the upper limit is not particularly provided for the fraction of austenite volume.
[0099] In order to optimize the austenite fraction when the steel sheet is wound, it is necessary that the cooling rate for a period from the completion of the hot rolling to the winding is 10 ° C / second or more, average. If the cooling rate is less than 10 ° C / second, the transformation of ferrite continues during cooling, and there is a possibility that the volume fraction of austenite during winding may become less than 50%. In order to optimize the volume fraction of austenite, the cooling rate is preferably 13 ° C / second or more, and more preferably 15 ° C / second or more. Although the effects of the present invention can be achieved particularly without determining the upper limit of the cooling rate, it is preferred that the cooling rate is 200 ° C / second or less, since a special installation is required to obtain a cooling rate greater than 200 ° C / second and manufacturing costs increase significantly.
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43/104 [00100] Since an oxide thickness formed on the surface of the steel sheet increases excessively and the acid pickling property is degraded if the steel sheet is wound at a temperature that exceeds 800 ° C, the temperature of winding is set to 750 ° C or less. In order to optimize the acid pickling property, the winding temperature is preferably 720 ° C or less, and more preferably 700 ° C or less. On the other hand, if the winding temperature is lower than the point of Bs, the resistance of the hot rolled steel sheet is excessively optimized, it becomes difficult to perform cold rolling and, therefore, the winding temperature is adjusted to the point of Bs or more. Furthermore, the winding temperature is preferably 500 ° C or more, more preferably 550 ° C or more, and even more preferably 600 ° C or more, in order to optimize the austenite fraction after winding.
[00101] Furthermore, since it is difficult to directly measure the volume fraction of austenite during production, a small piece is cut from the plate before hot rolling, the small piece is laminated and compressed at the same temperature and reduction lamination than that in the final passage of the hot and water-cooled rolling mill immediately after cooling at the same cooling rate as that during a period from the hot rolling and winding, the phase fractions of the small part are measured and a sum of the volume fractions of cooled martensite, tempered martensite and retained austenite is considered as a volume fraction of austenite during winding, in determining the volume fraction of austenite during winding according to the present invention.
[00102] The process of cooling the steel sheet after winding is important to control the distribution of Μη. The distribution
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44/104 Mn according to the present invention can be obtained by cooling the steel sheet from the coiling temperature at (coiling temperature -100) ° at a rate of 20 ° C / hour or less, while austenite fraction is adjusted to 50% or more during winding and the following equation (3) is satisfied. Equation (3) is an index that represents the degree of progression of the distribution of Mn between ferrite and austenite and represents that the distribution of Mn continues, additionally, as the value on the left side becomes larger. In order to additionally make the Mn distribution continue, the value on the left side is preferably 2.5 or more, and more preferably 4.0 or more. Although the effects of the present invention can be achieved particularly without determining the upper limit of the value on the left, it is preferred that the upper limit is 50.0 or less, since it is necessary to retain heat for a long time to maintain the above 50.0 and manufacturing costs increase significantly.
Equation 3
Tc: winding temperature (° C)
T: steel plate temperature (° C) t (T): maintenance time at temperature T (second) [00103] In order to make the Mn distribution proceed between ferrite and austenite, it is necessary to maintain a state where both phases coexist. If the cooling rate from the winding temperature (winding temperature -100) ° C exceeds 20 ° C / hour, the phase transformation proceeds excessively, the austenite in the steel plate may disappear and therefore the cooling rate from the winding temperature (winding temperature -100) ° C it is set to 20 ° C / hour or less. For the purpose
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45/104 to make the Mn distribution continue the cooling rate from the winding temperature (winding temperature 100) ° C is preferably 17 ° C / hour or less, and more preferably, 15 ° C / hour or less. Although the effects of the present invention can be achieved particularly without determining the lower limit of the cooling rate, it is preferred that the lower limit is 1 ° C / hour or more, since it is necessary to perform heat retention for a long time period of time in order to keep the cooling rate at less than 1 ° C / hour and manufacturing costs increase significantly.
[00104] In addition, the steel sheet can be reheated after winding within the satisfaction range of Equation (3) and the cooling rate.
[00105] Acid pickling is carried out on the hot-rolled steel plate thus manufactured. Acid pickling is important to optimize a phosphatability of the cold rolled high strength steel sheet as a final product and a hot dip zinc plating property of the cold rolled steel sheet to a galvanized steel sheet or sheet galvanized and annealed steel, since the oxide on the steel plate surface can be removed by stripping. In addition, acid pickling can be carried out once or a plurality of times.
[00106] Then, the hot-rolled steel sheet after acid pickling is subjected to cold rolling in rolling reduction from 35 to 80% and is made to pass through a continuous annealing line or a continuous galvanizing. By adjusting the lamination reduction to 35% or more, it is possible to keep the shape flatter and optimize the ductility of the final product.
[00107] In order to optimize the stretch stretching capacity, it is preferred that the regions where the concentration of Mn is
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46/104 high and the regions where the Mn concentration is low have a narrow distribution in the Mn distribution in the subsequent process. In order to do so, it is effective to increase the lamination reduction during cold rolling, recrystallize the ferrite during the temperature increase and make the grain diameters finer. In such a view, the lamination reduction is preferably 40% or more, and more preferably 45% or more.
[00108] On the other hand, in the case of cold rolling in the lamination reduction of 80% or less, the a rolling load is not excessively large and it is not difficult to perform the cold rolling. For this reason, the upper limit of the lamination reduction is set to 80% or less. In view of the cold rolling load, the lamination reduction is preferably 75% or less.
[00109] Furthermore, the effects of the present invention can be achieved particularly without determining the number and passes of lamination and reduction of lamination of each pass. In addition, cold rolling can be omitted.
[00110] Next, the cold-rolled steel sheet obtained is induced to pass through the continuous annealing line to manufacture the high-strength cold-rolled steel sheet. In relation to a process in which the cold rolled steel sheet is induced to pass through the continuous annealing line, a detailed description of a temperature history of the steel sheet will be given, when the steel sheet is induced to pass through of the continuous annealing line, with reference to FIG. 5.
[00111] FIG.5 is a graph illustrating the temperature history of the cold rolled steel sheet when the cold rolled steel sheet is induced to pass through the continuous annealing line, which is a graph showing the relationship between cold rolled steel sheet temperature and time. In FIG. 5, a track from (the point of Ae3
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47/104
- 50 ° C) at the Bs point is shown as a ferrite transformation temperature region, a range from the Bs point to the Ms point is shown as the bainite transformation temperature range and a range from the Ms point at room temperature is shown as the martensite transformation temperature range.
[00112] In addition, the point of Bs is calculated based on the following equation:
Bs Point [° C] = 820 - 290C / (1 - VF) - 37Si - 90Mn - 65Cr
- 50Ni + 70AI [00113] In the above equation, VF represents the volume fraction of ferrite and C, Mn, Cr, Ni, Al and Si represent added amounts [% by mass] of the elements.
[00114] In addition, the Ms point is calculated based on the following equation:
Ms Point [° C] = 541 - 474C / (1 - VF) - 15Si - 35Mn - 17Cr
- 17NÍ + 19AI [00115] In the above equation, VF represents a fraction of ferrite volume, C, Si, Mn, Cr, Ni and Al represent added amounts [% by mass] of the elements. In addition, since it is difficult to directly measure the volume fraction of ferrite during production, a small piece of the cold rolled steel sheet before the cold rolling sheet is made to pass through the continuous annealing line is cut and annealed based on the same history of temperature history as that when the small part is induced to pass through the continuous annealing line, the dispersion in the volume of ferrite in the small part is measured and a numerical value calculated using the result of the measurement is considered as the volume fraction VF of ferrite, in determining the point of Ms in the present invention.
[00116] As shown in FIG. 5, a heating process
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48/104 for the annealing of the cold rolled steel sheet at a maximum heating temperature (T1) which is in the range from 750 ° C to 1000 ° C is first performed by inducing the cold rolled steel sheet passing through the continuous annealing line. If the maximum heating temperature T1 in the heating process is less than 750 ° C, the amount of austenite is insufficient and it is not possible to ensure a sufficient number of hard structures in the phase transformation during the subsequent cooling. From this point of view, the maximum heating temperature T1 is preferably 770 ° C or more. On the other hand, if the maximum heating temperature T1 exceeds 1000 ° C, the diameter of the austenite grain becomes thick, the transformation hardly continues during cooling, and it is difficult to obtain sufficiently a soft ferrite structure, in particular . From this point of view, the maximum heating temperature T1 is preferably 900 ° C or less. [00117] Next, a first cooling process for cooling the cold rolled steel sheet from the maximum heating temperature T1 to the ferrite transformation temperature range or less is performed as shown in FIG. 5. In the first cooling process, the cold-rolled steel sheet is kept in the ferrite transformation temperature range for 20 seconds to 1000 seconds. In order to sufficiently produce a soft ferrite structure, it is necessary that the cold-rolled steel sheet be maintained for 20 seconds or more in the ferrite transformation temperature range in the first cooling process, and the steel sheet Cold rolled is preferably maintained for 30 seconds or more, and more preferably, maintained for 50 seconds or more. On the other hand, if the time during which the cold rolled steel sheet is kept in the temperature range of transformation of ferrite exceeds
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49/104 After 1000 seconds, the transformation of ferrite proceeds excessively, an amount of untransformed austenite decreases and a hard structure cannot be sufficiently obtained.
[00118] In addition, a second cooling process in which the cold rolled steel sheet, after being kept in the ferrite transformation temperature range for 20 seconds to 1000 seconds to cause the ferrite transformation in the first cooling process, is cooled at a second cooling rate and the cooling is stopped within a range from the point of Ms -120 ° C to the point of Ms (the temperature of initiation of martensite transformation) is performed as shown in FIG. 5. Through the execution of the second cooling process, it is possible to proceed with the transformation of untransformed austenite martensite to proceed.
[00119] If the second cooling stop temperature T2, at which the second cooling process is stopped, exceeds the point of Ms, martensite is not produced. On the other hand, if the second cooling stop temperature T2 or lower than the point of Ms 120 ° C, most parts of the untransformed austenite become martensite, and it is not possible to obtain a sufficient amount of bainite in the subsequent processes . In order to ensure that a sufficient amount of untransformed austenite remains, the second stopping temperature of the T2 cooling process is preferably the point of Ms -80 ° C or higher, and more preferably, the point of Ms - 60 ° C or higher.
[00120] In addition, it is preferred to prevent the bainite transformation from proceeding excessively in the bainite transformation temperature range, which is a temperature range between the ferrite transformation temperature range and the transformation temperature range of martensite, in the cooling of the steel plate from the time range
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50/104 ferrite transformation temperature at the martensite transformation temperature range in the second cooling rate in the second cooling process. For this reason, it is necessary to adjust the second cooling rate in the bainite transformation temperature range to 10 ° C / second or more, on average, and the second cooling rate is preferably 20 ° C / second or more, and more preferably, 50 ° C / second or more.
[00121] After executing the second cooling process that stops cooling in a range from the point of Ms - 120 ° C to the point of Ms, as shown in FIG. 5, a maintenance process is carried out in which the steel plate is kept within a range from the second cooling stop temperature to the point of Ms for 2 seconds to 1000 seconds, in order to cause the transformation of martensite proceed further. In the maintenance process, it is necessary to keep the steel plate for 2 seconds or more in order to make the martensite transformation proceed sufficiently. If the time during which the steel sheet is kept exceeds 1000 seconds in the maintenance process, the hard bottom bainite is produced, an amount of untransformed austenite is reduced, and bainite with a hardness that is close to that of the ferrite cannot be obtained.
[00122] In addition, after maintaining the steel sheet within the range from the second cooling stop temperature to the point of Ms and causing the martensite transformation to proceed as shown in FIG. 5, a reheating process for reheating the steel sheet is performed in order to produce the bainite with a hardness between the ferrite hardness and the martensite hardness. A temperature T ₃ (reheat stop temperature) at which reheating is stopped in the reheat process is set to the point of Bs (Bainite transformation start temperature
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51/104 (the upper limit of the bainite transformation temperature range)) -100 ° C or more, in order to reduce the dispersion in the distribution of hardness in the steel plate.
[00123] In order to further reduce the dispersion in the distribution of hardness in the steel plate, it is preferred to produce soft bainite with a small hardness different from that of ferrite. In order to produce soft bainite, the transformation of bainite is preferably induced to proceed at a temperature that is as high as possible. Consequently, the reheat stop temperature T ₃ is preferably the point of Bs- 60 ° C or more, and is most preferably the point of Bs or more, as shown in FIG. 5.
[00124] In the reheating process, the rate of temperature rise in the bainite transformation temperature range must be 10 ° C / second or more, on average, and the rate of temperature rise is preferably 20 ° C / second or more, and more preferably 40 ° C / second or more. Since the bainite transformation proceeds excessively in a state of the low temperature range, if the rate of temperature increase in the bainite transformation temperature range is low in the reheating process, the bainite lasts with a large difference in hardness from that ferrite is easily produced, and soft bainite with a small difference in hardness from that of ferrite, which can reduce the dispersion in the hardness distribution in the steel plate, is not easily produced. Consequently, it is preferred that the rate of temperature rise in the bainite transformation temperature range is high in the reheating process.
[00125] According to this modality, a sum (total maintenance time) of the time during which the steel plate is kept in the temperature range of bainite transformation in the second cooling process and the time during which the steel plate steel is kept in
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52/104 bainite transformation range in the reheating process is preferably 25 seconds or, and more preferably, 20 seconds or less, in order to suppress the excessive progression of the bainite transformation in the second cooling process and in the reheating process.
[00126] In addition, a third cooling process is performed to cool the steel sheet from the reheat stop temperature T3 to a temperature that is less than the bainite transformation temperature range, after the reheating, as shown in FIG. 5. In the third cooling process, the steel sheet is kept in the bainite transformation temperature range for 30 seconds or more, in order to make the bainite transformation continue. In order to obtain a sufficient amount of bainite, the steel sheet is preferably kept in the bainite transformation temperature range for 60 seconds or more in the third process, and more preferably, maintained for 120 seconds or more . Although the upper limit of time for which the steel sheet is kept in the temperature range of bainite transformation in the third cooling process is not particularly provided, the upper limit is preferably 2000 seconds or less, and more preferably 1000 seconds or less. If the time that the steel sheet is kept in the bainite transformation temperature range is 2000 seconds or less, it is possible to cool the steel sheet to room temperature before completing the transformation of unprocessed austenite bainite and, thus, additionally optimizing the elastic limit and ductility of the high-strength cold-rolled steel sheet by changing from unprocessed austenite to martensite or retained austenite.
[00127] In addition, a fourth cooling process is performed
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53/104 for cooling the steel sheet from a temperature that is less than the temperature range of bainite transformation to room temperature, after the third cooling process, as shown in FIG. 5. Although the cooling rate in the fourth cooling process is not particularly defined, it is preferred that the average cooling rate is 1 ° C / second or more in order to change the unprocessed austenite to retained martensite or austenite.
[00128] As a consequence of the above processes, it is possible to obtain a high-strength cold-rolled steel sheet with high ductility and high stretch-flanging capacity.
[00129] Additionally, a steel sheet coated with high strength zinc can also be obtained in the present invention by performing zinc electroplating on the high strength cold rolled steel sheet obtained by making the steel sheet steel passes through the continuous annealing line based on the previously mentioned method.
[00130] In addition, the steel sheet coated with high strength zinc can also be manufactured in the present invention by the following method using the cold rolled steel sheet obtained based on the above method.
[00131] That is, the steel sheet coated with high strength zinc can be manufactured in the same way as the case mentioned above, in which the cold rolled steel sheet is induced to pass through the continuous annealing line, except for the fact that the cold-rolled steel sheet is immersed in a zinc plating bath in the reheating process.
[00132] In this way, it is possible to obtain the steel sheet coated with high strength zinc with high ductility and high stretch-flanging capacity, the surface of which includes a zinc-plated layer formed on it.
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54/104 [00133] Additionally, when the cold rolled steel sheet is immersed in the zinc plating bath in the reheating process, the veneered layer on the surface can be bonded by adjusting the reheat stop temperature T3 during reheating process to 460 ° C to 600 ° C and carrying out the bonding process in which the cold rolled steel sheet, after being immersed in the zinc plating bath, is kept at the reheat stop temperature T3 for two or more seconds.
[00134] By performing such bonding processing, the Zn-Fe alloy obtained by bonding the zinc-plated layer is formed on the surface, and the steel sheet coated with high-strength zinc with the plated layer with alloyed zinc provided on its surface can be obtained.
[00135] In addition, the method of manufacturing high-strength zinc-coated steel sheet is not limited to the example above and the high-strength zinc-coated steel sheet can be manufactured by performing the same processing as that in the case mentioned earlier, in which the cold-rolled steel sheet is induced to pass through the continuous annealing line in addition to the steel sheet being immersed in the zinc plating bath in the temperature range of bainite transformation in the third cooling process, by example.
[00136] In this way, the steel plate coated with high strength zinc with high ductility and high stretch-flanging capacity, whose surface includes the zinc-plated layer formed on it, can be obtained.
[00137] When the steel sheet is immersed in the zinc plating bath in the temperature range of bainite transformation in the third cooling process, the veneer layer on the surface can be bonded by performing the bonding processing in the
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55/104 which the cold-rolled steel sheet, after being immersed in the zinc foiling bath, is reheated again to 460 ° C at 600 ° C and maintained for 2 seconds or more.
[00138] Even when such bonding processing is performed, the Zn-Fe alloy that is obtained by bonding the zinc-plated layer is formed on the surface, and the high-strength zinc-coated steel plate that includes the layer plated with zinc with alloy on its surface can be obtained.
[00139] In addition, the lamination for format correction can be performed on the cold-rolled steel sheet after annealing in this mode. However, since work hardening of the soft ferrite part occurs and ductility is significantly degraded if the reduction in lamination after annealing exceeds 10%, the reduction in lamination is preferably less than 10%.
[00140] Furthermore, the present invention is not limited to the examples above.
[00141] For example, the plating of one or a plurality of Ni, Cu, Co and Fe can be carried out on the steel sheet before annealing, in order to optimize the plating adhesion in the steel sheet manufacturing method coated with high-strength zinc according to the present invention.
Examples [00142] The plate containing chemical constituents A to AQ shown in tables 1,2, 19 and 20 was molded, the hot rolling was carried out under conditions (heating temperature of the hot rolling plate, rolling temperature finishing) shown in tables 3, 4, 21, 22 and 29, and winding was performed under conditions (cooling rate after rolling, winding temperature, cooling rate after winding) shown in tables 3, 4, 21 , 22 and 29. Then, after blasting
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56/104 acid, cold rolling was performed in reduction of rolling shown in tables 3, 21 and 22, to obtain the cold rolled steel sheets with thicknesses in Experiment Examples aa bd and in Experiment Examples ca a ds shown in tables 3, 21 and 22. In addition, acid pickling was carried out after winding, and cold rolling was not carried out therein, to obtain the hot rolled steel sheet with thickness in the Experiment Examples dt a dz shown in table 29.
[00143] Subsequently, the cold rolled steel sheet in Experiment Examples aa bd and Experiment Examples ca to ds and the hot rolled steel sheet in Experiment Examples dt to dz were induced to pass through the continuous annealing line to manufacture steel sheets in Experiment Examples 1 to 134. [00144] In inducing steel sheets to pass through the continuous annealing line, the high strength cold rolled steel sheets in Experiment Examples 1 to 134 were obtained based on the following method, under the conditions shown in tables 5 to 12, 23 to 25, 30 and 31 (a maximum heating temperature in a heating process, maintenance time in a temperature range of transformation of ferrite in a first cooling process, a cooling rate in the temperature range of bainite transformation in a second cooling process, a cooling stop temperature in the second pro cooling process, maintenance time in a maintenance process, a rate of temperature rise in the bainite transformation temperature range and the reheat stop temperature in a reheating process, maintenance time in the transformation temperature range of bainite in a third cooling process, the rate of cooling in a fourth cooling process, a sum of a time during which the steel sheet is held in
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57/104 bainite transformation temperature range in the second cooling process and a time during which the steel sheet is kept in the bainite transformation range in the reheating process (total maintenance time)).
[00145] That is, the heating process is performed for the annealing of the cold rolled steel sheet in the Experiment Examples aa bd and in the Experiment Examples ca a ds and the hot rolled steel sheet in the Experiment Examples dt a dz, the first cooling process for cooling the cold rolled steel sheet from the maximum heating temperature to the ferrite transformation temperature range or less, the second cooling process for cooling the cold rolled steel sheet after the first cooling process, the maintenance process for the maintenance of the cold rolled steel sheet after the second cooling process, the reheating process for the reheating of the cold rolled steel sheet after the maintenance process up to temperature reheat stop, the third cooling process for cooling the cold rolled steel sheet, after the reheating process, alongside from the reheat stop temperature to a temperature that is less than the bainite transformation temperature range, in which the cold rolled steel sheet is kept in the bainite transformation temperature range for 30 seconds or more, and the fourth cooling process for cooling the steel sheet from the temperature which is less than the temperature range of bainite transformation to room temperature.
[00146] As a consequence of the above processes, high strength cold rolled steel sheets and high strength hot rolled steel sheets were obtained in Experiment Examples 1 to 134.
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58/104 [00147] Subsequently, a part of the Experiment Examples, in which the steel sheets were induced to pass through the continuous annealing line, that is, the cold rolled steel sheets in Experiment Examples 60 to 63 were subjected to zinc electroplating based on the following method to manufacture the zinc-galvanized steel sheet (EG) in Experiment Examples 60 to 63.
[00148] Firstly, alkaline degreasing, rinsing with water, acid pickling, and rinsing with water were performed on the steel plate, which had passed through the continuous annealing line, as pre-processing for veneering. Subsequently, the electrolytic treatment was performed on the steel plate after pre-processing, using a liquid circulation electroplating device with a leaf bath containing zinc sulfate, sodium sulfate and sulfuric acid in a current density of 100 A / dm2 to a predetermined leaf thickness, and leafing with Zn was performed.
[00149] In relation to the cold rolled steel sheets in Experiment Examples 64 to 68, the cold rolled steel sheets were immersed in the zinc plating bath in the reheating process, when the cold rolled steel sheet was induced passing through the continuous annealing line and high strength zinc coated steel sheets were obtained.
[00150] In addition, in relation to the cold rolled steel sheets in Experiment Examples 69 to 73, the cold rolled steel sheets, after being immersed in the zinc plating bath in the reheating process, were subjected to the processing of connection, in which the cold-rolled steel sheets were kept at the reheat stop temperature T3 shown in table 11 during the maintenance time shown in table 12, to connect the veneered layer on the surface thereof, and the steel sheets coated
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59/104 with high strength zinc with zinc-plated layers bonded were obtained.
[00151] Regarding the cold rolled steel sheet in Experiment Examples 74 to 77, the cold rolled steel sheets were immersed in the zinc plating bath in the third cooling process, when the cold rolled steel sheets were induced to pass through the continuous annealing line, and steel sheets coated with high strength zinc were obtained.
[00152] Regarding the cold rolled steel sheets in Experiment Examples 78 to 82, the cold rolled steel sheets, after being immersed in the zinc plating bath in the third cooling process, were subjected to the bonding process in the which the cold rolled steel sheets were reheated again to the bonding temperature Tg shown in table 12 and maintained for the maintenance time shown in table 12, to bond the clad layers on their surfaces, and the coated steel sheets with high-strength zinc with bonded zinc-plated layers were obtained.
[00153] In relation to the hot-rolled steel sheet in Experiment Example 130, the high-strength zinc-coated steel sheet with the zinc-clad layer was obtained by immersing the steel sheet, which was made to pass through the continuous annealing line in the zinc plating bath, then carrying out the bonding process in which the steel plate was reheated again to the bonding temperature Tg shown in table 31 and maintained for the time maintenance shown in table 31, and, thus, connecting the veneer layer on its surface.
[00154] Regarding the hot rolled steel sheet in the Example
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60/104 of Experiment 132, the high-strength zinc-coated steel sheet with the zinc-clad layer was obtained by immersing the hot-rolled steel sheet in the zinc-plating bath when the hot-rolled steel sheet hot was induced to pass through the continuous annealing line, carrying out the bonding process in which the hot-rolled steel sheet was reheated again to the bonding temperature Tg shown in table 31 and maintained during the maintenance time shown in table 31, and, thus, connecting the veneer layer on the surface thereof.
[00155] Regarding the hot rolled steel sheet in Example 134, the steel sheet that was induced to pass through the continuous annealing line was immersed in the zinc plating bath, and the steel sheet coated with high zinc resistance was obtained.
[00156] Regarding the high-strength steel plates obtained in this way in Experiment Examples 1 to 134, microstructures were observed, and the volume fractions of ferrite (F), bainitic ferrite (BF), bainite (B), tempered martensite (TM), fresh martensite (M) and retained austenite (retained γ) were obtained based on the following method. In addition, B + BF in the tables represents a fraction of the total volume of ferrite and bainitic ferrite.
[00157] Regarding the fraction of volume of austenite retained, an observation surface in a thickness of 1/4, which was parallel to the surface of the steel plate sheet, was considered as an observation surface, the analysis of rays X was performed on it and a fraction of the area was calculated and considered as the volume fraction of the same.
[00158] Regarding the volume fractions of ferrite, bainitic ferrite, bainite, tempered martensite and fresh martensite, a cross section of the plate thickness that was parallel to the lamination direction of the
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61/104 steel plate was considered as an observation surface, a sample was collected from it, crushing and etching with nital were performed on the observation surface, a region surrounded by sides of 30pm was adjusted in a thickness range to From 1/8 to 3/8 around 1/4 of the plate thickness, the region was observed with FE-SEM, and the area fractions were measured and considered as the volume fractions of the same.
[00159] The results are shown in tables 13,14,17,26 and 32. [00160] Regarding the high strength steel plates in Experiment Example 1 to 134, the cross section of the plate thickness that was parallel to the rolling direction of the steel sheets was finished as mirror surfaces, and the ΕΡΜΑ analysis was performed in a range from 1/8 to 3/8 around 1/4 of the thickness of the plate to measure the quantities of Μη. The measurement was performed, while the probe diameter was adjusted to 0.5pm and a measurement time for one point was adjusted to 20 ms, and the amounts of Mn were measured to 40,000 points in the surface analysis. The results are shown in tables 15,16, 18, 27, 28 and 33. After removing the measurement results from including the measurement results, the maximum and minimum values of the Mn concentration were obtained respectively and the differences between the maximum and minimum values obtained from the concentration of Mn were calculated. The results will be shown in tables 15, 16, 18, 27, 28 and 33.
[00161] For each of the high-strength steel plates in Experiment Examples 1 to 134, a ratio (H98 / H2) of a hardness measurement value of 2% (H2) to a measurement value 98% hardness (H98), which was obtained by converting the measured values, while a difference between a maximum measured value and a minimum measured hardness value was considered to be 100%, a kurtosis (K * ) between the measured hardness value
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62/104 of 2% and the measured hardness value of 98%, an average grain size, and if the number of all measured values in each divided range, which were obtained by dividing a range evenly from the hardness of 2% to the hardness of 98% in 10 parts, was or not in a range from 2% to 30% of the number of all measured values in a graph that represents a relationship between the hardness classified in a plurality of levels and a number of measured values at each level, when each measured value was converted while a difference between a maximum and a minimum value of the hardness measurement values was considered to be 100% were exemplified. The results are shown in tables 15,16, 18, 27, 28 and 33.
[00162] In addition, hardness was measured using a dynamic microhardness tester equipped with a three-sided pyramid indenter Berkovich type under an indentation load of 1 g based on an indentation depth measurement method . The hardness measurement position was adjusted to a range from 1/8 to 3/8 around 1/4 of the plate thickness in the cross section of the plate thickness that was parallel to the rolling direction of the steel plate. In addition, the number of measured values (number of indentation points) was in the range from 100 to 10,000 and, preferably, 1000 or more.
[00163] In addition, the average grain size was measured using an EBSD (backscattered electron diffraction) method. A grain size observation surface was adjusted to a range from 1/8 to 3/8 around 1/4 of the plate thickness in the cross section of the plate thickness that was parallel to the lamination direction of the plate. steel. Then, an edge, in which a difference in crystal orientation between the measurement points that were adjacent in the bcc crystal orientation on the observation surface was 15 °
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63/104 or more, on the observation surface was considered as a crystal grain boundary, and the grain size was measured. Then, the average grain size was calculated by applying an interception method to the result (map) of the obtained crystal grain limit. The results are shown in tables 13, 14, 17, 26 and 32.
[00164] In addition, the tensile test pieces based on JIS Z 2201 were collected from high strength steel plates in Experiment Examples 1 to 134, tensile tests were performed on them based on JIS Z 2241, and maximum tensile strength (TS) and ductility (EL) were measured. The results are shown in tables 15, 16, 18, 27, 28 and 33.
TABLES
Table 1
Experiment Example ç Si Mn P s Al N O% in large scale % in large scale % in large scale % in large scale % in large scale % in large scale % in large scale % in large scale THE 0.185 1.32 2.41 0.006 0.0016 0.043 0.0039 0.0008 Example B 0.094 1.79 2.65 0.012 0.0009 0.017 0.0020 0.0011 Example Ç 0.128 1.02 2.87 0.022 0.0007 0.127 0.0028 0.0014 Example D 0.234 0.85 2.15 0.005 0.0004 0.233 0.0016 0.0011 Example AND 0.167 1.38 2.16 0.013 0.0021 0.026 0.0030 0.0009 Example F 0.219 1.47 1.82 0.007 0.0020 0.061 0.0025 0.0020 Example G 0.242 0.50 2.37 0.007 0.0043 1,175 0.0040 0.0022 Example H 0.124 1.65 2.14 0.005 0.0043 0.032 0.0050 0.0010 Example 1 0.104 2.28 1.95 0.018 0.0046 0.030 0.0023 0.0018 Example J 0.076 1.82 2.48 0.018 0.0013 0.064 0.0056 0.0009 Example K 0.197 0.78 2.82 0.005 0.0021 1,310 0.0054 0.0008 Example L 0.159 1.09 3.01 0.005 0.0040 0.029 0.0028 0.0016 Example M 0.088 2.06 2.50 0.020 0.0032 0.015 0.0034 0.0017 Example N 0.080 1.52 2.01 0.022 0.0023 0.046 0.0032 0.0018 Example O 0.172 1.33 2.67 0.014 0.0032 0.086 0.0039 0.0043 Example P 0.223 0.38 3.02 0.009 0.0037 2.304 0.0015 0.0012 Example Q 0.137 2.08 2.12 0.013 0.0045 0.075 0.0020 0.0015 Example R 0.143 1.13 1.59 0.004 0.0041 0.020 0.0060 0.0021 Example s 0.173 0.85 2.37 0.010 0.0004 1.526 0.0048 0.0023 Example T 0.167 1.95 1.79 0.009 0.0032 0.091 0.0016 0.0016 Example
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Experiment Example ç Si Mn P s Al N 0% in large scale % in large scale % in large scale % in large scale % in large scale % in large scale % in large scale % in large scale U 0.211 0.41 2.56 0.012 0.0043 0.683 0.0034 0.0023 Example V 0.226 1.26 1.68 0.003 0.0029 0.746 0.0014 0.0010 Example W 0.025 1.99 2.19 0.014 0.0039 0.046 0.0058 0.0021 Comparative Example X 0.519 1.22 1.84 0.018 0.0047 0.036 0.0033 0.0010 Comparative Example Y 0.175 0.03 2.14 0.019 0.0036 0.050 0.0034 0.0008 Comparative Example z 0.205 0.93 0.57 0.009 0.0037 0.099 0.0020 0.0015 Comparative Example
Table 2
Ex. YOU Nb B Cr Ni Ass Mo V Here Ce Mg ETRExperienced %in %in %in %in %in %in %in %in %in %in %in %inment pasta pasta pasta pasta pasta pasta pasta pasta pasta pasta pasta pastaTHE Example B Example Ç 0.0016 Example D0.0013 Example AND 0.017 Example F 0.065 0.0014 0.0007 Example G0.046 Example H 0.0300.0016 0.0014Example I 0.0034Example J 0.021 0.019 Example K 0.31 Example L 0.25 Example M0.42 Example N 0.29Example O 0.071 Example P 0.0530.00110.18 0.0032 Example Q 0.42 0.22 0.0012 Example R 1.29 0.10 0.0013 Example s 0.0280.0008 0.10 0.27 0.14 0.070.0007 0.0009 Example T0.0270.78 0.086 0.0018Example u 0.017 0.050 0.60 0.10 0.00280.0015 Example V 0.0029 1.11 0.50 0.039 0.0018 0.0018 Example w Comparative Example X Comparative Example Y Comparative Example z Comparative Example
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The Q E 8 LU The Q E8 LU The Q E8 LU the Q E8 LU The Q E8 LU the Q E8 LU the Q E8 LU The Q E8 LU the Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU Comparative | The Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU the Q E8 LU the Q E8 LU The Q E8 LU the Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU The Q. E8 LU Cold rolled sheet thickness AND IS CD CD 00 θ ' CN CN CN CN CN CD CD CD 00 θ ' CO CN CN CN CN CN CN CN 00 o CO CO CO CO CO CO Lamination reductionThe LO The LO 00 CO O CO CO the CO CO The LO The LO CO 00 CO 101 The LO The LO The LO The LO The LO The LO CN 1 ^ 00 CO 00 CO 00 CO 00 CO 00 CO the LD ω OO CN 03 The LO 0003 o> 1 ^ 00 δ δ O> 03 1 ^ δ LO δ 03 THE LO δ CO CN LO LO CN LO LO 03 LO CO!O CN CN LO THE CO LO CO CO LO 03CN LO 1 ^ CN LD δ LD CN δ 00 the LD O3 Volume fraction of Austenite Φ E3g EΦ ae CN CO O O O03 CN 1 ^ CO00 1 ^1 ^ 0000 LO 03 00 LO CN 1 ^ 03 CN 1 ^ 00 03 1 ^ 00 1 ^ CO03 s 00 1 ^ CO03 O o O03 CO00 1 ^ 03 the o CO00 CO00 Cooling rate after winding And the 6thCO LO 00 CN00 03 CO 03 00 00CN CN LO 1 ^ 03 O CO CO LD 00 CN Left side of the equation (1)CN CO CN o> CNCO o> LO 1 ^ LO 00 c T hCN CNCO CN CN CNIOhCNCO <Ô CN oo O> LD O> 00 IO Winding temperature OO THE COCONUT CO 1 ^ LO s CO CO CN LO δ CO CO OCO δ 1 ^ δ CO 1 ^ LO 00 CN LO 00 the CO $ CO CO LO CO δ LO CNLO LO LOLO 1 ^ CO LO δ LO 00 CN LO CO CO CO CO CO LD CO δ 03 LD LD 1 ^ CN CO CO 1 ^ LD 1 ^LD Cooling rate after lamination The ΌÇ03ΦCO O o 00CN CO 00 £ o> CO CNCO CN δ 03 CO 03 CN LO CN POO 03 1 ^ 1 ^ CO 03CO 00 CO LD LD CO CN CN CN 1 ^ the CO CO Finish laminating temperature OO o> o 03 1 ^ CO 03 CO s> 03 O 03 δ00 δ00 CO LO 03 CN O 03 O0300 O0300 00 or 03 00 δ O3 LO CO 00 030300 03CN 03 CN CO 00 1 ^ 03 00 LO3 CO o 03 δ00 CN 03 δ03 δ03 the LD 03 CO δ Air Transformation Point3 P LO CO CO LO CO CO LO CO CO 00 CO 00 CO 00 CO CO CO CO CO CO CO 1 ^ CO CO 1 ^ CO CO LO 03 CO LO 03 CO LO 03 CO £ £ CN 00 CO CN 00 CO The CN 1 ^ the CN 1 ^ The CN 1 ^ LD CO 1 ^ LD CO 1 ^ LD CO 1 ^ CN CN LD CO Plate heating temperature OO the CO CN LO CO CN OCN LOCN LOCN LO LO CN LOCN OCN LO 1 ^ LO CO O03 LO THE CN LO CO LO CN CN LO CN CN OCN the COCN LO CO LO 03 the 1 ^ OCN LD 1 ^ The CN COCN The 1 ^ CN OCN Chemical constituent < < < m m m O O Q Q LU LU LU LL LL O O T T T "5 "5Experiment Example 03 £ 3 O Ό Φ M— 03 £ .XAND Ç O Q σC03 > 3 X > N
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The Q E 8 LU The Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU the Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU the Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU the Q E8 LU the Q E8 LU The Q E8 LU the Q E8 LU The Q E8 LU the Q E8 LU the Q E8 LU the Q E8 LU the Q E8 LU the Q E> LU 1ro§ It's the The Q> LU § E <0 Q E8 The Q> LU comparative | the Q E> LU comoarativo 1 Cold rolled sheet thickness AND IS CD CN CN 00 o 00 o CN CN CN 00 o 00 o 00 o 00 o 00 o CD CD CD CD CD CD CD CD CD CD CD CN CN CD CD Lamination reductionThe LO The LO The LO the CO the CO The LO s POO the CO s CN 1 ^ 00 CO 00 CO the LO The LO The LO The LO The LO s 00 CO The LD The LD O O CO CO CN 1 ^ The LD The LD The LD ω OO LOLO O> CO CN LO CN o CN 00 CO CO LO 3 LO the CO LO 1 ^ 00 s CO00 00CD o> σ> LO s CO00 CO CN LO CN LO E LO 3 CO CO OCO 1 ^ 00 AND Os CO LD LD CO σ> AND 1 CO LD LD CO00 Volume fraction of Austenite ω E D § E ω ô O> CO 00 1 ^ O O and 1 ^ CO O o CO 1 ^ O>00 the o O00 00 σ> 3 s O00 s s 1 ^ 00 CN CO CO00 o>00 1 ^ 00 O> 1 ^ s 0000 00 1 ^ CO 1 ^ HI 1 ^ 00 CN 1 ^ CO CN Cooling rate after winding 2o 6th LO CO COLO CO CNo> LO 00 CO -the CN -LO CO CO CO CN 1 ^ - CN- - O CN Left side of the equation (1)CN CN V CN o> hCNO CO CNLO CN LO 1 ^ o> 00 CN b- CN 00 LO 1 ^ oo CO CN - 00 CN l < CD 00 l < CO o * CN 1 ^ CO co B-CN CD E LD b- CN 1 ^ b- Coiling temperature OO 1 ^ LO CN LO CO e CO 1 ^ LO AND o> CN CO 00 the CO 00 the LO 00 CO LO LO 1 ^ LO crazy 1 ^ e CO CO LO E LO LO E 1 ^ CO O00 LO CN CO LO CN CO CO 1 ^ LD AND O>00 LD the CN CO O3 O00 LD o> CO ANDCO LD CO LD LD CO CO3 Cooling rate after lamination The ΌÇ3 σ ΦCO O o The LO The CN o> 1 ^ AND LO CO 0000 CO CN 00 CO CO o CO CN O> 00 LO CO CO 00 CO CN 1 ^ LO CN LO CN POO CO O> 1 ^ CO 00 CO the CN CO LD CO CO LD CO LD 00 LD The LD Finish laminating temperature OO CO E CO CN o 00 o σ> CO O 00 O o σ> 005 CO 00 CO 1 ^ 00 o>5 O> o 1 ^ CO σ> 5O CO o σ> CN 1 ^ 00 00 LO O CN 1 ^ 00 O> o 00 s00 4 σ> CO CO σ> CO0000 CO σ> The CN o> o> o σ> 00 5 CN CO 00 CO CO O 00 CO O 1 ^5 Air Transformation Point3 OO 1 ^ LO CO 00 σ> LO 00 σ> LO CN O CO CN O CO o> CN 1 ^ o> CN 1 ^ o> CN 1 ^ 003 003 003 LO 1 ^ CO LO 1 ^ CO LO O 1 ^ LO O 1 ^ CO00CO CO00CO 1 ^ o 1 ^ the 1 ^ the 1 ^ LD LD AND AND O> 1 ^ CO o> 1 ^ CO LD 1 ^ LD O CO ANDCO 00AND Plate heating temperature OO LO CO LO CO CN the 1 ^ LOCN LOCN O00 OCN LO LO LO THE CN the LO CN LO LO CN LO CO LO CO the CO CN OCN o the CN the LO LO CO CN OCN LD the CN LD CO CN the CO LD 00 LDCN The σ> LD the CN LD LD OCN LD CN CN O00 Chemical constituent x _l _l z z Z O O O □ _ □ - σ σ 0Í 0i ω ω ω Π Π D D > > §1 XI > 1 NI Experiment Example 0303 £ 3 03 O03 Ό03 Φ03 to Ol 03 £03 '03 to 03 03 AND03 ç03 O03 Q03 σ03 dog CO03 03 303 frog 1to03 £ 3 £ 3 £ 3 £ 3 Ό £ 3
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The Q E8 LU OQAND8LU OQAND8LU the Q E8 LU The Q E8 LU The Q E8 LU OQAND8LU OQAND8LU the Q E8 LU Comparative | Example | OQAND8LU Example I the Q E8 LU the Q E8 LU Comparative | OQAND8LU OQAND8LU The Q E8 LU Comparative | The Q E8 LU The Q E8 LU οQAND8LU OQAND8LU the Q E8 LU the Q E8 LU Example | | Second Cooling Process I Cooling termination temperature -Ms OO -52 | -93 I CO 1 -40 | 00 in1 -64 | -66 | -23 -54 | -49 I -94 I 001 1 -83 | -85 | oõ1 00 l · -1 -60 | -62 | -36 | -62 | 00 l · -1 0000 1 Cooling termination temperature112) OO 257 | oõ 268 | 236 | 308 | 291 | 270 | 259 | 305 275 | 271 | 219 | 304 | 255 CXI 228 | 272 261 | 282 | 284 | 302 | 309 | 271 | | 281 | Average cooling rate in Bainite Transformation Temperature range ° C / second 57 | 64 | 85 I 68 | 60 | 62 | 74 | 74 | 0000 83 | 00 s 79 | 60 59 I 62 | 60 67 | 00 67 | 67 | 56 | 68 | | 69 | First cooling process | Maintenance time in ferrite transformation temperature range O o c D σ φCO l · - 82 | 39 I M00 126 | 79 | 149 | 164 | 150 I 99 0075 | 70 42 | 49 I CDI 85 | Μ CXI 90 I 77 | 35 | 53 | CXI Maximum heating temperature(T1) OO 822 | 835 | 839 | 845 | 837 | 00M-00 831 | 843 | 00 CO 00 827 | The Μ 00 803 | 00 o 00 802 817 | 833 | O0000 l 00 865 | 845 | 837 | 872 | 921 | 936 | Steel type Say O CR | CR | Say O Say O Say O CR | CR | CR Say O CR | CR | Say O CR CR | CR | CR Say O Say O CR | CR | Say O Say O Say O Chemical constituent < < < m m m O O O α α LU LU LU LL LL LL 0 0 I I I - - Cold rolled steel sheet CO _Q O TJ (D M— 03 .ç. .ç. - - El Ç O O Q σCO - D > Experiment ExampleCXI COLD CD r- 00OCXI COLD CD r- 00 σ> 120 | CXI CXI CXI CO CXI MCXI
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O Q E g LU ComDarativo I O Q E g LU O Q E g LU O Q E g LU O Q E g LU O Q E g LU ComDarativo | CO 03 00 CN 00IOCO1 CO1 CO1 LO1 1CO00 00 CNOCO O CO H"- COCO CO CN CN ioio H"- CN LO 00CO H"- CO 00 001730 h (O H"- 284 | 457 |00O> CN O CN CO00 LO CO CO O0000 00 00 03 03DíDí Dí Dí Dí DíOO O O O O- "3 "3 X > N POO aa io(O H"- 00 03 OCNCN CN CN CN CO
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The Q E 8 LU The Q E8 LU ο Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU Comparative | The Q E8 LU Comparative | The Q E8 LU Comparative | The Q E8 LU Comparative | LT)00 O O 1 ^ CO CO CNOOO>CO1 1 ^1 LO1 001 001 1 ^1CO1 CO1 0011O O> O CO CO O O 00 30000CNCOLO COCOCOinCNCO CN CN CN CN CN CN CN CO CNCN1 ^ LT) 54 |1 ^ LO00 CO001 ^LOLO 00 1 ^ LO LO CO 1 ^ LOLO000035 | 1 ss 1 47 I 59 |202 | 00 1 ^ 155 | 46 65 s 54 CN C7> CN 4 CN 1 ^ CO 00 CNOLOOO 1 ^ LOCO 1 ^ LO COCN1 ^O) 00 00 00 00 00 00 00 00000000rr rr rr rr rr rr rr rr rrrrrrrrO O O O O O O O OOOOω ω 1- 1- D D > > §1 XI > 1 NI COD > $ X > n 03 OT)03 03 03 03 03 CO 03 CO -Q-Q-Q-QCO σ> OCN COLO CO1 ^00C7> LO LO LO LO LO LO LOLOLOLO
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O Q E g LU OQE g LU O Q E g LU Comparative | O Q E g LU OQE g LU O Q E g LU ComDarativo 1 O Q E g LU O Q E g LU O Q E g LU OQE g LU OQE g LU O Q E g LU O Q E g LU Example 1 ComDarativo 1 Example I Example | Example | o Q E g LU O Q E g LU Comparative | CO - 00 CXI o> o> CO CD 00 CXI 00 CO Hi CO 00 Hi O CO O O CO COCXI CXI CD CO LD HiCXI1 CO LDCXI CD1 1 ld1CO1 ld1 CO11 LD1 1 LD1 CD1 11 1 CO1 1 CXI1ld H"- 00ld H"- H"-H"- 00 LD CDLD CXI H"-H"- LD LDLDldCOr »- CD OH"- CO HiCD O CXI 00 LD 00 Hi 00 LDLD LD LD LDLD H"-CXI CD LDCD LD CDr- LD CXI r-00H"- LD LD CXICXI CXI CXICXICXI CXI CXICXILD LD r- LD CD Hi 00Hi CD CXI r- - HI 00 CD - - LD CXI COLD CD r- 00 Hi | 20 I CXI 122 | | 23 | 124 | 25 CD CXI 127 | 00 CXI Hi CXI 30
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The Q E 8 LU Comparative | The Q E8 LU the Q E8 LU 1203 Q E o Othe Q E8 LU 1 the Q E8 LU The Q E8 LU the Q E8 LU The Q E8 LU the Q E8 LU the Q E8 LU The Q E8 LU the Q E8 LU The Q E8 LU the Q E8 LU the Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU the Q E8 LU The Q E8 LU Comparative | The Q E8 LU o> g § E o O ExampleHow to The Q E8 LU Comoarativo | CO O) 1 ^ S | - CN CN CN O) rt · - O) rt · rt · CN CN CO O) CN O CN CO O) 1 ^ O CO CN rt · O O) CN1 LO CO1 O)1 and1 the CO1 00 O LO O1 CO1 T CN CO1 CO COCN 1 O 00 CO1 the CN 1 CO CN the CO1 1 ^ 1 ^1 ^ LO 3 LO 00 CN 1 ^ CO the LO COLO 00AND 1 ^ CO the 1 ^ the CN LO CO LO S LO CO o LO the CO LO O AND LOAND o o LO 1 ^ CO 00 CO COAND CO CNAND s LO CO CN LO CN LO CN CO CN LO CO rt · rt · CN 1 ^ The CN LO CN CN CN - CO CN CO CO CN 1 ^ CN 00 LO CO CN O 1 ^ CN 00 rt · CO O O CN O CO CO 00 rt · - LO 1 ^ 1 ^ O LO O O) CO 1 ^ 1 ^ LO O O POO 1 ^ CO 00 CO the CO O rt · CN COLO CO 1 ^ 00 O the LO AND CN LO CO LO LO LO LO CO LO 1 ^ LO 00 LO the LO
the Q E8 LU the Q. E8 LU 1 CO ç 03CO 1- Cl) Ό 03 O « O Ç ç t O O) O s 0) 03 ° CO CN Ό 2 CD Ό * 03 O <03 Cl) O Q. 03 F F CD1- £CO m Cl) 03 Ό Ç O O 03 m ç CD O O) 1 ^ 1 ^ LD <1)° Ό the t03 03 O 3 03 03 £ Cl) £ n CO And cd ç2 1- 1- O ç Cl) AND 03 03 'CD CO £ O CDT) O ç Cl)3 Ό Φ σ cd CO 1 ^ 1 ^ CO AND CO CDOO AND 2 CL CD O Ό T- 03 X 3 s Cl 1- 1 E i— £ CD C O Ό (Π ç s" 0) AND03M-  P -D E °C <03 O CO CD Q T) 2ç 1 ^ O) CD Ό3 O 1 ^ o «E C .P σ cd* " O Φ U) CO CO 0) P Ç) 2 i- AND t <D CL CD Ό O ° ra O Cl) AND F í ° CD 0) 0) 1- 1— Q Cl) O Ό ç O CD Q. _t F Φ Cl) Q. X X LU LUCN
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The Q E 8 LU the Q E8 LU The Q E8 LU The Q E8 LU the Q E8 LU the Q E8 LU o>AND03Q E o Othe Q E 8 LU the Q E8 LU the Q E8 LU the Q E8 LU the Q E8 LU o>AND03Q E o Othe Q E 8 LU the Q E8 LU The Q E8 LU o>AND03Q E o Othe Q E 8 LU The Q E8 LU the Q E8 LU the Q E8 LU the Q E8 LU the Q E8 LU the Q E8 LU the Q E8 LU ComDarative Example | the Q E8 LU the Q E8 LU the Q E8 LU the Q E8 LU ComDarativo Example | 1 ^ dog LO CO CO 00 riCO O> riCO 3CO laughs ^- Cri CO 00 Cri CO σ> Cri CO OCreate CO Created Created LO O CO 3Cri Poo CO LO CO O> CO CO Create riCO CO riCO 00 COCO £ CO σ> riCO 00 CO CO CO LO Cri s CO CO 1 ^ CO O> o Cri the coconut O σ> Cri CO CO laugh- CO CO laughs ^- £ laughs ^- Cri1 ^ laugh- CO 1 ^ laughs ^- o 1 ^ laughs ^- Cri 1 ^ ri ^- CO CO LO 00 Create LO LO σ> laughs ^- LO O laughs ^- s laughs ^- 1 ^ o LO σ>io CO3 0000 LD 5> LD OIO LO o LO LO Create LO 1 ^ o LO σ>IO 005 the LO o o LO COIO CO CO LO IO CO LO CO O> laugh LO O 1 ^ 00 σ> laugh CO CO - σ> 1 ^ 1 ^ 00 CO laugh O σ> Cri CO - LO laugh - CriCri 3CO £Cri σ> the laughs ^- 1 ^ Laughs ^- O> CO CO σ> 1 ^ riCO dogCO 3Cri O 1 ^ CO CO00 O> LO σ> Cri CO LD CO σ> laughs ^- LD 00 Cri LO o CO σ> o Cri σ> laughs ^- s CO 1 ^ CO Cri LO o Cri 5Cri CO 1 ^ Cri 00 laughs Cri 3CO σ> CO CO laugh LO CO 1 ^ 00 σ> OCri CO laugh LO CO 1 ^ 00 σ> OCri Cri Cri Cri CO Cri laughs Cri LO Cri CO Cri 1 ^ Cri 00 Cri σ> Cri the CO
Petition 870180070295, of 8/13/2018, p. 75/120
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Petition 870180070295, of 8/13/2018, p. 76/120
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The Q E ω X LU the Q E ω X LU the Q E ω X LU the Q E ω X LU The Q E ω X LU the Q E ω X LU | Example | the Q E ω X LU I Example | I Example | I Example | I Example | I Example | I Example | the Q E ω X LU the Q E ω X LU the Q E ω X LU the Q E ω X LU the Q E ω X LU the Q E ω X LU the Q E ω X LU the Q E ω X LU | Example | Reheat process Total maintenance time in temperature rangeBainite transformation Second | CO O CO CN CO CO CO CN LO CO CO r *. COCO CO - - r *.CO CN CO Reheat stop temperature-Bs OO σ> dog CO CN -38 | CN LO CO CN CO -58 | the CO O -30 | r *. CO CN -33 |CN O CO I-25 I 03 CN CO CN Reheat stop temperature(Γ3) OO 485 | LO CO 467 | 437 | 486 | 471 | 497 | I Z89 548 | I frzs 492 | 501 | 507 | 531 | r *. CO 483 | 542 | 521 | 483 | 490 | 494 | 507 | | 501 | Average rate of temperature increase in Bainite transformation temperature range ° C / second | CN CN r *. CN CO CN CO - 03CO CN CNCN The CN O σ> LO CN σ> CN CO CN CO CN CN 03 CO CN The CN Maintenance process Maintenance time in Martensite Transformation Temperature range Second | r *. - CO CO O r *. O 03 COCOLO LO O - σ> σ> CO CO LO Second Cooling Process Cooling termination temperature -Ms OO -64 | Poo I EL I I-43 I 03-30 | CO03 -55 | the LO -44 | -84 | σ> -46 | Γγ -65 | it I w-I dog I-57 I CO LO -98 | I QZ-I Cooling termination temperature(Γ2) OO 270 | I 193 274 | 240 | I Ι · 68 301 | 266 | 312 | 284 | I psz 322 | 249 | 328 | 332 | I εζζ 304 | 281 | r *. o> CN 278 | 287 | 312 | 278 | 263 | Average cooling rate in Bainite Transformation Temperature range ° C / second | s CN CO POO 5 LO CN r *. r *. LO LO LO CO CN σ> CN CN r *. CN r *. LO LO CO σ> r *. σ> CN LO CN 03 r *. r *. First cooling process Maintenance time in Ferrite Transformation Temperature range Second | σ> CO CO Color*. CO LO CN CO the LO 03 LO r *. 5σ> LO CO LO CO the CO Color*. CO LO CO CO LO LO CN LO POO Heating temperaturemax ment(T1) OO σ) CO | 098 809 | 873 | 835 | OCO 822 | 864 | 912 | I 3fr9 832 | 825 | CO CO CO 868 | 829 | 852 | 802 | LO03 837 | 812 | I Zfr8 836 | | 847 | The" &f- tj ro 0 LU 0 LU 0 LU 0 LU 0 0 0 0 0 δ δ δ δ δ 0 0 0 0 δ δ δ δ | GA | Chemical constituent O_l > < m Q z Q_ < m LL - "3 < X 0 - O LU X ξ O Cold rolled steel sheet CT N u CO > CO CO Ό - CT CO 75 u ω Ç 3 X O - Q D.X ω Ό CO dog * Experiment Example CO 5 CN CO POO CO LO CO POO r *. CO POO σ> CO the r *.CN r *. Color*. r *. LO r *. Color*. r *. r *. Color*. 03 r *. the CO dog CN CO
Petition 870180070295, of 8/13/2018, p. 77/120
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ο Q Ε ω X LU | Example | the Q E φ X LU The Q E φ X LU The Q E φ X LU the Q E φ X LU the Q E φ X LU the Q E Φ X LU the Q E φ X LU the Q E φ X LU the Q E φ X LU the Q E φ X LU the Q E φ X LU I Example | I Example | I Example | I Example | I Example | I Example | the Q E φ X LU the Q E φ X LU the Q E φ X LU I Example | Connection conditions Maintenance time O Ό c D σ ω ωO O O O O r *. r *. r *. r *. r *. Connection temperature (Tg) ο 504 | | PPS | 909 535 | | 532 | Leaf bath position 1 After annealing 1 I After annealing | 1 After annealing 1 I After annealing I I Reheat process I I Reheat process I I Reheat process I I Reheat process I I Reheat process I I Reheat process I I Reheat process I I Reheat process I I Reheat process I I Reheat process I Third cooling process | I Third cooling process | Third cooling process | I Third cooling process | Third cooling process | Third cooling process | I Third cooling process | Third cooling process | Third cooling process | Start temperature of Martensite Transformation (Ms) ο 334 | 299 | 321 | 283 | 340 | 372 | 296 | 405 | 339 | 334 | 366 | 333 | 377 | 378 | 344 | 369 | 332 | 371 | 359 | 344 | | £ 99 376 | 333 | Bainite Transformation start rate(Bs) ο 476 | COLO475 | CO U) 486 | 513 | 559 | 606 | 494 | 482 | 531 | CN LO 503 | 500 | CN LO CO LO CN LO 491 | 515 | CO CN LO 491 | | 477 | Fourth cooling process Average cooling rate 1 ° C / second Iit CO CO σ>O CO r *. r *. CO CO CO CO -CO LOThird cooling process Maintenance time in Bainite transformation temperature range ο οC D σ φ ω 407 | 248 | the CN 374 | I ί9ί 136 | 179 I CO O 147 | σ> LO the LO r *. CO I opz 267 | 300 | I 9ZZ LO CO CN CO 137 | LO r *. CO POO dog Experiment Example Ο CO 5 CN CO POO CO LO CO POO r *. CO POO σ> CO the r *.CN r *. Color*. r *. LO r *. Color*. r *. r *. Color*. σ> r *. CO dog CN CO
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ο Q Ε φ X LU ο Q Ε φ X LU Ο Q Ε φ X LU Ο Q Ε φ X LU | Example | ο Q Ε φ X LU ο Q Ε φ X LU ο Q Ε φ X LU Ο Q Ε φ X LU 1φ§ Ε ο Ο Q Ε φ X LU ο Q Ε φ X LU ο Q Ε φ X LU Ο Q Ε φ X LU Ο Q Ε φ X LU I ComDarativo | ο Q Ε φ X LU Ο Q Ε φ X LU ο Q Ε φ X LU I ComDarativo | ο Q Ε φ X LU ο Q Ε φ X LU The Q E φ X LU The Q E φ X LU The Q E φ X LU The Q E φ X LU The Q E φ X LU The Q E φ X LU 1Φ § And the The Q E φ X LU The Q E φ X LU the Q E φ X LU The Q E φ X LU The Q E φ X LU 1φ§ It's the ANDD5ω ω g ο Ε φ ο ο '8.<06 ω ω ό ο φ ο§D ω φ QÍ Medium crystal grain AND ιό ’ΐ ΙΌ σ> CXl Ο the r *. r * - “ CXI r * - “ ΙΌ CO C0 r * C0C0 COC0 COC0 CO CXl 21.7 03 CXI CXl ΙΌ CXl CN Ο co CO ΙΌ r * The C < co r *. co 03 CÓ * LO ΙΌ CN co CO ΙΌ co 03 ci D E D § Φ o 8 E LL | Others | • s θ '· Ο Ο - ο - ο Ο ο - Ο Ο CXI Ο Ο Ο - CXI - - - O O O CN O O CN O - O 1 retained γ 1 θ '· ο Ο - ΙΌ ΙΌ CO CO ο CXI Ο r *. ΙΌοCO co - r *. 03 co r *. - 03 LO03 θ '· ο CXI CO ο Ο- CO Ο CO CO Ο - ο CXI Ο CXI CO - - O co O O O co CN CN O COs1- θ '· r *. CXI CXI CO CXI CXI POO ΙΌ CXI CXI ΙΌ CXI CXI CXI σ> r *. CXI CO CXI ΙΌ CO CO σ> σ> ΙΌ the ΙΌ CN CN O HI LO 03 LO CO CN CN | B + BF 1 θ '· ο CO CN POO ΙΌ C0 CO σ> CXI CXI CO CXI CO r *. CXI CO CXI σ> CO σ> ο CO C0POO co CO CN co CO CN CN co CN LO CNPOO CO LL m θ '· CXI CXI ΙΌ CXI σ> CXI ο σ> Ο CXI CO CXI σ> CXI σ> - C0 C0 CO CXI ΙΌ co 03 CN poo CN CO ΙΌ r *. co LO r *. co COI m • 5 θ '· CO σ> CN CO σ> σ> CO CXI CXI CO ΙΌ CO CXI Ο C0 ο CXI CXI CXI ο C0 σ> r *. CNO - O CO - LO O CN CN CN HI LL • 5 θ '· POO ΙΌ r *. CXI r *.σ> CO POO CO Ο CXI ΟCO ΙΌ CO C0 CXI Γ0 |co O CN co CO the co ΙΌ r *. CN CO LO CO O CO CNSteel type 1 «2 1 QÍ Ο 1 «2 1 1 «2 1 QÍ ο QÍ Ο 1 «2 1 1 «2 1 CR 1 «2 1 QÍ Ο 1 «2 1 1 «2 1 CR I «2 I QÍ Ο CR QÍ ο I «2 I I «2 I HELLO I «2 I I «2 I I «2 I CR £ O 1 «2 1 1 «2 1 1 «2 1 CR Chemical constituent < < < m m m Ο Ο Ο Q Q LU LU LU LL LL LL 0 0 T T T - - - "3 "3 Cold rolled steel sheet <0 Ό Ο Ό φ - CT £ £ -.X - Ε Ç Ο Ο Q σωD > 3 X > N poo poo Experiment Example - CXI COΙΌ CO r *. C0 σ> ο - CXI COΙΌ CO r *. C0 03 the CN CN CN CN CO CN CN LO CN CO CN r *. CN CO CN 03 CN the co
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o Q E g LU O Q. E g LU o Q E g LU O Q. E g LU Q E gLU g | g03Q E o Oo Q E 8 w O Q E g LU o Q. E g LU g g03 Q E o Othe Q E8 LU o Q. E g LU O Q E g LU The Q. E gLU O Q E g LU O Q. E g LU Q E gLU O Q. E g LU o Q E g LU o Q. E g LU Q E gLU o Q. E g LU O Q E g LU o Q. E g LU O Q E g LU The Q. E gLU o Q E g LU O |>ra α E o Oα E8 LU 1 Comparative Example | 1 Comparative Example | g | g03Q E o Othe Q E8w 23D(D2nd EΦ ΌThe o03 £ (D CO no Φ ΌCO o Ό .sDCO CD 0Í Medium crystal grain And the. CO LD laughs ⁷ co o laugh ⁷ 1 ϋϋ 1 c *> I created the LD 1 5.8 | 00 Cri hri ⁷ 1 5.0 | hri ⁷ CD 1 5.5 | The CD 00CO1 m 1 CO LD CO The l < CD CD 1 1 CO CD 1 8.9 | 00 o 1 8.4 | CD l < | Volume fraction | | Others | θ '* - O - O O O - O O O O - O O O O - O O O O Cri O O O LD CD O O 03 pΦ0Í • s9 θ '* CO CO N 00 N LD CO LD CO 00 LDO N O O N Cri LD - laugh O laugh N CO O laugh O -• s9 θ '* Cri O LD O O CO - O - laugh CO - O O Cri - O 00 CO Cri O LD CO - Cri - O O Cri Cri 1- • s9 θ '* 1 »5 1 Create CO CO Cri O N 1 w 1 I created 00 Cri O N CO Cri dog Cri Cri 5 Create CO LD CO Cri Cri O 1 »5 1 Cri Cri CD CO 00 CO I created N 00 Cri HI CO Cri LD CO Hi | B + BF I • s9 θ '* laugh ^- LD CO N the CO POO 00 Cri Cri 5 the CO 1 »5 1 O laugh 00 1 | O laughs ^- OCri CD Cri o Cri CD Cri Cri Cri CD Cri o Cri Create CO Cri LD CD 00 Cri Create CO LL m • s9 θ '* CO Cri laugh N LD Cri CO 00 CO O 1 37 1 LD Cri Cri LD dog 00 N laugh 00 LD CO Cri Cri O O 00 CO Cri 00 00 OCri O LD m • s9 θ '* Cri dog O LD OCri O LD Cri laugh laugh CO laugh O O OCri LD Cri Cri LD CO N CD Cri Cri 00 CD laugh laugh LD laughs ^- 00 Cri N Cri LL • s9 θ '* Cri N Cri N laughs ^- CO laughs ^- CO laughs HI OCri POO 1 35 | Create CO LD laughs ^- laugh 00 Cri rich O LD laughs ^- the CO Cri CO laughs ^- 00 CO o Cri LD Cri N LD CO CD Cri 1 83 | Cri LD CO ID | cdI Steel type l yo l 1 yo 1 l yo l 1 yo 1 l yo l 1 yo i l yo i 1 yo i l yo i 1 yo i l yo i 1 yo i l yo i 1 yo i l yo i 1 yo i l yo i 1 yo i l yo i 1 yo i l yo i 1 yo i l yo i 1 yo i l yo i 1 yo i l yo i 1 yo i l yo i Chemical constituent _l _l z z z O O O □ _ □ _ σ σ 0i 0i ω ω ω 1- 1- Z) Z) > > §1 X > 1 NI Cold rolled steel sheet £ 3 03 O03 Ό03 1 ® ^B 1 M—03 03 03 £03 '03 'rô 03 Õ3 AND03 ç03 1 ^0B 1 Q03 σ03 03 CO03 03 D03 1 ^ΛΒ 1 1 ^MB 1 1 ^XB 1 ro 1 1 03 £ 3 £ 3 £ 3 £ 3 Ό £ 3 Experiment Example dog Create CO POO rich LD CO POO 1 1 00 CO the CO The laugh laugh I created CO laughs laughs laughs^- LD laughs ^- CD laughs i 1 00 laughs laughs ^- 1 50 | ld Create LD 1 53 | 1 w 1 1 55 | 1 56 | 1 1 1 58 | The LD
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The Q E8 LU The Q E8 LU The Q E8 LU the Q E8 LU The Q E8 LU the Q E8 LU the Q E8 LU the Q E8 LU the Q E8 LU i §ANDO O the Q E8 LU the Q E8 LU the Q E8 LU the Q E8 LU the Q E8 LU i §ANDO O the Q E8 LU The Q E8 LU the Q E8 LU i §ANDO O the Q E8 LU the Q E8 LU the Q E8 LU the Q E8 LU the Q E8 LU the Q E8 LU the Q E8 LU the Q E8 LU i §ANDO O the Q E8 LU the Q E8 LU the Q E8 LU the Q E8 LU the Q E8 LU ComDarativo | Material quality measurement results << xo θ '* O> laughs ^- POO CO laughs ^- 00 1 ^ The 1 ^ CO LD Create CO 00 CO 21 LD LD 1 ^ CO The LD 0000 CNl cnI Cri laughs ^- laughs LD laughs laughs^- O> LD the CO o>00 LO CO LD laughs ^- CO 1 ^ O> LD 21 laughs ^- 1 ^ Create CO 00 CO o> LD 001 _l LU θ '* Cri Cri laughs Cri Cri laughs Cri Cri laughs Cri CO Cri Cri Cri Cri Cri LD Cri Cri Cri Cri Cri CO Cri LD CO 0) 1 CO OCri Cri o> LD o> O> LD Cri OCri o> Cri Cri o> o> ω1- 030. δ CO £ CO rio CO 1 ^ σ> LD Create 1 ^ LD O Cri Cri o Create CO o LD CO O the o CO Create I created the CO CO σ> CO O CO LD laughs ^- LD Cri Laughs ^- CO CO Cri 1 ^ Cri σ> 1 ^ riCO 1 ^ CO Cri Create LD O POOO OCri σ> o> Create o 00 σ> o 3 00 1 ^ CRI Cri Cri Segregation of Mn the E dSe ra Se 03 CO CO 03 EE Φθ '* CO O 1 ^ 1 ^ θ ' CO δ θ '00 σ> θ ' CO o θ ' LD laughs; 00 Cri O> riθ '' 1 ^ LD θ ' Create 00 Cri 00 riθ ' CO LD θ ' Create riθ ' Cri CO θ ' laughs LO θ ' Cri CO θ ' Create LO θ ' o> LD CO θ ' θ ' LD LD θ ' Cri o> LD θ ' COCO θ ' o 1 ^ θ ' CO 1 ^ θ ' The tCQThe «2I ã gO 03 CO CO03 EE Φθ '* o> OCri 00 σ> σ> o> the LDCri The Cri ΙΟ CriCri σ> wCri POOCri σ> CO Cri CO O CO 00 LD b- 00 CO IO 1 ^ IO POO LD CO LD OCri COCri CO O> CO00 O00 The CD the CD CD Create O> LDCri laughs; Cri Create LOCri LO Cri O103nSá2 E O O 03 CO CO 03 EE Φθ '* CriCO LD h-Cri CriCO OCO 00CO CO CriCO Create LDCO 00 1 ^CO 1 ^ COCO LD laughs;Cri laughs; Cri 1 ^ b- Cri o O Cri CO 00 Cri LD OCri COCri 1 ^ The Cri 1 ^ CD Cri 1 ^ CD Cri LO LO Cri 00 CO Cri o> O> Cri LO CriCri S Cri Cri CriCri richCO laughs b- Create OCO Cri CriCO the COCO Hardness measurement results o E M- _Έ χο θ '* 1 ^ 1 ^ CO 1 ^ LD CO CO LD HI laugh LD laugh CO CO CO laugh laugh LD laugh LO CO laugh laugh 1 ^ O CO LD 1 ^ laugh - sAnd Μ- ‘Χ'03 χο θ '* 1 ^ o> Cri Cri 1 ^ laughs Cri Cri Cri O> Cri Cri o> 00 O> Cri Cri o> CO Cri CO Cri O> OCri CO Cri 00 CO Cri OCri Cri o> 1 ^ CO CO Cri 00 00 Cri Cri o> «X.s o *1 o> σ> θ 'I o> riθ '1 3 θ '1 00 00 θ '1 00 riθ '1 CO LD θ '1 CO CO θ '1CO riθ ''1 Cri LD θ '1 LD riθ ''1 00 σ> θ '1 CO O1 CO riθ '1 s θ '1 CO riθ '1 δ θ '1 00 1 ^ θ '1 1 ^ O1 3 θ '1 LD riθ '1 o> CO θ '1 00 LD θ '1 3 00 CO θ '1 CO 1 ^ θ '1 LD 00 θ '1 CO 1 ^ θ '1 Cri Cri θ '1 Cri T00 σ> TCO00CO s laugh ⁷ 1 ^1 ^ CO CO LDCO the COCO 1 ^ COCO LD COCO POO 3 CO CO oCO 1 ^ COCO CriCO POOCO Create COCO o σ>Cri LDCri 001d 00 COCri the LOCO sCri CO00Cri O> LDCri CO CriCO sCri s>CO CriCreate CO δCO Cri Cri laughs ⁷ Create LDCO the LDCO 00 σ> T > T Cri 00 laughs ^- CO δ CO σ> laugh 1 ^ Create 00 o laughs ^- 3CO 1 ^1 ^ CO o> laughs ^- I created 3 laughs ^- laugh δ laugh- o> Cri laughs ^- 00 σ> CO CO LD laughs ^- CO CO laughs ^- 00 o laughs ^- δCO o> laughs ^- LO O laughs ^- o> Cri laughs ^- o> σ> CO 00 LD laughs ^- CO 1 ^ CO CO Cri LD LD CO laughs ^- σ> CO laughs ^- 1 ^ Cri laughs ^- δCO 1 ^ laugh- Cri T > T LD Cri o> δ OCri laughs Cri 1 ^ CO Cri O> I created the Cri 00 CO 00 Cri OCri 1 ^ LD 00 CO LD O Cri δ 1 ^ 00 laughs ^- the LD laughs LD Cri laughs ^- 1 ^ CO rich LD CO CO laughs ^- δ - O> Ex. OfExperimentCri CO laugh LD CO 1 ^ 00 o> OCri CO laugh LD CO 1 ^ 00 o> OCri Cri Cri Cri CO Cri laughs Cri LD Cri CO Cri 1 ^ Cri 00 Cri o> Cri CO
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Petition 870180070295, of 8/13/2018, p. 82/120
80/104
the Q E8 LU the Q. E8 LU The Q E8 LU the Q. E8 LU the Q E8 LU the Q. E8 LU The Q E8 LU the Q. E8 LU The Q E8 LU the Q. E8 LU The Q E8 LU the Q. E8 LU The Q E8 LU The Q. E8 LU the Q E8 LU the Q. E8 LU The Q E8 LU The Q. E8 LU The Q E8 LU the Q. E8 LU the Q E8 LU the Q. E8 LU the Q. E8 LU AND3D«Φ2nd EΦ ΌThe o03 £ Φ CO n oΦ ΌCO o Ό .sDCO Φ 0Í O '(DE ro «o Φ D O ^l E 0 And the. The CD The CD IO ° θ IO co IO CD 1 ^ LO CN CD O> LO O> CO l < The LO CO CN l < CO00 l < The σΓ LO co 1 ^ CD CO CD Φ E 3O>Φ ΌO103 CO2OF •s θ '* O - O - - - O - O O O O O O - O O O O CO O O O 03 pΦ0Í SP θ '* 1 ^CN LO 00 1 ^ O CO CO CN LO CO CO 1 ^ CO O o> LO O 00 o> 00 LOSP θ '* O O O CN - O O O - O O CN O O O - O O CO O - - O 1- SP θ '* σ> CO CO CN The CN the CN the CO the CO 1 ^ CO CN 1 ^ CN CO 00 CN CO CN CN o> CN POO LO CO CN CN CN 00 CN o> 1 ^ CO O> LL m + m SP θ '* LO CO CN CN O> CN CN CO o> O POO o> CN CO CN LO CO CO CN 00 CN CO LO CN o> 1 ^ CO 00 CN CO CO CN POO CO POO ANDLL LL m SP θ '*CN CN The CN CN CN O - the CO CO o> CO The CN LO The CN 00 CN CO o> O> 00 CN CN CN the CN - LO m SP θ '* CN The CN CN CN 1 ^ CN CN 00 O the CN O O LO - 00 LO o> O 00 O CN CN CN CO CN 00 LL SP θ '* O> CO LO CO CO CN POO 00 CO CO the CN CO 00 CO LO 1 ^ 00 CO O O> CN CN CO 1 ^ CO o> LO O> CO 00 CO 00 COPOO Steel type 0 LU 0 LU 0 LU 0 LU O O O O O <o <o <o <o <o O O O O <o <o <o <o <o Chemical constituent O_l > < m Q z □ _ < m LL - -J < T O - O LU TO Cold rolled steel sheet HI N £ 3 03 ro 03 Ό - 03 03 ro £ 3 φ Ç 3 X OQ D £ .X CO Ό03 ‘Rô Experiment Example the CO and CN CO POO 3 LO CO POO 1 ^ CO 00 CO O) CD the 1 ^ £ CN 1 ^ CO 1 ^ s LO 1 ^ CO 1 ^ 1 ^1 ^ 00 1 ^ O> 1 ^ O00 s CN 00
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Example Example Example Example Example Example Example Example Example Example Example Example Example Example Example | Quality measurement results ofMaterial << O*·· 77 63 09 CO LO 76 00 55 74 99 72 36 85 74 I 09 EL O*" 25 o> 22 σ> CN 28 CN 22 o> 24 CN CD 23 24 | 20 | SI <00. 940 1184 1070 1139 O 923 1005 096 1027 CO 961 1261 937 1024 1208 |
c ZΦ Difference between Maximum value and Minimum value % in large scale 0.93 0.51 0.52 0.58 1.20 O 0.46 0.64O 1.05 0.48 0.53 0.99 1.63 the o«CO O COO) Φ The 'CO θ' mΕ Epasta CN LD LD h «- CO LD D) CD h «- LD LD H-00 POO CD hh «- o> 96 I O) Φ ω Φ8 EO O% in CN CN CN CN CNCN CN O• 8. »5 E £ *pasta LD CO LD O CD CN CN O LD D> hD> hCO O hD> 0000 00 CO CN CO 00 D> LD8 EO O% in co ‘ co ‘ co ‘ CN CN CN CN CN co ‘ CN co ‘ CN CN co ‘ CO
'andM— O*" LD CD CO CDLD CD COCO r-CO CD LD f (Maximum) O*" r- 00 22 00 03 00 r- 00 σ> CN σ> 00 20 00 r- *0.63 0.63 0.79 0.58 0.71 0.71 0.82 0.44 0.60 0.68 0.91 0.47 0.72 0.98 1 H98 / H23.57 4.37 4.82 CO 3.54 4.50 3.12 4.06 3.32 4.56 3.31 3.15 4.23 4.14 3.71 |
CO CD 00 O H- H- CO H- 00 H- CD 00 CD CD H- O 00 LD LD CD H- 03 CD03 CDO 03 00 COCD
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82/104
Example Example Example Example Example Example Example Example Quality measurement results ofMaterial << O*··09 69 00 62 £ 63 70 £ EL O*··23 00 20 20 23 20 23 22 SI <0 Q.606 1237 1042 1039 1003 1048 941 929 Segregation of Mn Difference between Maximum value and Minimum value % in large scale0.60 the ~ 0.37 1.82 1.07 ro ~ 0.86 0.82 Minimum concentration % in large scale1.90 2.24 CD r · 2.23 1.62 1.92 2.25 2.35 Maximum concentration % in large scale2.50 2.68 2.13 4.05 2.69 2.39 CO 3.17 Hardness measurement results f (Minimum) O*··CO LO r- CO CD CO LO CD f (Maximum) O*"20 o> CD σ> 00 CXI r- 20 *0.97 I 0.45 1.03 0.93 0.65 0.68 0.74 0.80 0.71 H98 / H2 3.26 3.75 3.92 3.65 4.13 3.61 3.60 3.58 86H > T479 458 506 442 487 499 515 462 H2 > T147 122 129 CXI 00 138 143 129 Experiment Example75 76 77 00 79 O00 £ 82
Petition 870180070295, of 8/13/2018, p. 85/120
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Example Example Example Example Example Example Example Example Example Example Example Example Example Example Example Example Example O % in large scale 0.0020 0.0037 0.0014 0.0023 0.0018 0.0031 0.0021 0.0016 0.0025 0.0023 0.0015 0.0019 0.0023 0.0019 0.0019 0.0022 0.0023 z % in large scale 0.0022 0.0025 0.0041 0.0054 0.0044 0.0007 0.0055 0.0045 0.0055 0.0030 0.0050 0.0016 0.0053 0.0010 0.0019 0.0053 0.0044 < % in large scale 0.054 0.012 0.050 0.015 0.114 0.023 0.341 0.050 0.031 0.056 0.045 1,054 0.012 0.025 0.021 0.050 1,719 <z> % in large scale 0.0022 0.0036 0.0033 0.0038 0.0021 0.0005 0.0035 0.0015 CD O O OO* 0.0039 0.0015 Oo o o * 0.0013 0.0032 0.0090 0.0049 0.0002 Q. % in large scale 0.028 0.015 0.003 0.018 0.014 0.014 0.006 0.023 0.014 0.009 0.015 0.009 0.010 0.013 0.021 0.011 0.004 Mn % in large scale 1.99 2.52 2.60 1.93 2.28 m 1.94 2.34 1.97 2.78 1.46 2.38 2.20 1.96 1.84 dog 2.58 <Z> % in large scale 0.78 1.26 1.06 m 0.99 0.75 0.57 1.39 CO 1.92 CO 0.36 0.84 1.60 r- 0.73 0.17 O % in large scale 0.112 0.193 h00 O * 0.144 0.205 0.235 0.310 h00O* 0.159 0.098 0.237 0.172 0.130 0.275 0.193 0.257 0.205 Experiment Example AA AB B.C αν AE AF AG AH <AK AL AM AN OV AP AQ
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O Q. E g LU OQ. E g LU OQ. E g LU OQ. E g LU OQ. E g LU OQ. E g LU OQ. E g LU Example Example OQ. E g LU OQ. E g LU OQ. E g LU OQ. E g LU OQ. E g LU OQ. E g LU OQ. E g LU OQ. E g LU Dí1— LU % in large scaleO) Z % in large scaleΦO % in large scale 0.0027 CO O % in large scale 0.0022 > % in large scalethe Z % in large scale 0.14 DO % in large scale 0.23 0.12z % in large scale 0.93 1.23O % in large scaleCXI CO o ~ m % in large scale 0.0041£> z % in large scale 0.028 i— % in large scale 0.031 0.053 0.009Experiment Example X mα LU LL <í JL I _1 <íZ JL 0.
Petition 870180070295, of 8/13/2018, p. 87/120
85/104
The Q E8 LU The Q E8 LU the Q E8 LU Comparative | The Q E8 LU the Q E8 LU the Q E8 LU The Q E8 LU o>8 And the O The Q E8 LU the Q E8 LU the Q E8 LU the Q E8 LU Comparative 1 The Q E8 LU the Q E8 LU the Q E8 LU the Q E8 LU the Q E8 LU the Q E8 LU ο Q E8 LU The Q E8 LU the Q E8 LU Cpmparativp | The Q E8 LU the Q E8 LU the Q E8 LU The Q E8 LU The Q E8 LU the Q. E8 LU Cold rolled sheet thickness AND IS rt · rt · rt · rt · CN CN CN CN CN CN CN CN O O OCN OCN CN CN CN CN CO CO CO CO Lamination reductiondogThe LO The LO the LO The LO CO CO CO CO The LO The LO The LO The LO CO CO The LO The LO CO CO CO CO the LO the LO LO LO the LD the LDOO O 1 ^ LO CO 1 ^ LO LO 1 ^ LO 1 ^ LO £ CN 00 1 ^ CO CN 00 CO CN LO OCN LO 00£ 00£ dog LO CN CO LO CN CNLO 1 ^ CN LO 1 ^LO £ LO £ LO 1 ^ 5LO LOLO 1 ^ O LO CN O LO LD CN LD CN LD Volume fraction ofAustenite ra 3 g ra55 AND £ IOC cni O00 00 LO 00 the 1 ^ CO00 CN 03 00 00 1 ^ 03 1 ^ £ CN 00 CN 03 O O CO 1 ^ O03 O00 -1 00 1 ^ 00 O O CN 03 CN 00 £ Cooling rate after winding 2nd CO CN rt · CO - CO O -CO 001 cni CO 03 LO - O CN CO 00 rt · O 00 O 00 - LD Left side of the equation _____ (D_____H- co3 CO03 l < CO θ ' CN LO 3 O 5 CO aãO CN The s 03 CO CNLO CN 1 ^ 03 1 ^ θ ' 03CD CN C0 O03 CNThe CN CO CNLO CN CD CN 00CO Coiling temperatures OO 1 ^ CN CO 3CO 3 CO 1 ^ CO CD CO CO CO POO 00 CN CO 3CO LOCO LOCD 5CO The CN CO 00£ CO 1 ^ CO 4 CO £ the CN CO 4 CO 1 ^ CO CO CO LO CO rt £ the coconut 00 CO CO s CO OCO Cooling rate after lamination The ΌC 3 σ ra CO Õ o CO CN POO CO POO CO CN 1 ^ CO POO 1 ^ CN LO CO 03 CN POO dog 1 ^ CO 00 1 ^ CN 03 CO £ LO CO CN CO CO 1 ^ CO 03 00 CN 03 CN 00 £ Finish laminating temperature OO 3 dog σ> CN 03 CO O03 CN 00 00 O3 0300 CO0300 1 ^ CN 03 CO3 CO0000 CO 1 ^ 00 rt £ CO o 03 CN 03 00 £03 1 ^ £ O o 03 LO CN 03 OCN03 O0300 CO CN 03 OCN03 1 ^ CO 03 03£ 00 O) 00 Air Transformation Point ₃ OO 1 ^ o 1 ^ the 1 ^ 1 ^ o 1 ^ 1 ^ o 1 ^ 003 003 003 003 03 CO CO 03 CO CO 03 CO CO 03 CO CO CO 1 ^ CO 1 ^ 1 ^ LO CO 1 ^ LO CO 0000CO 0000CO 0000CO 0000CO POO POO £ CO CO LD CN 1 ^ LD CN 1 ^ Plate heating temperature OO LOCN the LO CN LO THE CN OCN LO CN CN LO 00 CO CN LO 00 O00 THE LO CN OCN LO THE CN LO THE CN LO 03 LO CO CN LO CO CN the LO CN LOCN LO 00 LO THE CN LO CO CN LOCN the LO CN the LD CN LD CN CN LD CO CN Chemical constituent 22 2 m< m< m< m< the < the < the < the < Q < Q < LU < LU < LL< LL< LL< LL< the < the < < T< < < Experiment Example 03 O £ 3 o υ υ Ό υ ra υ * 5 O) υ .c υ O 'ç υ O And υ c υ The υ Q υ σ υ O C0 υ O D υ δ 8 δ δ ' 8
Petition 870180070295, of 8/13/2018, p. 88/120
86/104
The Q. E 8 LU The Q E8 LU The Q. E8 LU the Q E8 LU The Q. E8 LU The Q E8 LU The Q. E8 LU The Q E8 LU The Q. E8 LU the Q E8 LU the Q. E8 LU The Q E8 LU the Q. E8 LU The Q E8 LU The Q. E8 LU The Q E8 LU The Q. E8 LU the Q E8 LU The Q. E8 LU Cold rolled sheet thickness AND IS CO CN CN CO CN CN CN CN CN CN CN CN CN CN CN CO CO CO CO Lamination reductiondogPOO The LO The LO 00 co The LO The LO CO CO CO The LO The LO The LO CO CO CO the LO the LO the LO the LO CO OO CO LO The LO CO CN LO co E 00 the co CO o co the LO LO LO3 o>3 CO00 O o O LO3 1 ^ LO LO CN LO LO 1 ^ CN LO CO LO CO CN CO COAND Volume fraction of Austenite 1 g O o O>00 O co00 LO 00 σ> 1 ^ 5 O00 0000 O00 co00 1 ^ 00 co00 O o CN O CO00 The σ> LO 1 ^ 1 ^ CO Cooling rate after winding 2nd CN00 LO σ> LO Oσ> O co σ> O O σ> Left side of equation ° (1) __ COCN The CD σ> o 5 poo 1 ^ 00 CO co00 1 ^ co CD co σ> CN 00 CN O o> CN 00 S oo LO LO CD σ> CD CN CO co Winding temperature OO CN3 CO LO CO 00AND LO the co 1 ^ co co the CN CO O> 1 ^ CO COThe 1 ^ 1 ^1 ^ co The 1 ^ co LO E CN 1 ^ co Poo co 1 ^ LO00CO OPoo 003 LO CO CO the co Cooling rate after inhaled Iamdog The ΌC 3O) CD CO 3 CO CN CO co LO AND LO O O CN σ> CN LO CO poo LO CN CN CO CN CN CO poo LO CN poo Finishing Inaction Temperature OO 00 O) 00 CO CO σ> σ> σ> O5 o σ> 00 CN CN o 1 ^ σ> 00 coσ> σ>5 LO0000 5 CN o CO0000 00 CN o LO CO O CN o 00 CN O σ> AND 1 ^ CN O) Transformation PointAr3 OO CN COCO CN COCO 5 co 5 co CN CO 1 ^ CN CO 00 co 00 co 00 co 00 co 00 co 00 co 00 or 1 ^ 00 or 1 ^ 00The 1 ^ σ> LO CO σ> LO CO σ> σ> LO σ> σ> ΙΟ Plate heating temperature OO s o the CN OCN LOCN LO CN CN LOCN LO the CN the CN co LOCN LOCN o the CN OCN LOCN the LO CN the CN co OCN CN LOCN OCN CN co CN Chemical constituent 3 3 < < _l< _l< < < < z< z< z< 5 5 5 0.< 0.< % % Experiment Example 03Ό £ 3 D o Ό Ό Ό CD Ό M— Ό 03 D £ D -X ΌANDΌ c Ό o Ό Q Ό σ Ό Ό co Ό
Petition 870180070295, of 8/13/2018, p. 89/120
87/104
The Q E8 LU The Q E8 LU the Q E8 LU o>§ And the O The Q E8 LU o>203 Q E o O the Q E8 LU the Q E8 LU the Q E8 LU Comparative | The Q E8 LU Comparative | The Q E8 LU the Q E8 LU The Q E8 LU Comparative | The Q E8 LU O>203 Q E o O the Q E8 LU the Q E8 LU the Q E8 LU ο Q E8 LU ο Q E8 LU ο Q Ε8 LU ο Q Ε8 LU ο> 1 8 Ε ο Ο Ο Q Ε8 LU Cpmparativp | Ο Q Ε8 LU ο Q Ε8 LU ο Q Ε8 LU Ο Q Ε8 LU ο Q Ε8 LU ο ο. Ε8 LU I Second Cooling Process 1 ώ φ e ό © ω co tj s D O i ra '& S fe <o c 8..Ç ® E E E, 2 j | OO LO O> 31 LO1 00 LO 1CN CO1 LO CO CO 1 CO CN1 CO LO1 LO CO1 00 CO1 31 CO CN 1 ^1 CO CO 1 POO1 LO CO CNI Ο CO1 LD COI Υ δ1 σ> 1 ^ P S s g §= E g '&. ® hi co £ li 2 "s -8 OO LO LO CO CN CO CO CO00 CN LO00CO δ CN o> the CN CO CO CN CO 1 ^ CN δ CO THE COCONUT 1 ^ CO CN 5CO the s 1 ^ CO CO LO CN CO CN 3 CN CN 00CN CN Ο 00 ο CO 3CN 1 ^1 ^ CN σ>00 CN CN Ο 00 Ο ο 00 osc _m . £ φ P co E = m <5 ro ω f EO 'CO E O ®, Φ β TJ 1— C (0 φ E = 5 Ό £ F 8 c ~ CO, with E ω 1— φ tj The ΌÇ3 σ Φ CO O o CO CO O> 1 ^ 1 ^ LO O> CO LO O> LO The LO 3 δ CO o> LO CN LO 1 ^ CO 1 ^ CO POO CO LO 00 CN 00 LO 00 LO 00 CO Ο LD CN 00 LD CO 00 LD CN LD I First cooling process | φ φ TJ TJ9 o £ ico, ço o ** “CO E Ê Φ ο * ω iCO E O-g φ 1— ®E E φ B TJ as aas Ε ΕΈ Φ Φ Φ 1- 1- LL The ΌÇ3O) Φ CO 1 ^ CN δ POO CO 3 CN O 1 ^ CO LO CO CO CN 1 ^ CN 00 O CO O 1 ^ CO LO o> 1 ^ O> 1 ^ Ο00 δ 3 00 LD 5 LD 00 00 Ο CN LD 1 ^ δ Maximum heating temperature (T1) OO CO00 1 ^ CO σ> 1 ^ 00 1 ^ LO O 1 ^ CO δ The σ> CO CN 00 CN 00 1 ^ 00 1 ^ 1 ^ O00 LO00 δ00 CO 1 ^ 1 ^ 3 1 ^ 300 the o 00 1 ^ CN 00 00 1 ^ 1 ^ ο ο 00 00 LO 00 s1 ^ σ> δ 300 Ο ο 00 00δ 1 ^1 ^ 00 Steel type 0 0 o 0 0 o 0 o 0 o 0 0 0 0 0 o 0 o 0 o 0 0 0 0 0Í ο 0Í ο 0ί ο 0Í ο 0ί ο 0Í ο 0Í ο 0Í ο 0Í ο Chemical constituent 22 2 m< m< m< m< the < the < the < the < Q < Q < LU < LU < LL< LL< LL< LL< <: <: < τ< < < Cold rolled steel sheetcold 03 O £ 3 o hi ol Ό υ φ υ T5 81 .c υ O ‘0 81 O And υ c υ The υ Q υ σ υ ι_ υ ω υ SI 3 υ δ 8 δ δ δ Experiment Example CO00 s LO 00 CO00 00 0000 O>00 o σ> δ CN O CO σ> 3 LO σ> CO σ> σ> 00 σ> σ> σ> ο ο δ CN Ο CO ο ο LD Ο CO ο 1 ^ ο 00 ο
Petition 870180070295, of 8/13/2018, p. 90/120
88/104
The Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU o> g § E o O The Q E8 LU the Q E8 LU The Q E8 LU Comoarativo | The Q E8 LU The Q E8 LU The Q E8 LU Comparative | The Q E8 LU The Q E8 LU The Q E8 LU The Q. E8 LU The 1 ^1 CO CO CN1 CN1 LO CO 1 CO 1 ^1 O> CO 1 1 ^ O> CO 1 CO LO1 00 ^ 1 1 ^ CO1 LO COI σ> 1 AND1 1 ^ CN1 The LO1 31 O> 1 ^ CN o o CO o> CN CN CN THE CN OCO 00 CN CO 00 1 ^ CN o> σ> CN COCO dog CN 3CN OI col LOs s Hi 00 col 1 ^ LO CN CO LO CN 1 ^1 ^ CN OCN CO CN the CO 00 POO LO 1 ^ dog CO o CN CO 1 ^ CO 1 ^ LO O> CO CN 1 ^ LO CO 00 CN POO 3 POO CO LO O>CO σ> LO 3 1 ^ o LO O 5 o> CN CO00 1 ^ 1 ^ CO the CO LO CO CO CN POO the CO CO CO00 LO 3CN CN LO CO CO00 1 ^ CN CO 1 ^ σ> LO O o o> CO 00 CO00 1 ^ O00 CNl LO o rt £ CO σ> COI O h-l O O 00 LO LO 00 the CO 00 CO o 00 CN 00 LO 00 1 ^ AND00 Hi o 0 0 0 o 0 0 0 0 0 0 0 o 0 o 0 I'm the 0 0 0 0 0 3< < _l< _l< < < < z< z< z< 5 5 5 CL < CL < % % 03Ό £ 3 D The Ό Ό Ό Φ Ό M— Ό HI D £ D DANDΌ c Ό o Ό Q Ό σ Ό Ό CO Ό O> O O T- CN CO rt · LO CO 1 ^ 00 O> the CN CN CN CN CO CN CN LO CN CO CN 1 ^ CN
The Q E8 LU The Q E8 LU The Q E8 LU Comparative | The Q E8 LU Comparative | The Q E8 LU the Q. E8 LU I Reheat process I Total maintenance time in Transformation Temperature rangefrom Bainita | opunSes 1 ^ CO 00 O LO 1 ^ Reheat stop temperature - Bs OO -35 | -56 | ζε- -40 -30 | 00 CN Reheat stop temperature (T3) OO 544 | AND 537 532 425 | 00 1 ^ Average rate of temperature increase in Bainite transformation temperature range ° C / sequence I 1 25 I CN and and LO CN 1 ss I Maintenance process I Maintenance time in Martensite Transformation Temperature range | opunSes CO 33 | LO -1 CO 00 CN Experiment Example 1 83 | 1 84 | 85 86 1 ^ 00 0000
Petition 870180070295, of 8/13/2018, p. 91/120
89/104
The Q E8 LU Comparative | The Q E8 LU o>§ And the O The Q E8 LU the Q E8 LU The Q E8 LU o>§ And the O The Q E8 LU Comparative | The Q E8 LU The Q E8 LU The Q E8 LU the Q E8 LU The Q E8 LU The Q E8 LU the Q E8 LU o> g § E o O The Q E8 LU Comparative | The Q E8 LU the Q E8 LU The Q E8 LU The Q E8 LU the Q E8 LU the Q E8 LU the Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU the Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU o> g § E o O The Q E8 LU The Q E8 LU The Q E8 LU Cpmparativp | CN1 ^ O 1 ^ 51 O O CN CN CO CO 1 ^ CN 00 O 1 ^ O 00 1 ^ 1 ^ 00 O CO The CN LO 00 CD O O O O1 Hi CN1 CDCN 1 O CO CN1 s1 1 ^ CN1 00 O THE LO 1 1 LO1 CN1 00 LO 1 1 ^1 CN 1 ^1 CN CN LO1 1 CD 1 ^ CD1 O 1 ^ CD1 CN CO1 CN1 The 001 00 O 00 00 CO1 00 CO o CO4 O |3l CO o 00 CN LO The LO 1 ^ CD CO o CN 00 The LO AND CO LO AND 5 CO o 1 ^ LO The 1 ^ 0000 005 O O LO CD CN LO 00 1 ^ CO CN4 O5 CD 1 ^ CO 1 ^ LO O O LO O3 CN 00 CN 1 ^ LO 1 ^ CO 00 o AND the CN LO CO CN 1 ^ CO C0 | The CN CN CO 00 CD CN CO CN 00 CN LO CN 1 ^ 1 ^1 ^ LO CN LO CO 1 ^ CO CD CO O AND The CN CN 00 The LO CO The CN CN CO AND O CN LO CN CD CO CN CN CN CD CN The CN CO CD 1 ^ CN - And cn | CD CN CO CN The CN CO CN 00 CN LO CN CN CN The CN CNCD CN O CD 1 ^ CO HI O00 the o 5> CN O CO O O LO O CD O 1 ^ o 00 O O O the o O CN O CO o 3 LO O CD O 1 ^ o 00 O O O O T- CN COLO CD 1 ^ 00 O the CN
Petition 870180070295, of 8/13/2018, p. 92/120
90/104
The Q E8 LU The Q E8 LU The Q E8 LU Comparative | The Q E8 LU the Q E8 LU the Q E8 LU the Q. E8 LU H- CO O)COLD O)COH- 00 00O Cri1 Cri1CO1H-1 LD1 O O 00H- LD laughs ^- CO O CXJ H-00 CO 3 CO LD LD laughs ^- laughs ^- laughs ^- LD laugh CO OCO OOlaughs ^- COCri CO laugh Cri CO CN 00 HI dog CO Cri Cri o>CXJ COlaughs ^- LD CO H- Cri Cri C JCri Cri Cri Cri
ο Q Ε g LU Example I Example I ComDarativo | ComDa-1 example rative | O Q E g LU O Q E g LU o Q E g LU ComDarativo | O Q E g LU ComDarativo | O Q E g LU o Q E g LU O Q E g LU ComDarativo | O Q E g LU ComDarativo | O Q E g LU O Q E g LU Example | Starting temperature of Martens Transformationsita (Ms) OO O ri- 381 I 390 390 289 | 253 I 295 318 384 | 383 I 323 379 348 I 361 I 296 | Bainite transformation start temperature(Bs) OO 579 | 567 | 574 572 455 | 450 I 467 478 519 | 518 I 482 517 520 I 530 I 494 | Fourth cooling process Average cooling rate ° C / second CO Hi • laughs - Hi 00 CXI • laughs r- LD CO CD CD • laughs - Third cooling process Maintenance time in Bainite Transformation O o cD σΦ ω 135 | 149 | 236 130 461 | 524 | • laugh 590 403 | 65 I 577 558 193 I 232 | | 130 | Experiment Example | 83 | laughs CO 85 86 H-00 0000 89 90 Hi 192 | 93 94 195 | 196 | | 97 |
Petition 870180070295, of 8/13/2018, p. 93/120
91/104
O Q E g LU o Q E g LU o Q E g LU o Q E g LU g2 § E O O o Q E g LU g2 § E O O o Q E g LU O Q E g LU O Q E g LU o Q E g LU o Q E g LU O Q E g LU o Q E g LU O Q E g LU o Q E g LU O Q E g LU o Q E g LU o Q E g LU o Q E g LU O Q E g LU o Q E g LU g2 § E O O o Q E g LU o Q E g LU o Q E g LU g2 § E O O o Q E g LU o Q E g LU O Q E g LU g2 § E O O o Q E g LU O Q E g LU O Q E g LU Example | 302 | 327 | 280 | 293 328 160 I 299 | 00dog 290 | 351 I 347 | 349 | 346 | 275 | 313 I 364 | 363 | 351 | 338 I 390 270 | 287 | -144 352 | 356 | 287 288 I 280 I 336 | 303 | 501 I 545 I 519 | 515 551 474 | 542 | 486 | 470 | 523 I 520 I 445 | 442 | 486 | 508 I 597 | 598 | 522 | 531 I 554 475 | 490 | 278 547 | 548 | 506 517 | 506 I 615 | | 584 | CXILO CO CXI CO o> CO o> -00 r- CO CO CO 00 CXI r- - 00 O 1 o> CO CO CO - LO o> 218 I 173 I 295 | 156 146 218 I 275 | the LO463 I 00 | 909 535 | 233 | 264 | LO 241 | 236 | CXI 163 136 | 152 | 163 164 | LO 244 399 I 382 | 276 | | 205 | COO o O 102 I 103 I | 104 | I 105 I I 106 I I 107 | 00 o | 109 | OCXI COLO CO r- 00 o> 120 CXI I 122 | 123 I 124 | I 125 I I 126 | I 127 |
Petition 870180070295, of 8/13/2018, p. 94/120
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CO CN ro φ
X3 CO
o Q E g LU O Q E g LU O Q E g LU g E § E O O o Q E g LU g E § E O O o Q E g LU O Q E g LU o Q E g LU g E § E O O o Q E g LU g E § E O O o Q E g LU o Q E g LU O Q E g LU g E § E O O o Q E g LU g E § E O O o Q E g LU O Q E g LU O Q E g LU O Q E g LU O Q E g LU O Q E g LU o Q E g LU g E § E O O o Q E g LU g E § E O O o Q E g LU O Q E g LU Example E * 5L_ 'tfíΦ2nd E φ othe sCO £ Φ CO n oΦ oCO o o5CO í Dí Medium crystal grain AND3 LO CO 5.5 | ω LO 4.9 | CO ω 3.4 4.2 | LO l < rLO ~ 4.2 | 4.0 | l < CN 3.7 | 8.0 | 5.3 CO 6.0 I tr 'tr 6.3 | Φ E DO>Φ oo ICÜ o> s LL Others O*" CN O O O - - O - CO - - O CN - O O O - 33 O O - O > CO pÍ Dí O*" CO CN Or- CO CO LO '' t O - O O CO LO O '' t - O CN '' t r- CO s O*" O O - O CO O co | CO CN O O CO CN O O O CO O O - O CN - s1- O*" 40 | 27 | 56 '' tl 30 | 03 03 34 00 CN δ LO 33 CN CO 34 | 1 οε 40 | 23 | POO 27 r- CO 20 | I £ fr B + BF | O*" £ 1 * 40 | 20 99 CO CN CN CO CN CO 36 trtr 1 LO 37 POO 40 | 27 | 28 | trtr CO O 69 LO CN trtr CO CN LL m O*" CNCN SI CO 00 LO 00 δ CO 00 CN O CO O CN 00 03 HI 36 LO CN POO CN m O*" 03 CO CN 00 32 O 24 | 27 28 CO 37 | r- 35 POO 27 | r- 26 | 36 | '' t HI 33 O - - LL O*" CN δ 23 26 POO LO '' t 33 CN 03 LO CN 89 27 δ CN CN 00 CO CN CO 26 | 42 | 40 CN 00 '' t CO | 27 | Steel type CR | Say O CR CR Say O Say O CR CR Say O Say O CR CR Say O Say O Say O CR | CR | Say O CR CR Say O Say O Say O Chemical constituent AA | $ AA AA m < m < AB AB AC | 1 ov B.C B.C Q < 1 αν LU < LU < LL < LL < AF AF AG | AG | < Cold rolled steel sheet CO o £> O O o the o Φ o You ü) o .ç. O Ό 6th ¹ O O It's the IT'S THE g Q O g L_O CO o O OF δ g Experiment Example 83 I CO 85 86 l 00 0000 89 90 δ CN 03 93 94 LO03 96 | 97 1 98 I 0303 the o δ 102 103 | 104 | 105 |
Petition 870180070295, of 8/13/2018, p. 95/120
93/104
O Q E g LU o Q E g LU O Q E g LU o Q E g LU O Q E g LU O Q E g LU o Q E g LU o Q E g LU o Q E g LU o Q E g LU O Q E g LU 1 CO Q E o Oo Q E g LU rative | O Q E g LU O Q E g LU 1 CO Q E o Oo Q E g LU rative I O Q E g LU o Q E g LU 1 CO Q E o Oo Q E g LU rative | O Q E g LU O Q E g LU O Q E g LU Example | 6.5 I 4.7 | 6.7 | 5.6 | 6.4 | 7.0 I 7.5 I 5.4 | 4.8 | 6.7 | 7.5 I co ~ 5.5 | 3.2 | 16.9 6.7 | 4.4 | 00Hi 4.4 | 6.8 I 5.9 | CDCXIOO OO OCXI CO O CXI O O r- CO CDlaughLD CXI 00 O LD laugh CXI O CO 00 Hi LD HiO O O O O O CO OO O laugh O O CO CO O COO Odog Hi CXI POO H- dog Hi 00 30 | 24 | 38 | r- 45 hCO CO laughs HI Hi CXI hCO CXII Hi LD POO CO CXI 20 | 43 | 36 | Hi CXI 38 | 33 | 43 | CXI laughs laugh Hi 35 | 44 30 | 38 | O trtr CXI laughs 43 CXI laughs laughs ^- 35 | CXI CO Hi LD CXI r- CXI 23 | laugh O POO O 28 | 00 O CO HI trtr POO CD 30 | 36 | 00 CD r- 34 | - CXI CXI r- O CXI CXI laughs 00 Hi r- 26 30 | 35 | HI O Hi 27 CXI LD 27 | LD laugh CXI CXI CO CXI CO CXI CD CXI 37 | CXI LD CXI CD CXI CO laughs CXI laughs Ή 00 CXI 00 "I LD CXI 45 00 CXI CXI CO CXI CO 45 | CR | CR | Say O Say O Say O CR | CR | Say O Say O Say O CR | CR Say O Say O CR Say O Say O CR CR | CR | Say O Say O AH | < < AK | AK | _1< _l< < < AM z< z< AN AO | I ov TO 0. < 0. < %δ δ · B gives £ 3 Ό O o the o in M— o O .ç. Ό TJO TJ It's the c o of Q o σ o ιό CO o 1 106 I I 107 | CO o | 109 | OCXI CO laugh LD CD r- 00 Hi 120 CXI I 122 | 123 I 124 | I 125 I I 126 | I 127 |
Petition 870180070295, of 8/13/2018, p. 96/120
94/105
The Q E8 LU the Q E8 LU the Q E8 LU s § E O O the Q E8 LU s § EThe ol the Q E8 LU The Q E8 LU The Q E8 LU s § E O O the Q E8 LU s § E O O the Q E8 LU the Q E8 LU The Q E8 LU s § E O O the Q E8 LU s § E O O the Q E8 LU The Q E8 LU OQAND8LU The Q E8 LU The Q E8 LU Example | Material quality measurement results << θ ' l · CD AND CO CXI r- LD CO 00 CXI CXI 00 CXI LD CD CD CD LD LD CXI LD CD l·LD CO CD CXI LD l · - l · CO EL θ ' CO CXI CO CXI - CD CO LD CO 00 CXI CXI CD CXI CXI CXI CXI CD CXI CXI CXI CXI LD CXI CD SI MPa 952 | O00 o 1144 944 1527 | 1349 | 1427 1260 1090 | 1085 | 917 1027 1066 | 1091 | 1129 | 1403 | 1124 | 1376 | Segregation of Mn Difference between Maximum value and Minimum value %in large scale 0.89 | 1.03 | 0.21 0.63 1.02 | 0.88 | 0.27 - 1.36 | CM 0.23 0.84 0.92 | 1.49 I 1.68 | - 0.54 | 0.77 | Concentrationminimum %in large scale 1.53 | 1.46 | 1.89 l · - 2.16 | 2.12 | 2.44 2.04 1.88 | 1.95 I 2.51 2.25 1.60 I 00 1.59 I 1.94 I 1.49 I | 1.43 | Maximum concentration %in large scale CXI cxT 2.49 | 2.10 2.40 3.18 | 3.00 | 2.71 3.15 3.24 | 3.16 | 2.74 3.09 2.52 | 2.97 | 3.27 | 3.05 | 2.03 | | 2.20 | Hardness measurement results f(Minimum) θ ' r- CO - HI LDCO Hello r- CO Hello O LDLD 00r- f(Maximum) θ ' 00 CXI POO 00 CXI CD O CO CXI r- r- CXI LD CO O 00 O CO CXI 00 the CXI 00 *-0.89 | -0.60 | -0.05 -0.21 -0.57 | -0.44 | -0.34 -0.30 -0.91 | -0.78 | 0.13 -0.26 -0.56 | -0.64 | -0.58 | -0.68 | -0.72 | | -0.46 | H98 / H24.23 | I 1-S'fr 4.50 4.39 3.91 | 3.58 | 4.81 4.34 4.82 | 2.74 | 3.55 4.79 5.15 | 5.20 | 5.25 | 3.76 | 4.94 | | 3.94 | 96H Hv COAND 541 | 524 542 534 | The LD 602 566 584 | 372 | 430 581 O00 CD 721 | 646 | 00 COAND 00 CO H2 Hv CXI 120 | r- 123 137 | 00 CXI 125 AND CXI CD CO CXI CXI 132 | CO 123 | D) CXI 124 |Experiment Example CO00 00 ld00 CD00 l 00 0000 00 the o O CXI O CO o O LD O CD O l · O 00 D) D) D) the o
Petition 870180070295, of 8/13/2018, p. 97/120
95/104
The Q E8 LU o>E co Q E o O the Q E8 LU O>E co Q E o O OQAND8 LU The Q E8 LU The Q E8 LU The Q E8 LU OQAND8 LU OQAND8 LU the Q E8 LU The Q E8 LU the Q E8 LU OQAND8 LU OQAND8 LU the Q E8 LU the Q E8 LU The Q E8 LU The Q E8 LU o>E co Q E o O the Q E8 LU the Q E8 LU ExampleComparative OQAND8LU OQAND8LU The Q E8 LU O>E co Q E o O Example | Material quality measurement results << O*·· r- CXI | cxilCXI 00 LO 00 rr- 00 LO CDLO00 CO Hi LO LO LO LO LO CD CXI 00 Hi CDCXI LO δ LO CD EL O*·· 00 HI 00 LO The CXI 00 CXI the CXI 00 CD CXI CXI CXI LO 00 Hi CXI CXI The CXI - 0000 O LO 00 00MPa 1228 1306 1398 | 1532 | oõ o 1135 | 1098 | 1404 | dog 1250 | 1332 | 1450 | 1280 | 1237 | 1194 | O 1056 1319 | 1455 | 733 00 δ 1005 1129 | Segregation of Mn Difference between Maximum value and Minimum value %in large scale 0.86 0.18 00 CO 1.02 | 1.22 | CXI CXI 0.93 | 1.29 I - 0.67 | 0.56 | 1.70 | 0.77 | LO 1.23 | O O 0.87 | 0.85 1.20 | 1.29 I 1.03 | 0.67 I Minimum concentration %in large scale LO 1.68 δ 1.56 | 1.76 | 1.93 |1.60 | 2.36 | 2.38 | 1.23 | LO 1.80 | 2.15 | 1.69 I LO CD 1.43 |1.65 1.39 I CXI 1.33 - Maximum concentration %in large scale 2.37 1.86 2.69 | 2.58 | 2.98 | 3.05 | 2.83 | 2.53 | 3.65 | OCO 1.90 |3.50 | 2.92 | 2.84 | 2.74 | 2.86 2.44 | 2.58 | 2.50 2.59 | 2.50 | 2.36 00 Hardness measurement results f(Minimum) O*·· HI -r- LO CXI r- CD r- CD CXI 00r- LO00 00 CD HI CXI 00 HI 00 f(Maximum) O*" rCXI O00 00CXI 00 CD CXI CXI 00 The CXI 00 Hi CXI CXI r- r- CXI CXI 00 00 CXI the CXI CXI CXI 00 00 CXI 00 hi CXI Hi *O'1-0.29 I-0.44 | -0.57 | -0.65 | -0.58 | -0.86 | -0.79 | -0.63 | -0.95 | -0.45 | -0.66 | -0.59 | -0.84 | -0.45 | -0.50 | -0.32 I-0.61 | O1 0.21 -0.46 | -0.58 | -0.24 I| -0.62 I H98 / H24.06 4.21 4.40 | 00C3 3.82 | 5.00 |5.17 | 3.74 | 5.04 | LO 3.77 | 4.37 | 4.59 | 5.19 | 3.66 | 1.38 4.68 | 3.61 | r- 4.03 | 3.66 |3.74 | 86H Hv 456 510 476 | LO CO 00LO LO LO CD | 699 725 | 572 | 00 r- s CD 491 | 465 | LOLO 624 | 422 | 419 00CD δ 615 507 | 459 | 522 00 o H2 Hv CXI CXI 00 oCD00 dog 139 | 140 | 00 LO 00 LO Hi CXI 130 | 106 | CXI 120 | LO 304 0000 CD00 129 126 | 125 | 127 109 | Experiment Example O 102 I 103 | | 104 | I 105 | I 106 | I 107 | 00 o | 109 | O - CXI 00LO CD r- 00 Hi 120 CXI I 122 | 123 I 124 |
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O O O Q Q Q. F F F Φ Φ Φ X X X LU LU LUCD CD ld00 00 CD O CXI O 00CO H"- LD 00 CXI 00 CD CD CD T— LD OO CXI 00 H"- T— t— CXICXI CXI 00 O> 00 H"- CXI 0000 CXI r- CD - r- 00 CXI CXI H"- O> H"- LDO1 O1 O1 LD O CXI O> CXI LD CXI LD H"- LD H"-LD 00 LD CXI O> LD THE 00 O> LD CD H"- CXI CXI CXI
The Q E 8 LU the Q E8 LU The Q E8 LU The Q E8 LU The Q E8 LU The Q. E8 LU The Q. E8 LU Cold rolled steel sheet thickness AND IS 13.0 I 13.0 I 13.0 I 12.3 I 12.3 I CJ CJ Lamination reductionO O O O O O OOO CD 1 ^ LD 1 ^ LD CN 1 ^ LD CN 00 CO00 00 LOT CN LD Volume fraction of Austenite | % by volume | dog CO00 0000 LD 00 CD00 I LLI CD00 Cooling rate after winding I ° C / hour I LD CN CO COCO LD Left side of the equation (1)122.6 | 1 Z '6t | The CN I 18.9 | I 15.9 | O) l < 128.2 | Winding temperature OO CN3 | 635 | 00 CN CD 1626 | 00 s 1623 I CD3 Cooling rate after lamination I ° C / sequndo | LD CO 1 oe | dog O) CN CD CO O) CN dog Finish laminating temperature OO | 903 | | 918 | 1 ^ O) 00 LDS) 1 ^ O O) CD CN O) 1890 | Ar3 transformation point 9 1 ^ o 1 ^ 1 ^ o 1 ^ 1 ^ O 1 ^ 1648 I | 648 | I 6991 I 6991 Heating temperature ofboard OO | 1205 | o the CN I 1220 I OCN | 1215 | CO CN | 1235 | Chemical constituent 2 2 2 m< m< <: <: Experiment ExampleD Ό > Ό 3Ό X Ό > Ό N Ό
The Q E8 LU The Q. E8 LU The Q E8 LU the Q. E8 LU the Q E8 LU the Q. E8 LU The Q. E8 LU Reheat process CO -1 (0 C0 C0 E -· o · * - s o coS Φ E c ΦΦ 2, Ο Φ Φ icoΗ C Η ΌΌ o Όç3O) Φ ω LD 1 ^ CD CD 1 ^ LD 1 ^ The ffl ω CL -D φ 3 with EE -o § φ É φ E 2. σ _m φ φ OO O O)1 LD CD1 CD O)1 CN The CN CN1 s1 The ffl ® c L -D φ 3 co E E -o § φ 2 Φ o. ro d E Q. CT <- »IsSE OO the co 00 O) 00 1 ^ δ LD CO O) OF) D) 1 ^ ® «oco φ P φ P ‘8. = 5 · ° = ό = 2 co c 5 2 S 2 = Έ lirhíã5 φ Ε φ E Ã 1— ro o b tj The ΌC 3O) Φ CO O) LD CO 1 ^ co LD O O LD CN Maintenance process gp _ ffl® Ê φ Ε φ φ ® ω tj <5 c φ E Ê £ g. go = S ra E §5 SE g Ξ, φ d -s ω íç ω | - C «52 ⁿ 1 r 7 The ΌÇ3O) Φ ω 1 ^ 00 OOLD Second Cooling Process E = co ω ¹ OO O) O) CN1 the CD1 CD 1 ^1 D) CO1 00 CN1 δ1 23 co ω ra c φ o OO THE COCONUT Poo CN CO co O)CN O00 CN 5 co The CN CO «Only co -9 φ g '8. S φ · ° 3 E. <5 1 E 8 E gz ^c co -s Φ «2 dogs PE Ê Ê êi £ 3 The ΌC 3O) Φ CO 00 LD LD LD 5 CN LD 00 CN CD the LD First cooling process É Ε É φ j φ EsSEc ^ φ d -s φ íç φ | - C «52 ⁿ 1 r 7 The ΌÇ3O) Φ ω CN CO CN LD 00 co O) LD CO LD CD Maximum heating temperature (T1) OO 00 co 00 CO00 1 ^ co 00 CO 1 ^ 00 CO CD 00 O00 CN CN 00 Steel type 0ÍT 0ÍT <o1 0 T 0ÍT <o1 0 T 0ÍT O1 Hi T Chemical constituent 2 2m< m< <: <: Hot rolled steel sheetD Ό > Ό 3Ό X Ό > Ό N Ό Experiment Example 00 CN O) CN CO δ CN CO POO 5
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ο ο Ε8 LU Ο Q Ε8 LU Ο Ο Ε8 LU ο Q Ε8 LU ο ο. Ε8 LU ο Q Ε8 LU ο ο. Ε8 LU Connection conditions O 'O Φ o Ό C O ® Q. 3 P c h The ΌC D σ Φ ω I I ΙΟ CN I CN I 1 ΦD2 ~2 - 0. o 0.103 with Çr Cü ® .5 * οο 1 1 ΙΟ Ο ΙΟ 1 00 σ> 1 1 Leaf bath position 1 1 Ο CΦ Ε ’ΝΟ ο2C0 »οο < 1 I φ 3 σ 03 2φ ΌΟ828 φ2 Ε 0. Õ 1 ο C φ Ε ’νο υ2C0 »οο.< Start temperature of Martensite Transformation (Ms) οο 000000 CN 1 ^ 00 CN σ> 00 ΙΟ CN 00 σ> Ε CN 1 ^ 00 Ε00 Bainite Transformation start rate (Bs) οο ο 1 ^ ΙΟ 00 CO ΙΟ S ΙΟ 1 ^1 ^ 00 Ε ο Ε Fourth cooling process o li ^c CO g 2, co φ 1- O Ο ΌC D σ ΦC0 Ο ο CNΟο 00Third cooling process E to Φ c o g ra 2 2 ³ B 2 ra ^E 'ra <D § S o ® o CL „<0 ESE Φ ~ J = u 03 O Γ“ Μ— M— Ο ΌC D σ φ ω CN 00 Ο0000 Ο ΙΟ 00 CN ΙΟ CN 00 000000 0000 Experiment Example 00 CN σ> CN Ο00 Ε CN 00 0000 3
o Q E g LU o Q E g LU O Q E g LU O Q E g LU o Q E g LU o Q E g LU Example | Microstructure observation results Medium crystal grain E λ 1 S 'z | B-00 * 1 fr '9 1 1 6.3 | 1 z 's | 1 6.3 | 1 z 's | Volume fraction I Others | O*" O O O O O - - Retained γ | O*" CO LO CXI LO CO O O*" - O O O CXI - O 1- O*" σ> CXI CD CXI CO POO LO CXI CO CXI | B + BF | O*" 1 Otr 1CD CO 1 ζε | 1 et | 1 ot | 00 CO LL CO O*" LO 00 CXI O CXI CXI CD CXI CO m O*" LO CXI CO CD CO LO bCO 00 CXI LO CXI LL O*" bCXI 00 CO The CXI LO 03 POO CO Steel type 1 «h 1 l ι | HR-GA | 1 «h 1 | HR-GA | 1 «h 1 | HR-GI | Chemical constituent $ $ $ m< m< 1 ac |Hot rolled steel sheetOf > Ό dw | X o > o At the Experiment Example CO CXI 03 CXI OCO AND CXI CO POO CO
Petition 870180070295, of 8/13/2018, p. 100/120
98/104
ο Q Ε8 LU Ο Q Ε8 LU The Q E8 LU the Q E8 LU the Q E8 LU the Q E8 LU the Q. E8 LU Material quality measurement results << SP θ '* 1 56 | 1 59 | Create LD CO O> CO laugh- LD laughs EL χο θ '* σ> Cri Cri CO LD 00 00 TS | MPa | I 086 | Cri σ> | 963 | I 1418 | | 1305 | I 1019 | | 1107 I Segregation of Mn Difference between Maximum value and Minimum value | mass% I 1 0.68 | 1 0.62 | CD 1 ^ θ ' I 0.82 | ri00 θ ' I 0.94 | O00 θ ' Concentrationminimum | Bulk% | δ σ> LD CD I St’2 I I 2.16 | I I I 8t‘2 | Maximum concentration | Bulk% | 1 2.39 | 1 | 1 | I 2.97 | I 3.00 | I 3.06 | I 2.98 | Hardness measurement results o E y- · _ε SP θ '· CN Cri CO Cri laugh Cri Cri S E X 'Cü SP θ '· CO LD Cri 1 ^ CO LD LD íd1 -0.62 1 1 ^ LD θ '1 1 ^ CD θ '1 1 -0.64 1 I -0.58 | 00 riθ '1 I -0.66 | H98 / H2CO Ο laugh ⁷ 1 4.29 | 1 3.92 1 1 | I 4.06 | 1 3.92 1 The laugh H98 1 ^Λ Η 1 5 Cri 1 SL * 1 1 510 | | 495 | | 396 | I 92 * | Cri T > τ 00 ο CO o LD O LD Cri Cri O rich Experiment Example 00 Cri o> Cri CO δ Create CO POO 3
Petition 870180070295, of 8/13/2018, p. 101/120
99/104 [00165] As shown in tables 15, 16, 18, 27, 28 and 33, it was confirmed that the 98% hardness measurement value was 1.5 or more times as high as the hardness measurement value 2%, that the kurtosis (K *) between the 2% hardness measurement value and the 98% hardness measurement value was -0.40 or less, that the average grain size was 10μπΊ or less and that the steel plate had excellent maximum tensile strength (TS), ductility (EL) and stretch-flanging capacity (λ), in the Examples of the present invention.
[00166] On the other hand, in Experiment Examples 9, 14, 17, 25, 30, 36, 39, 56 to 59, 85, 86, 89, 90, 93, 94, 101, 102, 117, 120 and 123 , as Comparative Examples of the present invention, there was no steel plate in which all of the maximum tensile strength (TS), ductility (EL) and the stretching-flanging capacity (λ) were sufficient, as shown below. Particularly, in Experiment Example 102, the total volume fractions of bainite and bainitic ferrite was 50% or more, the K * value was -0.4 or more, that is, the hardness distribution was close to normal distribution and therefore ductility was low even at a hardness ratio of 4.2.
[00167] In Experiment Example 9, the maintenance time in the bainite transformation temperature range was short in the third cooling process in the continuous annealing line, and the bainite transformation did not proceed sufficiently. For this reason, the bainite and bainitic ferrite ratios were low in Experiment Example 9, the kurtosis (K *) exceeded -0.40, the hardness distribution was not flat and had a valley, and therefore the stretching capacity λ deteriorated.
[00168] In Experiment Example 14, the reduction in rolling in the cold rolling process was below the lower limit, and the flatness of the steel plate deteriorated. In addition, since the lamination reduction was low, recrystallization did not proceed on the
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100/104 continuous annealing, the average grain size becomes coarse and therefore the stretch-flange capacity λ has been reduced.
[00169] In Experiment Example 17, the maintenance time in the ferrite transformation temperature range was short in the first cooling process, and the ferrite transformation did not proceed sufficiently. For this reason, a fraction of soft ferrite was low, H98 / H2 was below the lower limit, the difference in hardness between the hard part and the soft part was small and the EL ductility deteriorated, in Experiment Example 17.
[00170] In Experiment Example 25, since the maintenance time in the ferrite transformation temperature range was long, the ferrite transformation proceeded excessively. In Experiment Example 25, the cooling termination temperature exceeded the point of Ms in the second cooling process, and the tempered martensite was not obtained sufficiently. For this reason, the stretch-flanging capacity λ was reduced in Experiment Example 25.
[00171] In Experiment Example 30, the cooling termination temperature was below the lower limit in the second cooling process, and it was not possible to cause the bainite transformation to proceed in the third cooling process. For this reason, the bainite and bainitic ferrite ratios were low, the hardness distribution has a valley and, therefore, the λ stretch-flanging capacity deteriorated in Experiment Example 30.
[00172] In Experiment Example 36, the maximum heating temperature exceeded the upper limit, and the cooling termination temperature in the second cooling process was below the lower limit. For this reason, a fraction of tempered martensite increased, and soft structures, such as ferrite, were not present and, therefore, H98 / H2 was below the lower limit, the hardness difference between
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101/104 the hard part and the soft part were small and the EL ductility deteriorated, in Experiment Example 36.
[00173] Experiment Example 39 was an example in which the average cooling rate in the bainite transformation temperature range was low in the second cooling process and the bainite transformation proceeded excessively in the process. In Experiment Example 39, the tempered martensite was not present and, therefore, the tensile strength TS was insufficient.
[00174] The chemical constituents of steel sheets in Experiment Examples 56 to 59 were not within the definition range.
[00175] More specifically, the C content in steel W in Experiment Example 56 was below the lower limit defined in this invention. For this reason, the soft structure ratio was high and the tensile strength TS was insufficient, in Experiment Example 56.
[00176] In Experiment Example 57, the C content in steel X exceeded the upper limit. For this reason, the rate of the soft structure was low, and the ductility EL was insufficient, in Experiment Example 57.
[00177] In Experiment Example 58, the Si content in steel Y was below the lower limit. For this reason, the strength of tempered martensite was low and the tensile strength TS was insufficient in Experiment Example 58.
[00178] In Experiment Example 59, the Mn content in steel Z was below the lower limit. For this reason, a quenching property was significantly reduced, it was not possible to obtain tempered martensite and martensite that had soft structures and, therefore, TS tensile strength was insufficient, in Experiment Example 59. [00179] In the Examples of Experiments 85 and 102, the cooling rate from the completion of the hot rolling to the winding was below the lower limit. For this reason, the phase transformation proceeded excessively before winding, most parts
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102/104 of austenite in the steel plate disappeared, the Mn distribution did not proceed and a predetermined microstructure was not obtained in the continuous annealing line, in Experiment Examples 85 and 102. For this reason, K * kurtosis exceeds the upper limit and the stretch-flanging capacity λ was insufficient.
[00180] In Experiment Example 86, the maintenance time in the maintenance process in the martensite transformation temperature range in the continuous annealing line was below the lower limit. For this reason, the tempering martensite ratio was low, the kurtosis (K *) exceeded -0.40, the hardness distribution was not flat and had a valley, and therefore the stretch-flanging capacity λ was reduced, in the Experiment Example 86.
[00181] In Experiment Example 89, the winding temperature was below the lower limit. For this reason, the Mn distribution did not proceed and the predetermined microstructure was not obtained in the continuous annealing line in Experiment Example 89. For this reason, the K * kurtosis exceeded the upper limit and the λ stretch-flange capacity was insufficient. .
[00182] In Experiment Example 90, the reheat stop temperature in the reheat process on the continuous annealing line was below the lower limit. For this reason, the hardness of bainite and bainitic ferrite produced increased excessively, the difference in hardness between the ferrite hardness and the hardness of bainite and bainitic ferrite increased, the kurtosis (K *) exceeded -0.40, the hardness distribution had a valley and therefore the λ stretch-flange capacity was reduced.
[00183] In Experiment Example 93, the cooling rate after winding has exceeded the upper limit. For this reason, the distribution of Mn did not proceed and the predetermined microstructure was not obtained.
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103/104 in the continuous annealing line, in Experiment Example 93. Therefore, K * kurtosis exceeded the upper limit and the λ stretch-flange capacity was insufficient.
[00184] In Experiment Example 94, the rate of average temperature rise in the bainite transformation temperature range in the reheating process on the continuous annealing line exceeded the upper limit. For this reason, the hardness of produced bainite and bainitic ferrite increased excessively, the difference in hardness between the ferrite hardness and the hardness of bainite and bainitic ferrite increased, the kurtosis (K *) exceeded -0.40, the hardness distribution had a valley and therefore the λ stretch-flange capacity was reduced.
[00185] In Experiment Example 101, the maintenance time in the maintenance process in the martensite transformation temperature range in the continuous annealing line has exceeded the upper limit. For this reason, the hard lower bainite was produced, relatively soft bainite and / or bainite ferrite was not obtained, the kurtosis (K *) exceeded -0.40, the hardness distribution had a valley and, therefore, the stretching capacity λ flanging has been reduced.
[00186] In Experiment Example 117, the maximum heating temperature in the continuous annealing line has exceeded the upper limit. For this reason, the soft ferrite was not obtained, H98 / H2 was below the lower limit, the difference in hardness between the hard part and the soft part was small and the EL ductility deteriorated, in Experiment Example 117.
[00187] In example 120, the maximum heating temperature in the continuous annealing line was below the lower limit. For this reason, the less hard structure was obtained and the TS resistance deteriorated, in Experiment Example 120.
[00188] In Experiment Example 123, the stop temperature
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104/104 of cooling in the second cooling process in the continuous annealing line has exceeded the upper limit. For this reason, the tempered martensite was not obtained, the kurtosis (K *) exceeded -0.40, the hardness distribution had a valley and, therefore, the stretching-flanging capacity λ was reduced, in Experiment Example 123.
Industrial applicability [00189] Since the high strength steel sheet of the present invention contains predetermined chemical constituents, the hardness of 98% is 1.5 or more times as high as the hardness of 2%, the K * kurtosis of the distribution hardness between 2% hardness and 98% hardness is -0.40 or less, the average grain size in the steel plate structure is 10μΓη or less and therefore the steel plate has excellent ductility and stretch-flanging capability, while tensile strength that is as high as 900 MPa or more is ensured. Consequently, the present invention can make very significant contributions to the industry, since the strength of the steel sheet can be ensured without degrading the workability.

权利要求:
Claims (16)
[1]
1. High strength steel plate that has excellent ductility and a stretch-flanging capacity, the steel plate that is characterized by the fact that it consists of mass percentage:
0.05 to 0.4% C;
0.1 to 2.5% Si;
1.0 to 3.5% Mn;
0.001 to 0.03% P;
0.0001 to 0.01% S;
0.001 to 2.5% Al;
0.0001 to 0.01% N;
0.0001 to 0.008% O; and optionally, one or more among
0.005 to 0.09% Ti;
0.005 to 0.09% Nb;
0.0001 to 0.01% B;
0.01 to 2.0% Cr;
0.01 to 2.0% Ni;
0.01 to 2.0% Cu;
0.01 to 0.8% Mo;
0.005 to 0.09% of V; and one or more among Ca, Ce, Mg and ETR at 0.0001 to 0.5% by mass percentage in total; and a remaining iron compound and unavoidable impurities, a steel plate structure containing 10 to 50% of a ferrite phase, 10 to 50% of a tempered martensite phase, optionally a retained austenite, and optionally a remaining phase, where when a plurality of measurement regions
Petition 870180070295, of 8/13/2018, p. 108/120
[2]
2/8 with diameters of 1 gm or less is adjusted in a range from 1/8 to 3/8 of a thickness of the steel plate, the hardness measurement values in the plurality of measurement regions are arranged in ascending order to obtain a hardness distribution, an integer NO, 02 consisting of a number obtained by multiplying a total number of hardness measurement values by 0.02 and, if present, by rounding up a decimal number, is obtained, a hardness of a measured value consisting of a N0.02-th greater value from a lower hardness measurement value is considered to be a hardness of 2%, an integer NO, 98 which consists of a number obtained by multiplying the total number of hardness measurement values by 0.98 and, if present, by rounding down the decimal number, is obtained, and a hardness of a measurement value consisting of a N0.98th higher value from the measured value of dur Lesser hardness is considered to be a hardness of 98%, the hardness of 98% is 1.5 or more times as high as the hardness of 2%, with a K * kurtosis of the hardness distribution between the hardness of 2% and the 98% hardness is equal to or greater than -1.2 and equal to or less than -0.4, with an average grain size in the steel plate structure being 10gm or less, with a difference between a maximum value and a minimum value of Mn concentration in a base iron in a thickness range from 1/8 to 3/8 of the steel plate is equal to or greater than 0.4% and equal to or less than 3.5% when converted to the mass percentage, and the remaining phase includes one or both of a bainitic ferrite phase and a bainite phase and optionally a fresh martensite phase.
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[3]
3/8
2. High strength steel plate that has excellent ductility and stretch-flanging capacity, according to claim 1, characterized by the fact that when a section from 2% hardness to 98% hardness is equally divided into 10 parts and 10 1/10 sections are adjusted, a number of the hardness measurement values in each 1/10 section is 2 to 30% of a number of all measurement values.
3. High strength steel plate that has excellent ductility and stretch-flanging capacity, according to claim 1 or 2, characterized by the fact that the hard phase includes either or both of a bainitic ferrite phase and a phase of 10 to 45% bainite for a fraction by volume, and a fresh martensite phase of 10% or less.
[4]
4. High strength steel sheet that has excellent ductility and stretch-flanging capacity, according to any one of claims 1 to 3, characterized by the fact that the steel sheet structure includes 2 to 25% of a retained austenite .
[5]
5. High strength steel plate that has excellent ductility and stretch-flanging capacity, according to any one of claims 1 to 4, characterized by the fact that it comprises by mass percentage one or more among:
0.005 to 0.09% Ti; and
0.005 to 0.09% Nb.
[6]
6. High strength steel plate that has excellent ductility and stretch-flanging capacity, according to any one of claims 1 to 5,
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4/8 characterized by the fact that it comprises by mass percentage one or more of:
0.0001 to 0.01% B;
0.01 to 2.0% Cr;
0.01 to 2.0% Ni;
0.01 to 2.0% Cu; and
0.01 to 0.8% Mo.
[7]
7. High strength steel sheet that has excellent ductility and stretch-flanging capacity, according to any one of claims 1 to 6, characterized by the fact that it comprises by mass percentage:
0.005 to 0.09% of V.
[8]
8. High strength steel sheet that has excellent ductility and stretch-flanging capacity, according to any one of claims 1 to 7, characterized by the fact that it comprises one or more of Ca, Ce, Mg and ETR at 0, 0001 at 0.5% by mass percentage in total.
[9]
9. High-strength zinc-coated steel sheet that has excellent ductility and stretch-flanging capability, characterized by the fact that high-strength zinc-coated steel sheet is produced by forming a zinc-plated layer on a surface of the high-strength steel sheet as defined in any one of claims 1 to 8.
[10]
10. Method of manufacturing a high-strength steel sheet that has excellent ductility and a stretch-flanging capacity, as defined in claim 1, the method characterized by the fact that it comprises:
a hot rolling process in which a plate that
Petition 870180070295, of 8/13/2018, p. 111/120
5/8 contains the chemical constituents, as defined in any one of claims 1 and 6 to 9, is heated to 1050 ° C or more, directly or after cooling once, a hot lamination is carried out on it at a temperature higher than one at 800 ° C and an Are transformation point, and a winding is performed in a temperature range of 750 ° C or less in such a way that an austenite phase in a laminated material structure after lamination occupies 50% in volume or more;
a cooling process in which the steel sheet after hot rolling is cooled from a coiling temperature (the coiling temperature -100) ° C at a rate of 20 ° C / hour or less, while an Equation (1) next is satisfied;
a cold rolling process in which the steel sheet is subjected to acid pickling and a cold rolling in reduced rolling from 35 to 80%, as an optional process; and a process in which continuous annealing is performed on the steel sheet after cooling, in which in the process in which continuous annealing is performed, the steel sheet is annealed at a maximum heating temperature of 750 to 1000 ° C, a first cooling, in which the steel plate is cooled from the maximum heating temperature to a ferrite transformation temperature range or less and maintained in the ferrite transformation temperature range for 20 to 1000 seconds, is subsequently performed, a second cooling, in which the steel plate is cooled in order to satisfy (a transformation temperature range of
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6/8 bainite) / (maintenance time in the bainite transformation temperature range)> 10 ° C / second and cooling is stopped within a range from a martensite transformation start temperature - 120 ° C at start temperature of martensite transformation, is subsequently performed, the steel sheet after the second cooling is maintained in a range from a second temperature of cooling stop at the temperature of start of martensite transformation for 2 to 1000 seconds, at steel sheet is subsequently reheated to a reheat stop temperature, which is equal to or greater than a start temperature of bainite transformation -100 ° C, in order to satisfy (a range of bainite transformation temperature) / ( maintenance time in the bainite transformation temperature range)> 10 ° C / second, and a third cooling, in which the steel plate after reheating is cooled after from the reheat stop temperature to a temperature that is less than the bainite transformation temperature range and maintained in the bainite transformation temperature range for 30 seconds or more, is performed: [Equation 11 y ^and 9.47x] The ⁵ exp- ¹⁸⁴⁸⁰ Ϊ / (Γ) tj / l> 1.0 - (1) [where, t (T) in Equation (1) represents maintenance time (seconds) of the steel sheet at a temperature T ° C in the process cooling after winding].
[11]
11. Method of manufacturing high-strength steel sheet that has excellent ductility and stretch-flanging capacity, according to claim 10,
Petition 870180070295, of 8/13/2018, p. 113/120
7/8 characterized by the fact that the winding temperature after hot rolling is equal to or greater than a point of Bs and equal to or less than 750 ° C.
[12]
12. Method of manufacturing high-strength steel sheet which has excellent ductility and stretch-flanging capacity, according to claim 10 or 11, characterized by the fact that a sum of a time during which the steel sheet is kept in the bainite transformation temperature range in the second cooling and a time during which the steel sheet is kept in the bainite transformation temperature range in the reheat is 25 seconds or less.
[13]
13. Method of manufacturing a high-strength steel sheet that has excellent ductility and stretch-flanging capacity, according to any of claims 10 to 12, characterized in that the steel sheet is immersed in a zinc plating bath reheating.
[14]
14. Method of manufacturing a high-strength steel sheet that has excellent ductility and stretching-flanging capacity, according to any of claims 10 to 12, characterized by the fact that the steel sheet is immersed in a sheet bath with zinc in the temperature range of bainite transformation in the third cooling.
[15]
15. Method of manufacturing a high-strength steel plate that has excellent ductility and stretching-flanging capacity, according to any of claims 10 to 12, characterized by the fact that a zinc electroplating is performed after the third cooling.
[16]
16. Method of manufacturing a high-strength steel sheet that has excellent ductility and stretch-flanging capacity, according to any one of claims 10 to 12,
Petition 870180070295, of 8/13/2018, p. 114/120
8/8 characterized by the fact that hot-dip zinc plating is performed after the third cooling.

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CA2811189C|2014-04-22|

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ES2617477T3|2017-06-19|

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JPWO2012036269A1|2014-02-03|

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CA2811189A1|2012-03-22|

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KR101329840B1|2013-11-14|

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EP2617849A1|2013-07-24|

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BR112013006143A2|2016-06-14|

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法律状态:
2018-05-15| B06A| Notification to applicant to reply to the report for non-patentability or inadequacy of the application according art. 36 industrial patent law|

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2018-11-06| B09A| Decision: intention to grant|

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2018-12-18| B16A| Patent or certificate of addition of invention granted|Free format text: PRAZO DE VALIDADE: 20 (VINTE) ANOS CONTADOS A PARTIR DE 16/09/2011, OBSERVADAS AS CONDICOES LEGAIS. |

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2019-11-26| B25D| Requested change of name of applicant approved|Owner name: NIPPON STEEL CORPORATION (JP) |

优先权:

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申请号 | 申请日 | 专利标题

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JP2010-208330|2010-09-16|

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JP2010208329|2010-09-16|

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JP2010208330|2010-09-16|

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JP2010-208329|2010-09-16|

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PCT/JP2011/071222|WO2012036269A1|2010-09-16|2011-09-16|High-strength steel sheet with excellent ductility and stretch flangeability, high-strength galvanized steel sheet, and method for producing both|

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