HIGH RESISTANCE STEEL SHEET AND HIGH RESISTANCE GALVANIZED STEEL SHEET FOR CONFORMING CAPACITY AND M

专利摘要:
patent summary: "high strength steel sheet and high strength galvanized steel sheet excellent in forming capacity and production methods thereof". The present invention relates to a high strength steel sheet and high strength galvanized steel sheet which are excellent in forming capacity which guarantee a maximum tensile strength of 900 mpa or more while obtaining excellent ductility and flanging capability in the field. stretch sheets, which have predetermined ingredient compositions, have steel plate structures which contain a volume fraction of 1 to 20% residual austenite, and which have martensite transformation points of -60 ° C or any less.
公开号:BR112014002198B1
申请号:R112014002198-8
申请日:2012-07-27
公开日:2019-04-24
发明作者:Hiroyuki Kawata；Naoki Maruyama；Akinobu Murasato；Akinobu Minami；Takeshi Yasui；Yuji Yamaguchi
申请人:Nippon Steel & Sumitomo Metal Corporation；
IPC主号:

专利说明:

DESCRIPTION REPORT OF THE INVENTION PATENT FOR HIGH RESISTANCE STEEL SHEETS AND HIGH RESISTANCE GALVANIZED STEEL SHEETS EXCELLENT IN CONFORMATION CAPACITY AND PRODUCTION METHODS.
Technical Field [001] The present invention relates to a high-strength steel sheet and a high-strength galvanized steel sheet that are excellent in forming capacity and methods of producing them.
Fundamentals of Technique [002] In recent years there has been an increasing demand for greater strength in the steel sheet that is used for automobiles, etc. In particular, in order to improve safety in collisions, etc., a high strength steel plate of 900 MPa or more is also being used. Such high-strength steel sheet is inexpensively shaped in large volumes by pressing work in the same way as a mild steel sheet and is being used as structural members.
[003] However, in recent years, together with the rapid increase in strength of high strength steel sheet, particularly in high strength steel sheet with a maximum tensile strength of 900 MPa or more, the problem has arisen that forming capacity becomes insufficient and the work accompanied by local deformation such as stretching forming capacity becomes difficult. For this reason, even on high-strength steel sheet with a high maximum tensile strength, the realization of sufficient working capacity has become a requirement.
[004] PLT 1 describes, as a technique for improving the folding capacity of high strength steel sheet, a steel sheet
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2/69 with a tensile strength of 780 to 1470 MPa, a good shape, and an excellent bending capacity that is obtained by taking the steel sheet that has a microstructure comprised mainly of tempered bainite or martensite, making the amount of Si that is contained in steel, in mass%, 0.6% or less, cooling to a temperature at least 50 ° C lower than the predetermined transformation temperature of bainite to promote the transformation from austenite to bainite or martensite and thus making the volume rate of the residual austenite, which is contained in the structure and has a martensite transformation point of -196 ° C or more, 2% or less.
[005] PLT 2 describes, as a technique to improve the forming capacity of high-strength steel sheet, the method of improving ductility and flanging capacity in the drawing by cooling the steel sheet that has been hot rolled to 500 ° C or less, wind it up, then reheat it to 550 to 700 ° C, and then successively run a cold rolling process and a continuous annealing process so that a second phase that contains residual austenite and also contains a low temperature transformation phase becomes thin in average particle size and so that the amount of residual austenite, the amount of solid C solution in the residual austenite, and the average particle size satisfy the predetermined relationship formulas.
[006] PLT 3 describes, as a technique to improve the flanging capacity in the stretching of the high strength steel sheet, a steel sheet that has a reduced standard difference in hardness within the steel sheet and which is given a hardness equivalent throughout the steel plate region.
[007] PLT 4 describes, as a technique to improve the capacity
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3/69 flanging in the drawing of the high-strength steel plate, a steel plate that has reduced hardness in the hard portions by heat treatment and that has a reduced hardness difference with the soft parts.
[008] PLT 5 describes as a technique to improve the flanging capacity in the stretching of the high strength steel sheet, making the bainite relatively soft like the hard portions, in order to reduce the difference in the hardness of the soft parts.
[009] PLT 6 describes, as a technique to improve the flanging capacity in the drawing of high-strength steel sheet, a steel sheet that has a structure comprised of, in area rate, 40 to 70% tempered martensite and the balance being ferrite where the ratio between the upper limit value and the lower limit value of the MN concentration in the cross section in the direction of the thickness of the steel plate is reduced.
List of Citations Patent Literature
PLT 1: Japanese Patent Publication No. 10-280090A PLT 2: Japanese Patent Publication No. 2003-183775A PLT 3: Japanese Patent Publication No. 2008-266779A PLT 4: Japanese Patent Publication No. 2007-302918A PLT 5: Japanese Patent Publication n ° 2004-263270A PLT 6: Japanese Patent Publication n ° 2010-65307A
Summary of the Invention
Technical Problem [0010] In the high-strength steel sheet that is described in PLT1, there is the problem that, in the steel sheet structure, there is little ferrite and residual austenite to improve ductility and, therefore, sufficient ductility cannot be obtained.
[0011] The production method of high strength steel sheet
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4/69 according to PLT 2, requires large-scale reheating equipment, so there is a problem that the cost of production increases.
[0012] Also in the techniques that are described in PLTs 3 to 6, the working capacity in high strength steel sheet with a maximum tensile strength of 900 MPa or more is insufficient.
[0013] The present invention was made in consideration of the above problems, and aims to supply high strength steel sheet and high strength galvanized steel sheet that are excellent in forming capacity and methods of producing them by which a maximum tensile strength of 900 MPa or more is guaranteed while excellent ductility and stretching flanging capacity are obtained.
Solution to the Problem [0014] Inventors etc. engaged in intense studies in the structure of the steel sheet and in the production method to obtain excellent ductility and flanging capacity in the drawing in the high strength steel sheet. As a result, they found that by making the steel ingredients have suitable ranges and also by establishing suitable annealing conditions after cold rolling, it is possible to make the ratio of the residual austenite phase in the steel sheet structure to having a predetermined range while decreasing the temperature at the start of the transformation of the martensite of the residual austenite phase, and producing a high strength steel plate under such conditions and controlling the ratio of the residual austenite phase in the structure of the steel plate and the point transformation into martensite for suitable ranges, a maximum tensile strength of 900 MPa or greater is guaranteed while the ductility and the flanging capacity in the stretch (hole expansion capacity) are improved and a
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5/69 excellent forming capacity.
[0015] The present invention was made as a result of other studies based on the above findings and has its essence as follows:
(1) High strength steel sheet which is excellent in forming capacity and contains, in weight%, C: 0.075 to 0.300%, Si: 0.70 to 2.50%, Mn: 1.30 to 3, 50%, P: 0.001 to 0.030%, S: 0.0001 to 0.0100%, Al: 0.005 to 1.500%, N: 0.0001 to 0.0100%, and O: 0.0001 to 0.0100% , which contains, as optional elements, one or more elements between Ti: 0.005 to 0.150%, Nb: 0.005 to 0.150%, B: 0.0001 to 0.0100%, Cr: 0.01 to 2.00%, Ni : 0.01 to 2.00%, Cu: 0.01 to 2.00%, Mo: 0.01 to 1.00%, V: 0.005 to 0.150%, and one or more elements between Ca, Ce, Mg , Zr, Hf, and REM: total 0.0001 to 0.5000%, and has a balance of iron and the inevitable impurities, where the steel plate structure contains, in fraction of volume, 2 to 20% of austenite phase residual, and the residual austenite phase has a transformation point of -60 ° C or less.
(2) The high strength steel sheet which is excellent in forming capacity according to item (1), characterized by the fact that the ratio of the residual austenite phase that turns into martensite at -198 ° C is, in volume fraction, 2% or less in the total residual austenite phase.
(3) The high strength steel sheet which is excellent in forming capacity according to item (1) or (2), characterized by the fact that the residual austenite phase has a martensite transformation point of -198 ° C or less.
(4) The high strength steel sheet which is excellent in forming capacity according to any of items (1) to (3), characterized by the fact that the steel sheet structure contains, in volume fraction, ferrite phase: 10 to 75%, bainitic ferrite phase and / or bainite phase: 10 to 50%, tempered martensite phase: 10 to 50%, and
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6/69 “fresh” martensite: 10% or less.
(5) High strength galvanized steel sheet which is excellent in forming capacity, characterized by comprising the high strength steel sheet according to any of the items (1) to (4) on whose surface the galvanized layer is formed.
(6) A method of producing high strength steel sheet which is excellent in forming capacity, characterized by a hot rolling process of heating a plate containing, in mass%, C: 0.075 to 0.300%, Si : 0.70 to 2.50%, Mn: 1.30 to 3.50%, P: 0.001 to 0.030%, S: 0.0001 to 0.0100%, Al: 0.005 to 1.500%, N: 0, 0001 to 0.0100%, and O: 0.0001 to 0.0100%, which contains, as optional elements, one or more elements between Ti: 0.005 to 0.150%, Nb: 0.005 to 0.150%, B: 0.0001 to 0.0100%, Cr: 0.01 to 2.00%, Ni: 0.01 to 2.00%, Cu: 0.01 to 2.00%, Mo: 0.01 to 1.00%, V: 0.005 to 0.150%, and one or more elements between Ca, Ce, Mg, Zr, Hf, and REM: total 0.0001 to 0.5000%, and has a balance of iron and the inevitable impurities, directly, or after cooling once , up to 1050 ° C or more, finish rolling at point Ar3 or more to obtain a steel sheet, and wind it to a temperature of 500 to 750 ° C, a cold rolling process of stripping the coiled steel sheet , and then They will not be cold rolled at a reduction rate of 35 to 75%, and an annealing process to heat the steel sheet after the cold rolling process to a maximum heating temperature of 740 to 1000 ° C, then cool it at an average cooling rate from the maximum heating temperature of 700 ° C from 1.0 to 10.0 ° C / s and an average cooling rate of 700 to 500 ° C from 5.0 to 200 ° C / s, then maintaining at 350 to 450 ° C for 30 to 1000 seconds, and then cooling to room temperature, reheat from Bs or less than 500 ° C to 500 ° C or more at least once and reheat
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7/69 from the point Ms or less than 350 ° C to 350 ° C or more at least once.
(7) The method of producing high strength galvanized steel sheet which is excellent in forming capacity characterized by the production of high strength steel sheet by the method of producing high strength steel sheet according to item (6 ), and then galvanizing it.
(8) A method of producing high strength galvanized steel sheet which is excellent in forming capacity characterized by the production of high strength steel sheet by the production method according to item (6) during the annealing process of even, when cooling from the maximum heating temperature to room temperature, dip the steel sheet after the cold rolling process in a zinc bath in order to galvanize it by hot immersion.
(9) A high strength galvanized steel sheet production method that is excellent in forming capacity characterized by the production of the high strength steel sheet by the production method according to item (6) and after the annealing process perform hot-dip galvanizing.
(10) A method of producing galvanized steel sheet which is excellent in forming capacity according to item (8) or (9) characterized by carrying out the bonding treatment at a temperature of 470 to 650 ° C after galvanizing by hot immersion. Advantageous Effects of the Invention [0016] In accordance with the present invention, a high strength steel sheet can be obtained where a maximum tensile strength of 900 MPa is guaranteed while an excellent forming capacity is obtained.
Brief Description of Drawings
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8/69 [0017] FIG. 1A is a view showing an example of a cooling pattern in an annealing treatment in the production method of the present invention.
[0018] FIG. 1B is a view showing another example of a cooling pattern in an annealing treatment in the production method of the present invention.
[0019] FIG. 2 is a view that explains a configuration of the present invention and a view that shows the relationship between the tensile strength TS and the total elongation EL.
[0020] FIG. 3 is a view explaining a configuration of the present invention and a graph showing the relationship between the tensile strength TS and the hole expansion rate λ.
Description of Embodiments [0021] The high-strength steel sheet and the high-strength galvanized steel sheet which are excellent in forming capacity and production methods for the embodiments of the present invention will be explained below. Note that the following embodiments are explained in detail to allow the essence of the present invention to be better understood, so, unless otherwise stated, they do not limit the present invention.
[0022] Note that, in the following explanation, the starting temperature at which austenite (γ iron) becomes martensite in the process of dropping the temperature in the production of the steel sheet will be referred to as point Ms while the starting temperature at which residual austenite that is produced in the structure of the high strength steel sheet of the present invention turns into martensite will be referred to as point Msr.
[0023] Initially, the structure of the high-strength steel plate of the present invention will be explained.
[0024] The structure of the high strength steel sheet of this
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9/69 invention has 2 to 20% residual austenite phase. The residual austenite phase has an Msr point of -60 ° C or less. The residual austenite phase that is contained in such a steel plate structure of the high strength steel plate of the present invention is stable even in relation to a plurality of deep cooling treatments.
[0025] A structure different from the residual austenite phase is not particularly limited, as long as the maximum tensile strength of 900 MPa or greater can be guaranteed, but preferably it has, in fraction of volume in the steel plate structure, a ferrite phase: 10 to 75%, a bainite ferrite phase and / or a bainite phase: 10 to 50%, a tempered martensite phase: 10 to 50%, and a "fresh" martensite phase: 10% or less. By having such a steel plate structure, the result becomes a high strength steel plate that has an excellent forming capacity.
[0026] The phases that can be obtained in the steel plate structure will be explained below:
Residual Austenite Phase [0027] The residual Austenite phase has the property of greatly improving strength and ductility, but in general forms fracture starting points and greatly degrades the stretching flanging capacity.
[0028] In the structure of the present invention steel plate, heating twice as explained later, the defects that were present in the residual austenite phase and were capable of forming starting points for transformation into martensite are already consumed and only the phase austenite with its high degree of cleanliness remains selectively. As a result, an extremely stable residual austenite phase is obtained. Such residual austenite phase gradually turns into martensite together with deformation, so it has the property of not easily forming points
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10/69 start of fractures and cause an extremely small deterioration of the flanging capacity in the stretch.
[0029] As an indicator of the aforementioned stability, the temperature at which martensite starts to be transformed (Msr point) of the residual austenite phase can be mentioned. The stable residual austenite in which an austenite phase with a high degree of cleanness remains does not change in amount of residual austenite even with immersion in liquid hydrogen for an hour, that is, applying to the so-called deep cooling treatment. The Msr point is the temperature of liquid hydrogen (-198 ° C) or less and is extremely stable. In addition, in general, repeating the application of the deep cooling treatment, the residual austenite is gradually decreased, but in the high-strength steel plate according to the present invention, the residual austenite does not decrease and is extremely stable even if treated five times by deep cooling.
[0030] The steel sheet of the present invention gives a high strength steel sheet with a strength and ductility that are greatly improved and with a flange stretching capacity that is extremely small in deterioration by a residual austenite phase with an Msr point -60 ° C or less present in a volume fraction of 2% or more.
[0031] From the point of view of strength and ductility, the volume fraction of the residual austenite phase in the steel sheet structure is preferably 4% or more, more preferably 6% or more. On the other hand, to make the volume fraction of the residual austenite phase in the steel sheet structure greater than 20%, it is necessary to add elements such as C or Mn above the adequate amount resulting in the fact that the welding capacity is impaired, so the upper limit of the residual austenite phase is made 20%.
[0032] In the present invention, the residual austenite phase ratio that
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11/69 turns into martensite at -198 ° C and is preferably at a volume fraction of 2% or less. Because of this, a more stable residual austenite phase is obtained, so the ductility and the flanging capacity in the stretch are remarkably improved and an excellent forming capacity is obtained.
[0033] In addition, if the Msr point of residual austenite in the steel sheet structure is -198 ° C or less, the result becomes a more stable residual austenite phase, ductility and the ability to flange in the stretch are also notably improved, and excellent forming ability is achieved, so this is preferable.
[0034] The volume fraction of the residual austenite phase is obtained by examining the steel sheet in the plane parallel to the surface of the sheet at 1/4 of the thickness by x-ray analysis, calculating the area fraction, and considering this as the volume fraction. However, the plane at 1/4 of the thickness is made the plane obtained by polishing and chemical polishing the base material again after the deep cooling treatment to obtain a mirror finish.
[0035] In addition, considering the measurement error, the residual austenite phase is considered to transform into martensite at the point in time when the relationship shown below is satisfied:
V _Y (n) / V _Y (0) <0.90 where n is the number of times of the deep cooling treatment, _Y (n) is the percentage of residual austenite after the n ° deep drawing treatment, and V _Y (0) is the percentage of residual austenite in the base material.
Ferrite Phase [0036] The ferrite phase is a structure that is effective in improving ductility and is preferably contained in the structure of the steel sheet in a volume fraction of 10 to 75%. If the volume fraction of the phase
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12/69 ferrite in the steel plate structure is less than 10%, a sufficient ductility is not likely to be obtained. The ferrite fraction in the steel sheet structure, from the point of view of ductility, is more preferably 15% or more, even more preferably 20% or more. The ferrite phase is a soft structure, so if the volume fraction exceeds 75%, sufficient strength will sometimes not be achieved. In order to sufficiently increase the tensile strength of the steel sheet, the volume fraction of the ferrite phase in the steel sheet structure is more preferably made 50% or less.
Bainitic Ferrite Phase and / or Bainite Phase [0037] The bainitic ferrite phase and / or the bainite phase is a structure with a good balance of strength and ductility and is preferably contained in the steel plate structure in a volume fraction of 10 to 50 %. The bainitic and / or bainite ferrite phase is a microstructure that has an intermediate resistance to that of a soft ferrite phase and hard martensite phase and tempered martensite phase and residual austenite phase. From the point of view of the flanging capacity in the stretch, the inclusion of 15% or more is more preferable and inclusion of 20% or more is more preferable. If the volume fraction of the bainitic and / or bainite ferrite phase exceeds 50%, the yield strength will increase excessively and the freezing capacity of the shape will deteriorate, then this is not preferred.
Tempered Martensite Phase [0038] The tempered Martensite phase is a structure that greatly improves tensile strength and can be included in the steel sheet structure up to a volume fraction of 50% or less. From the point of view of tensile strength, the volume fraction of the tempered martensite is preferably 10% or more. If the volume fraction of the tempered martensite that is contained in the steel sheet structure exceeds 50%, the yield strength will increase excessively, and the
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13/69 the shape's freezing capacity will deteriorate, so this is not preferable.
"Fresh" Martensite Phase [0039] The "fresh" Martensite Phase has the effect of greatly improving the tensile strength. However, it forms fracture starting points and greatly degrades the stretching flanging capacity, so it is preferably limited to a volume fraction of 15% in the steel plate structure. To increase the stretching flanging capacity, it is more preferable to make the volume fraction of the tempered martensite phase in the steel sheet structure 10% or less, even more preferably 5% or less.
Others [0040] The structure of the high-strength steel sheet of the present invention may also contain a pearlite phase and / or a crude cementite phase or other structure. However, if the structure of the high-strength steel sheet contains a large amount of pearlite phase and / or crude cementite phase, the problem of deterioration in the folding capacity arises. Hence, the volume fraction of the pearlite phase and / or the crude cementite phase that is contained in the steel sheet structure is preferably a total of 10% or less, more preferably 5% or less.
[0041] The volume fractions of the different structures that are contained in the structure of the high-strength steel sheet of the present invention can, for example, be measured by the following method: [0042] To measure the volume fractions of the ferrite phase, bainitic ferrite phase, bainite phase, tempered martensite phase, and “fresh” martensite phase that are contained in the structure of the high strength steel plate of the present invention, a sample is initially taken using the cross section of the plate thickness parallel to the
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14/69 steel sheet rolling direction as the examined surface. In addition, the examined surface of this sample is polished and etched by Nital and the range of 1/8 to 3/8 of the thickness of the plate is observed by a scanning electron microscope with field emission (FESEM) to measure the fraction of area . This was considered as the volume fraction.
[0043] In the following, the composition of ingredients of the high-strength steel plate of the present invention will be explained. Note that in the following explanation, unless otherwise designated,% indicates% by mass.
C: 0.075 to 0.300% [0044] C is an element that is necessary to obtain a residual austenite phase. It is included to achieve both excellent forming capacity and high strength. If the C content exceeds 0.300%, the welding capacity becomes insufficient. From the point of view of the weldability, the C content is more preferably 0.250% or less, even more preferably 0.220% or less. If the C content is less than 0.075%, it becomes difficult to obtain a sufficient amount of residual austenite phase and the strength and conformability drop. From the point of view of strength and conformability, the C content is more preferably 0.090% or more, even more preferably 0.100% or more.
Si: 0.70 to 2.50% [0045] Si is an element that allows the residual austenite phase to be easily obtained by suppressing the formation of iron-based carbides in the steel plate and is an element that is necessary to increase resistance and conformability. If the Si content exceeds 2.50%, the steel sheet becomes brittle and the ductility deteriorates. From the point of view of ductility, the Si content is more preferably 2.20% or less, even more preferably 2.00% or less. If the
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15/69 Si content is less than 0.70%, iron-based carbides form after annealing while cooling to room temperature, the residual austenite phase cannot be achieved sufficiently, and the strength and forming capacity deteriorate. From the point of view of strength and conformability, the lower limit value of Si is more preferably 0.90% or more, even more preferably 1.00% or more.
Mn: 1.30 to 3.50% [0046] Mn is added to increase the strength of the steel plate. If the Mn content exceeds 3.50%, parts concentrated with crude Mn form at the center of the thickness of the steel sheet, embrittlement occurs easily, and the rupture of the cast plate or other problems arise easily. In addition, if the Mn content exceeds 3.50%, there is a problem that the welding capacity also deteriorates. Therefore, the Mn content has to be made 3.50% or less. From the point of view of the weldability, the Mn content is more preferably 3.20% or less, even more preferably 3.20% or less, even more preferably 3.00% or less. If the Mn content is less than 1.30%, a large number of soft structures are formed during cooling after annealing, then ensuring a maximum tensile strength of 900 MPa or more becomes difficult. Therefore, the Mn content has to be made 1.30% or more. In addition, to increase the strength of the steel sheet, the Mn content is more preferably 1.50% or more, even more preferably 1.70% or more.
P: 0.001 to 0030% [0047] P tends to segregate in the center of the thickness of the steel sheet and is likely to make the welding zone fragile. If the P content exceeds 0.030%, the welding zone becomes highly fragile, then the P content is limited to 0.030% or less. The lower limit of P is not particularly adjusted as long as the effect of this
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16/69 invention is displayed, but if the P content is less than 0.001%, the production cost increases greatly, so the lower limit is made 0.001%.
S: 0.0001 to 0.0100% [0048] S has a detrimental effect on the welding capacity and the production capacity at the time of casting and when hot rolling. Therefore, the upper limit value of the S content is made 0.0100% or less. In addition, S binds to Mn to form crude MnS which causes ductility and flanging capacity in the stretch to drop, so the S content is preferably made 0.0050% or less, even more preferably 0.0025% or less. The lower limit of the S content is not particularly adjusted as long as the effect of the present invention is exhibited, but if the S content is less than 0.0001%, the production cost increases greatly, so 0.0001% is made the lower limit.
Al: 0.005 to 1.500% [0049] Al is an element that suppresses the formation of iron-based carbides and allows residual austenite to be easily obtained. It increases the strength and forming capacity of the steel sheet. If the Al content exceeds 1,500%, the welding capacity deteriorates, then the upper limit is made 1,500%. From the point of view of the weldability, the Al content is more preferably 1,200% or less, even more preferably 0.900% or less. Al is an element that is also effective as a deoxidizing material, but if the Al content is less than 0.005%, the effect as a deoxidizing material is not sufficiently obtained, so the lower limit of the Al content is made 0.005%. In order to sufficiently obtain the deoxidation effect, the amount of Al is most preferably made at 0.010% or more.
N: 0.0001 to 0.0100% [0050] N forms crude nitrides that make ductility and
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17/69 flange capacity in the stretch deteriorates, so the amount of addition has to be kept low. If the Ni content exceeds 0.0100%, this trend becomes more marked, then the upper limit of the NI content is made 0.0100%. N becomes the cause of bubble formation at the time of welding, so the lower its content, the better. The lower limit of the N content is not particularly adjusted as long as the effect of the present invention is exhibited, but if the N content is less than 0.0001%, the production cost increases greatly, so 0.0001% is made the limit bottom.
O: 0.0001 to 0.0100% [0051] O forms oxides that cause ductility and flanging capacity in the stretch to deteriorate, so the content has to be kept low. If the O content exceeds 0.0100%, the deterioration of the stretching flanging capacity becomes noticeable, then the upper limit of the O content is made 0.0100% or less. The O content is more preferably 0.0080% or less, more preferably 0.0060% or less. lower limit of the O content is not particularly adjusted as long as the effect of the present invention is exhibited, but if the O content is less than 0.0001%, the production cost increases greatly, so 0.0001% is made inferior limit.
[0052] The high-strength steel sheet of the present invention can also contain the elements that are shown below according to need:
Ti: 0.005 to 0.150% [0053] Ti is an element that contributes to an increase in the strength of the steel plate by reinforcing precipitation, reinforcing fine grain by suppressing the growth of ferrite crystal grains, and reinforcing displacement by suppressing recrystallization. If the Ti content exceeds 0.150%, the precipitation of carbonitrides increases and the capacity for forming capacity
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18/69 deteriorates, so the IT content is made 0.150% or less. From the point of view of forming capacity, the Ti content is more preferably 0.100% or less, even more preferably 0.070% or less. To obtain sufficiently the effect of increasing the resistance by Ti, the Ti content has to be made 0.005% or more. To increase the strength of the steel sheet, the Ti content is preferably 0.010% or more, more preferably 0.015% or more.
Nb: 0.005 to 0.150% [0054] Nb is an element that contributes to the increase in the strength of the steel plate through the reinforcement of precipitation, the reinforcement of the fine grain by suppressing the growth of the ferrite crystal grains, and reinforcement of the displacement by suppressing recrystallization. If the Nb content exceeds 0.150%, the precipitation of carbonitrides increases and the forming capacity deteriorates, then the Nb content is made 0.150% or less. From the point of view of forming ability, the Nb content is more preferably 0.100% or less, even more preferably 0.060% or less. In order to sufficiently obtain the effect of increasing the resistance by Nb, the Nb content has to be made 0.005% or more. To increase the strength of the steel sheet, the Nb content is preferably 0.010% or more, more preferably 0.015% or more.
V: 0.005 to 0.150% [0055] V is an element that contributes to the increase in the strength of the steel sheet by reinforcing precipitation, by reinforcing the fine grain by suppressing the growth of the ferrite crystal grains, and by reinforcing the displacement by suppressing recrystallization. If the V content exceeds 0.150%, the precipitation of carbonitrides increases and the forming capacity deteriorates, then the content is made 0.150% or less. In order to sufficiently obtain the effect of increasing resistance by V, the content must be 0.005% or more.
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19/69
B: 0.0001 to 0.0100% [0056] B is an element that suppresses the phase transformation at high temperature and is effective in increasing resistance and can be added instead of part of C and / or Mn. If the B content exceeds 0.0100%, the working capacity while hot is impaired and productivity drops, then the B content is made 0.0100% or less. From the point of view of productivity, the B content is preferably 0.0050 or less, more preferably 0.0030% or less. To obtain sufficiently greater resistance to B, the B content must be made 0.0001% or more. To effectively increase the strength of the steel sheet, the B content is preferably 0.0003% or more, more preferably 0.0005% or more.
Mo: 0.01 to 1.00% [0057] Mo is an element that suppresses the phase transformation at a high temperature and is effective in increasing resistance and can be added instead of part of C and / or Mn. If the Mo content exceeds 1.00%, the working capacity when hot is impaired and productivity drops, then the Mo content is made 1.00% or less. To obtain sufficiently greater resistance to Mo, the content must be 0.01% or more.
W: 0.01 to 1.00% [0058] W is an element that suppresses the phase transformation at a high temperature and is effective in increasing resistance and can be added instead of part of C and / or Mn. If the W content exceeds 1.00%, the working capacity when hot is impaired and productivity drops, then the W content is made 1.00% or less. To obtain a sufficiently higher resistance for W, the content must be 0.01% or more.
Cr: 0.01 to 2.00% [0059] Cr is an element that suppresses the phase-to-transformation
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20/69 high temperature and is effective for increasing strength and can be added in place of part of C and / or Mn. If the Cr content exceeds 2.00%, the working capacity when hot is impaired and productivity falls, then the Cr content is made 2.00% or less. To obtain sufficiently greater resistance to Cr, the content must be 0.01% or more.
Ni: 0.01 to 2.00% [0060] Ni is an element that suppresses the phase transformation at a high temperature and is effective in increasing resistance and can be added instead of part of C and / or Mn. If the Ni content exceeds 2.00%, the welding capacity is impaired, then the Ni content is made 2.00% or less. To obtain a sufficiently higher resistance for Ni, the content must be 0.01% or more.
Cu: 0.01 to 2.00% [0061] Cu is an element that increases the resistance due to the presence of fine particles in steel and can be added instead of part of C and / or Mn. If the Cu content exceeds 2.00%, the welding capacity is impaired, then the content is made 2.00% or less. To obtain a sufficiently higher resistance for Cu, the content must be 0.01% or more.
[0062] One or more elements between Ca, Ce, Mg, Zr, Hf, and REM: 0.0001 to 0.5000% in total [0063] Ca, Ce, Mg, Zr, Hf, and REM are elements that are effective to improve conformability. One or more can be added. If the content of one or more between Ca, Ce, Mg, Zr, Hf, and REM exceeds a total of 0.5000%, on the contrary the ductility is likely to be impaired, then the total content of the elements is made 0, 5000% or less. In order to sufficiently obtain the effect of improving the forming capacity of the steel sheet, the total content of the elements must be 0.0001% or more. From the point of view of
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According to conformation, the total content of the elements is preferably 0.0005% or more, more preferably 0.0010% or more. Here, REM is an abbreviation for rare earth metal and indicates the elements that belong to the lanthanoid series. In the present invention, REM or Ce is often added as Misch metal. Sometimes, elements of the lanthanoid series in addition to La and Ce are contained in compound. Furthermore, even when elements of the lantanoid series other than Ce are included, the effects of the present invention are presented.
[0064] The composition of ingredients of the present invention has been explained above, but as long as they do not impair the properties of the steel sheet of the present invention, for example, elements other than the essential elements added can also be included as impurities that are derived from the materials of match. [0065] The high-strength steel sheet of the present invention can also be made of a high-strength galvanized sheet on whose surface a galvanized layer or a galvannealed layer is formed. The formation of a galvanized layer on the surface of the high-strength steel plate results in a steel plate that has excellent resistance to corrosion. In addition, the formation of a galvannealed layer on the surface of the high-strength steel plate results in a steel plate that has excellent corrosion resistance and has excellent coating adhesion.
[0066] Next, the production method of the high-strength steel plate of the present invention will be explained.
[0067] To produce the high-strength steel plate of the present invention, a plate is initially cast which has the above-mentioned composition of ingredients. As a plate that is used for hot rolling, for example, it is possible to use a continuously cast plate or a plate that is produced by a
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22/69 thin plates, etc. For the production method of the high strength steel sheet of the present invention, it is preferable to use a process such as direct continuous casting (CC-DR) where the steel is cast, and then immediately hot rolled.
[0068] The heating temperature of the plate in the hot rolling process must be 1050 ° C or more. If the heating temperature of the plate is low, the temperature of the finishing laminate falls below the point Ar3. As a result, two-phase lamination of the ferrite and austenite phases results, so that the hot-rolled sheet structure becomes a mixed-grain structure. The irregular structure is not eliminated even after cold rolling and the annealing process and therefore the ductility and the folding capacity deteriorate. In addition, if the temperature of the finishing lamination drops, the lamination load increases and the lamination becomes difficult or defects in shape are likely to happen on the steel sheet after lamination. The upper limit of the heating temperature of the plate is not particularly adjusted as long as the effect of the present invention is presented, but it is not economically preferable to adjust the heating temperature to an excessively high temperature, then the upper limit of the heating temperature of the plate preferably 1350 ° C or less.
[0069] The Ar3 point can be calculated using the following formula: Ar3 (° C) = 901-325xC + 33xSi92x (Mn + Ni / 2 + Cr / 2 + Cu / 2 + Mo / 2) + 52xAl [0070] In the formula above, C, Si, Mn, Ni, Cr, Cu, Mo, and Al are the levels of the different elements (% by mass).
[0071] The temperature of the finishing lamination of the hot lamination is set higher between 800 ° C or the Ar3 point as the lower limit and 1000 ° C as the upper limit. If the temperature of the
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23/69 finish is less than 800 ° C, the rolling load at the time of finishing lamination becomes high, the lamination becomes difficult, and shape defects are likely to be presented in the hot rolled steel sheet that is obtained after lamination. If the temperature of the finishing lamination is lower than the Ar3 point, the hot lamination becomes a two phase region lamination of the ferrite phase and the austenite phase and the structure of the hot rolled steel sheet will sometimes become a structure of mixed grains.
[0072] The upper temperature limit of the finishing laminate is not particularly adjusted as long as the effect of the present invention is presented, but if the finishing temperature is made too high, to guarantee that temperature, the heating temperature of the plate has to be made excessively high. Therefore, the upper temperature limit of the finishing laminate is preferably made 1000 ° C or less. [0073] The steel sheet after rolling is wound at 500 to 750 ° C. If the steel sheet is wound at a temperature exceeding 750 ° C, the oxides that are formed on the surface of the steel sheet increase excessively in thickness and the stripping capacity deteriorates. To increase the pickling capacity, the coiling temperature is preferably 720 ° C or less, more preferably 700 ° C or less. If the coiling temperature becomes less than 500 ° C, the hot rolled steel sheet becomes excessively high in strength and cold rolling makes it difficult. In order to decrease the load in cold rolling, the winding temperature is preferably made at 550 ° C or more. 600 ° C or more is more preferable.
[0074] The hot-rolled steel sheet thus produced is pickled. Due to pickling, the oxides on the steel sheet surface can be removed. This is important from the point of view of
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24/69 improve the chemical conversion capacity of the high-strength cold-rolled steel sheet of the final product or the ability to hot-dip coating the cold-rolled steel sheet for use on hot-dip galvanized steel sheet or in galvannealed steel sheet. Stripping can be just a single treatment or it can be divided into a plurality of treatments.
[0075] The pickled steel plate can be supplied in the state to the annealing process, but by cold rolling at a reduction rate of 35 to 75%, a steel plate with high thickness precision and excellent shape is obtained. If the rate of reduction is less than 35%, it is difficult to maintain the flat shape and the final product becomes poor in ductility, then the rate of reduction is made 35% or more. If the reduction rate exceeds 75%, the cold rolling load becomes very large and cold rolling becomes difficult. Hence, the upper limit of the rate of reduction is 75%. The number of lamination passes and the reduction rate for each pass are not particularly prescribed as long as the effect of the present invention is presented.
[0076] Next, the hot-rolled steel sheet or the cold-rolled steel sheet obtained is subjected to the annealing treatment below.
[0077] Initially, the cold-rolled sheet is heated to a maximum heating temperature in the range of 740 ° C to 1000 ° C. If the maximum heating temperature is less than 740 ° C, the amount of austenite phase becomes insufficient and it is difficult to guarantee a sufficient amount of hard structures in the phase transformation during the subsequent cooling. If the maximum heating temperature exceeds 1000 ° C, the austenite phase becomes rough in particle size, the transformation does not proceed easily during cooling and, in particular, a soft ferrite structure becomes hard to obtain sufficiently.
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25/69 [0078] Heating up to the maximum heating temperature is preferably carried out with a heating rate from (maximum heating temperature -20) ° C to the maximum heating temperature, that is, in the last 20 ° C at the moment heating, from 0.1 to 0.8 ° C / s. By making the heating rate of 20 ° C up to the maximum heating temperature gradual heating in the above range, the effects are obtained that the rate of advance of the reverse transformation to the austenite phase becomes slower and the phase defects initial austenite become smaller.
[0079] The retention time at the time of heating up to the maximum heating temperature can be properly determined according to the maximum heating temperature, etc. and it is not particularly limited, but 10 seconds or more is preferable, while 40 to 540 seconds is more preferable.
[0080] The primary cooling is then performed at an average rate from the maximum heating temperature of 700 ° C to 10.0 ° C / s. Through this primary cooling it is possible to make the transformation of the ferrite and the transformation to bainitic and / or bainite ferrite proceed properly while leaving an austenite phase not transformed to the point MS and transforming all or part into martensite.
[0081] If the average cooling rate in the above cooling temperature range is less than 1.0 ° C / s, the transformation into perlite continues during cooling with which the untransformed austenite phase is reduced and a sufficiently hard structure cannot be obtained. As a result, it is sometimes not possible to guarantee the maximum tensile strength of 900 MPa or more. If the average cooling rate exceeds 10.0 ° C / s, sometimes the soft ferrite structure cannot be formed sufficiently.
[0082] The retention time in the temperature region of the
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26/69 transformation into ferrite from immediately after heating until when the temperature of the steel plate reaches 700 ° C is not particularly limited, but is preferably 20 to 1000 seconds. To make the ferrite phase smoothly formed sufficiently, it is necessary to keep the steel for 20 seconds or more in the region of ferrite transformation temperatures from immediately after annealing until when the temperature of the steel plate reaches 700 ° C, preferably keeping it there for 30 seconds or more, more preferably keep it there for 50 seconds or more. If the time during which the steel is made to remain in the region of ferrite transformation temperatures exceeds 1000 seconds, the transformation into ferrite proceeds excessively, the untransformed austenite is reduced, and a sufficient hard structure cannot be obtained.
[0083] In addition, after primary cooling, secondary cooling is performed at an average cooling rate of 700 to 500 ° C from 5.0 to 200 ° C / s. Due to this secondary cooling, the transformation from austenite to ferrite after annealing proceeds safely. If cooling at an average cooling rate of 1 ° C / s to 10.0 ° C / s similar to primary cooling from the region of temperatures exceeding 700 ° C, the ferrite phase is insufficiently formed and the ductility of the high-grade steel sheet resistance cannot be guaranteed.
[0084] In the production method of the present invention, the steel sheet that has been treated to cool in the two steps above is kept at a temperature of 350 to 450 ° C for a time of 30 to 1000 seconds. If the holding temperature at that time is less than 350 ° C, fine iron-based carbides are formed and the concentration of C in the austenite phase does not proceed resulting in an unstable austenite phase. If the retention time exceeds 450 ° C, the limit of the solid solution of C in the austenite phase becomes smaller and C becomes saturated
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27/69 even in a small amount, then the C concentration does not proceed resulting in an unstable austenite phase.
[0085] If the retention time is less than 30 seconds, the transformation of the bainite does not proceed sufficiently, the amount of C (carbon) that is discharged from the bainite phase to the austenite phase is small, the concentration of C in the phase austenite becomes insufficient, and an unstable austenite phase results. If the retention time exceeds 1000 seconds, crude iron-based carbides begin to form and the concentration of C in austenite, on the contrary, drops, then an unstable austenite phase results.
[0086] Furthermore, in the annealing process of the present invention, as shown in FIG. 1 A, when cooling from the maximum heating temperature to room temperature, the steel is reheated from point Bs (temperature of beginning of transformation into bainite) or less than 500 ° C to 500 ° C or more at least one time and is reheated from point Ms or less than 350 ° C to 350 ° C or more at least once. By performing the reheat treatment for such two types of conditions, it is possible to make the austenite phase that has internal defects and easily transform into other structures in the untransformed residual austenite phase, that is, the unstable austenite phase, preferably it is transformed and obtains a bainite phase, a bainitic ferrite phase, or a tempered martensite phase.
[0087] Note that, for example, as shown in FIG. 1B, even if it has cooled down to the point Ms or less than 350 ° C, and then reheated to 500 ° C or more, it is considered that reheating from the point Ms or less than 350 ° C to 350 ° C or more and reheating from point Bs or less than 500 ° C to 500 ° C or more were performed respectively. Such a reheat treatment pattern can also be performed.
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28/69 [0088] In addition, it is possible to maintain steel at the above-mentioned temperature range of 350 to 450 ° C between reheating from the point Ms or less than 350 ° C to 350 ° C or more and reheating from from point Bs or less than 500 ° C to 500 ° C or more.
[0089] The Bs point (temperature of initiation of transformation into bainite) can be calculated by the following formula:
Bs (° C) = 820-290C / (1-VF) -37Si-90Mn-65Cr-50Ni + 70Al [0090] In the above formula, VF is the volume fraction of ferrite, while C, Mn, Cr, Ni, Al, and Si are the addition amounts of these elements (% by mass).
[0091] The Ms point (starting temperature of transformation into martensite) can be calculated using the following formula:
Ms (° C) = 541-474C / (1-VF) -15Si-35Mn-17Cr-17Ni + 19Al [0092] In the above formula, VF is the volume fraction of ferrite, while C, Si, Mn, Cr, Ni, and Al are the addition amounts of these elements (% by mass).
[0093] Note that it is difficult to directly measure the volume fraction of the ferrite phase during the production of the high-strength steel sheet, so in the present invention, a small hair from the cold-rolled steel sheet is cut before passing the sheet through the continuous annealing line this small part is annealed by the same temperature history as if it is passed through the continuous annealing line, the change in the volume of the ferrite phase of the small part is measured, the result is used to calculate a numerical value, and that the value is used as a fraction of the VF volume of the ferrite. This measurement can be performed using the result of the first measurement operation when steel sheet is produced under the same conditions. The value does not have to be measured each time. The measurement is performed again when the production conditions change greatly. Of course, it is also possible to observe the
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29/69 microstructure of the steel sheet actually produced and feedback the production results next time, etc.
[0094] In the reheating mentioned above from point Bs or less than 500 ° C to 500 ° C or more, the starting temperature is made point Bs or less than 500 ° C in order to cause the formation of bainite nuclei to consume defects in austenite. The reheat temperature was made 500 ° C or more in order to deactivate the transformation cores and avoid the formation of iron-based carbides induced by the transformation that proceeds excessively in the high temperature region.
[0095] In the reheating mentioned above from point Ms or less than 350 ° C to 350 ° C or more, the starting temperature is made point Ms or less than 350 ° C in order to cause the formation of martensite nuclei to consume defects in austenite. The reheat temperature was made 350 ° C or more in order to avoid the formation of fine iron-based carbides that obstruct the concentration of C in the austenite, martensite and / or bainite phase due to being allowed to stay below 350 ° C.
[0096] The reason why performing the two-stage reheating mentioned above in different temperature regions results in the residual austenite phase visibly increasing is not completely clear, but it is believed that the bainite cores and the martensite cores consume different types of respectively. defects. [0097] Due to the above processes, defects that may form starting points of transformation into martensite that are present in the residual austenite phase are consumed, only the austenite phase with its highest degree of cleanliness remains selectively, and an extremely stable residual austenite phase is obtained. As a result, a high-strength steel sheet is obtained that has high ductility and flange
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30/69 excellent in forming capacity.
[0098] The annealed steel sheet can be cold rolled by about 0.03 to 0.80% in order to correct the shape. At that time, if the rate of cold rolling after annealing is very high, the soft ferrite phase will be hardened at work and the ductility will deteriorate greatly, then the rolling rate is preferably done in the above range.
[0099] The annealed steel sheet can be electrolytically galvanized to obtain high strength galvanized steel sheet. In addition, the annealed steel sheet can be hot dip galvanized to obtain high strength galvanized steel sheet. In this case, for example, it is possible to cool from the maximum heating temperature to room temperature in the annealing process, for example, up to 500 ° C, apply another annealing, and then dip in a zinc ring for hot dip galvanizing. .
[00100] In addition, during secondary cooling during the above annealing treatment and while retaining between 350 and 450 ° C or after retaining and 350 to 450 ° C, the steel sheet can be dipped in a galvanizing bath to produce high strength galvanized steel sheet.
[00101] After hot-dip galvanizing, it is also possible to treat the coating layer on the surface of the steel sheet to bond it at a temperature of 470 to 650 ° C. Performing such a bonding treatment, a Zn-Fe alloy obtained by the galvanized layer being bonded is formed on the surface, and a high strength galvanized steel sheet is obtained which is excellent in preventing rust.
[00102] This heating in the bonding treatment can be performed instead of the reheating from point Bs or less than
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500 ° C to 500 ° C or more or from the Ms point or less than 350 ° C to 350 ° C or more.
[00103] Performing the coating treatment, to improve the adhesion of the coating, for example, it is possible to coat the steel sheet before the annealing process by the coating comprised of one or more elements selected from Ni, Cu, Co, and Fe. By carrying out such coating treatment by this method, a high-strength galvanized steel sheet is obtained which is formed with a galvanized layer on its surface, has high ductility and flanging capacity in the stretch, and has excellent forming capacity .
[00104] The high-strength steel sheet on whose surface a galvanized layer is formed can also be formed with a film comprised of a P oxide and / or a composite oxide containing P.
Examples [00105] The high strength steel sheet and the high strength galvanized steel sheet which are excellent in forming capacity and the production methods of the same invention will be explained more specifically below using examples. The present invention is, of course, not limited to the following examples and can be changed accordingly in a range capable of being compatible with the essence of the present invention. These are all included in the technical scope of the present invention.
[00106] Plates that have the chemical ingredients (compositions) from A to AG that are shown in Tables 1 and 2 were cast, then immediately after casting they were hot rolled, cooled, coiled, and pickled under the conditions shown in Tables 3 to 5. After this, experiments 5, 14, 19, 24, 29, 34, 39, 44, 49, 54, 59, 98, 102, and 119 left the steel plates
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32/69 hot rolled in the state they were in, while the other experiments cold rolled them under the conditions that are described in Tables 3 to 6 after blasting. After that, an annealing process was applied under the conditions that are shown in Tables 7 to 14 to obtain the steel sheets from Experiments 1 to 127.
abela 1
Experience CC Si Mn P s Al N O % inpasta % inpasta % inpasta % inpasta % inpasta % inpasta % inpasta % inpasta THE 0.107 1.33 1.56 0.020 0.0038 0.043 0.0035 0.0006 B 0.193 1.97 2.49 0.014 0.0009 0.027 0.0021 0.0016 Ç 0.107 0.99 2.02 0.017 0.0024 0.038 0.0030 0.0025 D 0.247 1.14 1.92 0.019 0.0034 0.005 0.0050 0.0029 AND 0.191 1.05 1.41 0.015 0.0029 0.067 0.0030 0.0011 F 0.133 1.89 1.92 0.010 0.0046 0.038 0.0041 0.0022 G 0.203 1.02 1.51 0.014 0.0052 0.073 0.0024 0.0015 H 0.182 0.75 1.87 0.012 0.0037 0.263 0.0037 0.0019 I 0.084 1.51 2.79 0.018 0.0031 0.123 0.0013 0.0020 J 0.260 0.71 2.20 0.019 0.0014 0.302 0.0040 0.0025 K 0.199 1.19 1.89 0.018 0.0027 0.041 0.0060 0.0004 L 0.094 0.90 1.85 0.014 0.0034 0.056 0.0051 0.0013 M 0.183 2.00 1.99 0.007 0.0018 0.045 0.0041 0.0016 N 0.170 1.66 2.59 0.020 0.0008 0.015 0.0037 0.0016 O 0.140 0.74 1.45 0.013 0.0043 0.598 0.0055 0.0004 P 0.099 0.98 1.89 0.020 0.0007 0.044 0.0034 0.0006 Q 0.230 1.24 1.45 0.016 0.0010 0.068 0.0054 0.0028 R 0.119 1.39 2.27 0.016 0.0019 0.031 0.0060 0.0016 s 0.225 1.80 1.52 0.014 0.0042 0.032 0.0029 0.0011 T 0.142 0.99 2.17 0.011 0.0046 0.068 0.0021 0.0011 U 0.194 1.24 1.45 0.011 0.0015 0.053 0.0044 0.0019 V 0.133 2.27 2.55 0.017 0.0051 0.071 0.0056 0.0023 W 0.090 1.44 1.68 0.016 0.0044 0.054 0.0020 0.0007 X 0.101 1.95 1.54 0.009 0.0025 0.062 0.0058 0.0007 Y 0.114 1.62 2.70 0.010 0.0034 0.071 0.0020 0.0013 Z 0.150 1.06 3.16 0.010 0.0036 0.055 0.0018 0.0029 AA 0.015 1.05 2.00 0.013 0.0022 0.027 0.0035 0.0014 AB 0.097 0.06 1.97 0.012 0.0022 0.027 0.0032 0.0008 B.C 0.101 1.05 0.52 0.015 0.0021 0.033 0.0033 0.0014 AD 0.093 1.68 2.67 0.002 0.0013 0.033 0.0076 0.0009 AE 0.152 0.75 2.07 0.013 0.0018 0.065 0.0015 0.0005 AF 0.148 1.72 1.55 0.007 0.0025 0.059 0.0080 0.0014 AG 0.209 0.89 2.50 0.007 0.0036 0.039 0.0057 0.0008
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Table 2
Experienceco You Nb B Cr Ni Ass Mo V Here Ce Mg Zr Hf REM % inpasta % inpasta % inpasta % inpasta % inpasta % inpasta % inpasta % inpasta % inpasta % inpasta % inpasta % inpasta % inpasta % inpasta THE Ex. Inv. B Ex. Inv. Ç Ex. Inv. D Ex. Inv. AND 0.044 Ex. Inv. F 0.022 Ex. Inv. G 0.0019 Ex. Inv. H 0.49 Ex. Inv. I 0.0020 Ex. Inv. J 0.25 Ex. Inv. K 0.105 Ex. Inv. L 0.023 0.013 0.0026 0.39 0.11 0.0032 0.0010 Ex. Inv. M 0.65 Ex. Inv. N 0.24 Ex. Inv. O 1.00 0.60 Ex. Inv. P 0.0025 Ex. Inv. Q 0.0017 Ex. Inv. R 0.0019 Ex. Inv. s 0.0025 Ex. Inv. T 0.0021 Ex. Inv. U 0.069 0.0015 Ex. Inv. V 0.005 0.035 0.23 0.0019Ex. Inv.
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Ta Bela 2 (continued)
W 0.0009 0.0024 Ex. Inv. X 0.67 0.18 Ex. Inv. Y Ex. Inv. Z Ex. Inv. AA Ex. Comp. AB Ex. Comp. B.C Ex. Comp. AD Ex. Inv. AE Ex. Inv. AF Ex. Inv. AG Ex. Inv.
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Table 3
Experiencedence Ingredientschemicals Temp. heating plate. Transformation point Ar3 Temp. termination of hot rolling Temp. coil nto Cold rolling rate ° C ° C ° C ° C % 1 THE 1265 769 915 584 52 Ex. Inv. 2 THE 1215 769 901 600 52 Ex. Inv. 3 THE 1185 769 952 612 52 Ex. Inv. 4 THE 1265 769 952 583 52 Ex. Inv. 5 THE 1225 769 926 562 0 Ex. Inv. 6 B 1195 676 943 618 40 Ex. Inv. 7 B 1170 676 910 638 40 Ex. Inv. 8 B 1240 676 925 567 40 Ex. Inv. 9 B 1185 676 929 528 40 Ex. Inv. 10 Ç 1205 715 912 632 52 Ex. Inv. 11 Ç 1200 715 900 671 52 Ex. Inv. 12 Ç 1175 715 892 695 52 Ex. Inv. 13 Ç 1205 715 885 614 52 Ex. Inv. 14 Ç 1245 715 923 605 0 Ex. Inv. 15 D 1190 682 935 660 52 Ex. Inv. 16 D 1275 682 904 546 52 Ex. Inv. 17 D 1235 682 930 556 52 Ex. Inv. 18 D 1250 682 949 613 52 Ex. Inv. 19 D 1195 682 905 568 0 Ex. Inv. 20 AND 1225 747 913 598 38 Ex. Inv. 21 AND 1240 747 908 682 38 Ex. Inv. 22 AND 1240 747 898 563 67 Ex. Inv. 23 AND 1245 747 908 645 67 Ex. Inv. 24 AND 1270 747 892 620 0 Ex. Inv. 25 F 1180 745 944 652 50 Ex. Inv. 26 F 1230 745 893 639 50 Ex. Inv. 27 F 1215 745 928 542 50 Ex. Inv. 28 F 1215 745 894 687 50 Ex.Comp. 29 F 1210 745 943 577 0 Ex. Inv. 30 G 1170 734 939 681 52 Ex. Inv. 31 G 1180 734 933 619 52 Ex. Inv. 32 G 1200 734 893 661 52 Ex.comp. 33 G 1230 734 917 594 52 Ex. Inv. 34 G 1255 734 931 594 0 Ex. Inv. 35 H 1235 686 890 643 38 Ex. Inv.
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Table 4
Experiencedence Chemical ingredient Temp. plate heating Ar3 transformation point Temp. termination of hot rolling Temp. coil nto Cold rolling rate ° C ° C ° C ° C % 36 H 1240 686 886 554 38 Ex. Inv. 37 H 1225 686 942 572 38 Ex. Comp. 38 H 1245 686 929 557 38 Ex. Inv. 39 H 1215 686 905 570 0 Ex. Inv. 40 I 1205 673 885 528 68 Ex. Inv. 41 I 1175 673 951 643 68 Ex. Inv. 42 I 1205 673 926 559 68 Ex. Comp. 43 I 1265 673 953 566 68 Ex. Inv. 44 I 1235 673 910 615 0 Ex. Inv. 45 J 1265 642 949 612 36 Ex. Inv. 46 J 1215 642 938 618 36 Ex. Inv. 47 J 1250 642 898 638 36 Ex. Comp. 48 J 1295 642 856 677 52 Ex. Inv. 49 J 1215 642 933 588 0 Ex. Inv. 50 K 1205 704 930 658 71 Ex. Inv. 51 K 1230 704 930 615 71 Ex. Inv. 52 K 1195 704 942 672 71 Ex. Comp. 53 K 1265 704 914 611 71 Ex. Inv. 54 K 1240 704 950 597 0 Ex. Inv. 55 L 1190 710 919 616 50 Ex. Inv. 56 L 1190 710 950 669 50 Ex. Inv. 57 L 1270 710 902 693 50 Ex. Comp. 58 L 1200 710 891 679 50 Ex. Inv. 59 L 1230 710 924 582 0 Ex. Inv. 60 M 1270 697 944 660 52 Ex. Inv. 61 M 1180 697 931 581 52 Ex. Inv. 62 M 1255 697 883 569 52 Ex. Comp. 63 M 1245 697 945 605 52 Ex. Inv. 64 N 1185 652 933 675 52 Ex. Inv. 65 N 1225 652 895 580 52 Ex. Inv. 66 N 1265 652 925 628 52 Ex. Comp. 67 N 1220 652 914 681 52 Ex. Inv. 68 O 1225 704 949 613 52 Ex. Inv. 69 O 1255 704 877 690 52 Ex. Inv. 70 O 1220 704 903 671 52 Ex. Comp.
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Table 5
Experiencedence Chemical ingredient Temp. heating plate. Ar3 transformation point Temp. termination of hot rolling Temp. coil nto Cold rolling rate ° C ° C ° C ° C % 71 O 1215 704 915 684 52 Ex. Inv. 72 P 1230 730 932 609 52 Ex. Inv. 73 P 1180 730 923 603 52 Ex. Inv. 74 P 1230 730 903 639 52 Ex. Comp. 75 P 1215 730 927 614 52 Ex. Inv. 76 Q 1180 737 890 646 52 Ex. Inv. 77 Q 1270 737 934 671 52 Ex. Inv. 78 Q 1260 737 913 664 52 Ex. Comp. 79 Q 1280 737 947 591 52 Ex. Inv. 80 R 1190 701 909 642 40 Ex. Inv. 81 R 1245 701 907 629 40 Ex. Inv. 82 R 1205 701 886 568 52 Ex. Comp. 83 R 1210 701 924 602 52 Ex. Inv. 84 s 1215 749 900 648 52 Ex. Inv. 85 s 1180 749 918 573 52 Ex. Inv. 86 s 1210 749 931 578 52 Ex. Inv. 87 s 1265 749 920 589 52 Ex. Inv. 88 T 1245 691 942 625 47 Ex. Inv. 89 T 1275 691 889 652 47 Ex. Inv. 90 T 1275 691 907 585 47 Ex. Inv. 91 T 1230 691 897 558 47 Ex. Inv. 92 U 1225 748 904 551 67 Ex. Inv. 93 U 1190 748 904 608 67 Ex. Inv. 94 U 1205 748 897 591 52 Ex. Inv. 95 U 1275 748 930 607 52 Ex. Inv. 96 V 1185 691 909 678 52 Ex. Inv. 97 V 1200 691 899 645 52 Ex. Inv. 98 V 1215 691 901 650 0 Ex. Inv. 99 V 1230 691 917 582 52 Ex. Inv. 100 W 1260 768 888 664 52 Ex. Inv. 101 W 1190 768 907 657 52 Ex. Inv. 102 W 1195 768 921 564 0 Ex. Inv. 103 W 1280 768 914 606 52 Ex. Inv. 104 X 1235 755 910 634 52 Ex. Inv. 105 X 1275 755 952 604 52 Ex. Inv.
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Tabe to 6 Experiencedence Ingredienteschemicals Temp. heating plate Transformation point Ar3 Temp. end ofhot rolling Temp. coil nto Cold rolling rate ° C ° C ° C ° C % 106 X 1210 755 900 621 52 Ex. Inv. 107 X 1280 755 939 616 52 Ex. Inv. 108 Y 1200 673 886 673 67 Ex. Inv. 109 Y 1185 673 925 652 67 Ex. Inv. 110 Y 1175 673 940 673 43 Ex. Inv. 111 Y 1185 673 953 563 43 Ex. Inv. 112 Z 1225 599 929 643 52 Ex. Inv. 113 Z 1185 599 915 694 52 Ex. Inv. 114 Z 1220 599 902 683 52 Ex. Inv. 115 Z 1275 599 735 666 52 Ex. Comp. 116 AA 1190 748 935 623 52 Ex. Comp. 117 AB 1205 692 889 622 52 Ex. Comp. 118 B.C 1175 857 894 660 52 Ex. Comp. 119 B 1210 676 925 566 0 Ex. Inv. 120 AD 1200 682 866 588 50 Ex. Inv. 121 AD 1225 682 903 600 50 Ex. Inv. 122 AE 1230 689 889 601 50 Ex. Inv. 123 AE 1220 689 887 611 50 Ex. Inv. 124 AF 1220 770 894 621 50 Ex. Inv. 125 AF 1215 770 922 588 50 Ex. Inv. 126 AG 1205 634 902 599 50 Ex. Inv. 127 AG 1210 634 892 591 50 Ex. Inv.
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Table 7
Experienced Ingredients Kind of Heating process Firstprocessinwarm upnto Secondprocessinwarm upnto ence chemicals steel Heating rate Temp, maximum heating Average cooling rate Average cooling rate ° C / s ° C ° C / s ° C / s 1 THE CR 0.3 920 3.3 34 Ex. Inv. 2 THE CR 0.3 812 3.1 32 Ex. Inv. 3 THE GA 0.3 816 3.1 28 Ex. Inv. 4 THE GI 0.3 821 3.4 29 Ex. Inv. 5 THE HR-GA 0.3 812 3.3 33 Ex. Inv. 6 B CR 0.3 819 1.7 27 Ex. Inv. 7 B CR 0.3 825 1.6 28 Ex. Inv. 8 B CR 0.3 826 1.5 31 Ex. Inv. 9 B GA 0.3 823 2.5 27 Ex. Inv. 10 Ç CR 0.5 846 2.5 13 Ex. Inv. 11 Ç CR 0.5 836 2.6 11 Ex. Inv. 12 Ç CR 15 831 3.2 11 Ex. Inv. 13 Ç EG 0.5 845 3.4 10 Ex. Inv. 14 Ç HR 0.4 845 3.1 13 Ex. Inv. 15 D CR 0.7 793 6.2 10 Ex. Inv. 16 D CR 0.7 782 4.5 10 Ex. Inv. 17 D CR 8 781 3.6 8 Ex. Inv. 18 D GI 0.7 786 4.4 10 Ex. Inv. 19 D HR 0.7 784 3.7 8 Ex. Inv. 20 AND CR 0.7 822 2.6 7 Ex. Inv. 21 AND CR 0.7 829 3.1 12 Ex. Inv. 22 AND GA 0.7 823 2.5 8 Ex. Inv. 23 AND EG 0.7 821 2.5 12 Ex. Inv. 24 AND HR-GA 0.7 816 2.6 10 Ex. Inv. 25 F CR 0.7 834 2.5 8 Ex. Inv. 26 F CR 0.7 898 3.5 7 Ex. Inv. 27 F CR 0.7 892 2.9 46 Ex. Inv. 28 F CR 0.7 1076 2.7 52 Ex. Comp. 29 F HR 0.7 898 2.7 55 Ex. Inv. 30 G CR 0.5 793 3.3 31 Ex. Inv. 31 G CR 0.5 789 2.8 35 Ex. Inv. 32 G CR 0.5 730 3.2 32 Ex. Comp. 33 G EG 0.5 783 2.7 30 Ex. Inv. 34 G HR-GA 0.5 800 3.5 30 Ex. Inv. 35 H CR 0.5 780 4.9 33 Ex. Inv.
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Table 8
Experienced Ingredients Kind of Heating process Firstprocessinwarm upnto Secondprocessinheatingto ence chemicals steel Heating rate Temp, maximum heating Average cooling rate Average cooling rate ° C / s ° C ° C / s ° C / s 36 H CR 0.5 889 5.3 31 Ex. Inv. 37 H CR 0.5 886 31 30 Ex. Comp. 38 H GA 0.5 788 5.4 30 Ex. Inv. 39 H HR 0.5 790 2.6 33 Ex. Inv. 40 I CR 0.5 817 3.1 26 Ex. Inv. 41 I CR 0.6 817 3.2 34 Ex. Inv. 42 I CR 0.5 818 02 33 Ex. Comp. 43 I GI 0.5 811 2.5 35 Ex. Inv. 44 I HR-GA 0.5 828 3.5 30 Ex. Inv. 45 J CR 0.4 840 2.5 34 Ex. Inv. 46 J CR 0.4 835 3.3 102 Ex. Inv. 47 J CR 0.4 856 3.6 1 Ex. Comp. 48 J GI 0.4 835 2.4 33 Ex. Inv. 49 J HR-GA 0.4 846 2.7 31 Ex. Inv. 50 K CR 0.5 810 3.3 59 Ex. Inv. 51 K CR 0.5 793 2.7 65 Ex. Inv. 52 K CR 0.5 804 2.7 57 Ex. Comp. 53 K GI 0.5 796 3.1 61 Ex. Inv. 54 K HR-GA 0.5 799 3.1 63 Ex. Inv. 55 L CR 0.4 821 2.9 56 Ex. Inv. 56 L CR 0.4 837 2.9 61 Ex. Inv. 57 L CR 0.4 828 3.5 58 Ex. Comp. 58 L GI 0.4 837 2.8 66 Ex. Inv. 59 L HR-GA 0.4 826 3.1 53 Ex. Inv. 60 M CR 0.4 829 3.0 57 Ex. Inv. 61 M CR 0.4 824 3.5 11 Ex. Inv. 62 M CR 0.4 823 3.4 59 Ex. Comp. 63 M GA 0.4 815 2.7 64 Ex. Inv. 64 N CR 0.4 827 3.0 27 Ex. Inv. 65 N CR 0.4 821 3.1 31 Ex. Inv. 66 N CR 0.4 810 3.5 29 Ex. Comp. 67 N GI 0.4 818 2.6 31 Ex. Inv. 68 O CR 0.5 953 3.8 8 Ex. Inv. 69 O CR 0.5 943 3.3 30 Ex. Inv. 70 O CR 0.5 944 3.7 32 Ex. Comp.
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Table 9
Experiencedence Ingredientschemicals Steel type Heating process Firstprocessinheatingto Secondprocessinheatingto Heating rate Temp, maximum heating Average cooling rate Average cooling rate ° C / s ° C ° C / s ° C / s 71 O GA 0.5 939 2.7 41 Ex. Inv. 72 P CR 0.4 849 7.8 27 Ex. Inv. 73 P CR 0.3 838 2.6 30 Ex. Inv. 74 P CR 0.4 842 2.9 33 Ex. Comp. 75 P GA 0.4 841 2.6 8 Ex. Inv. 76 Q CR 0.4 794 2.8 28 Ex. Inv. 77 Q CR 0.4 801 3.4 30 Ex. Inv. 78 Q CR 0.4 800 2.7 26 Ex. Comp. 79 Q GA 0.4 806 2.8 29 Ex. Inv. 80 R CR 0.4 817 3.2 27 Ex. Inv. 81 R CR 0.4 803 3.3 30 Ex. Inv. 82 R CR 0.4 800 2.6 30 Ex. Comp. 83 R GI 0.4 807 2.7 33 Ex. Inv. 84 s CR 0.4 798 1.9 27 Ex. Inv. 85 s CR 0.4 806 1.8 128 Ex. Inv. 86 s GA 0.4 801 2.4 35 Ex. Inv. 87 s GI 0.4 804 2.1 28 Ex. Inv. 88 T CR 0.4 835 2.1 32 Ex. Inv. 89 T CR 0.4 820 1.6 34 Ex. Inv. 90 T GA 0.5 826 2.4 32 Ex. Inv. 91 T EG 0.4 833 1.9 29 Ex. Inv. 92 U CR 0.4 785 4.8 28 Ex. Inv. 93 U CR 0.4 771 5.4 32 Ex. Inv. 94 U GA 0.4 787 4.7 26 Ex. Inv. 95 U EG 0.4 775 5.2 27 Ex. Inv. 96 V CR 0.4 865 5.0 47 Ex. Inv. 97 V CR 0.4 880 5.1 49 Ex. Inv. 98 V HR 0.4 872 4.8 52 Ex. Inv. 99 V GA 0.4 867 5.2 54 Ex. Inv. 100 W CR 0.2 882 5.1 50 Ex. Inv. 101 W CR 0.2 796 5.3 51 Ex. Inv. 102 W HR-GA 0.2 793 4.6 47 Ex. Inv. 103 W GI 0.2 804 5.1 54 Ex. Inv. 104 X CR 0.5 852 5.4 47 Ex. Inv. 105 X CR 0.5 847 4.9 53 Ex. Inv.
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Table 10
Experiencedence Ingredientschemicals Steel type Heating process Firstprocessinheatingto Secondprocessinheatingto Heating rate Temp,maximuminwarm upnto Average cooling rateto Average cooling rateto ° C / s ° C ° C / s ° C / s 106 X CR 17 853 4.6 53 Ex. Inv. 107 X EG 0.5 857 5.0 47 Ex. Inv. 108 Y CR 0.5 810 4.7 50 Ex. Inv. 109 Y CR 0.5 791 3.1 46 Ex. Inv. 110 Y GA 0.5 803 2.5 50 Ex. Inv. 111 Y CR 18 807 3.5 43 Ex. Inv. 112 Z CR 0.5 759 2.8 51 Ex. Inv. 113 Z CR 0.5 759 2.7 48 Ex. Inv. 114 Z EG 0.5 747 3.4 51 Ex. Inv. 115 Z CR 0.5 757 2.8 28 Ex. Comp. 116 AA CR 0.5 799 3.1 30 Ex. Comp. 117 AB CR 0.5 795 3.1 27 Ex. Comp. 118 B.C CR 0.5 790 3.3 30 Ex. Comp. 119 B HR 0.4 827 1.7 34 Ex. Inv. 120 AD CR 0.4 819 1.8 26 Ex. Inv. 121 AD GA 0.8 842 2.8 27 Ex. Inv. 122 AE CR 0.7 943 3.1 63 Ex. Inv. 123 AE GA 0.7 846 1.9 24 Ex. Inv. 124 AF CR 0.7 899 2.1 33 Ex. Inv. 125 AF GA 0.7 928 2.2 65 Ex. Inv. 126 AG CR 0.7 793 2.1 68 Ex. Inv. 127 AG GA 0.7 809 2.0 61 Ex. Inv.
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Table 11
Experiencedence Reheat process 1 Reheat process 2 Reheat process 3 Retention process Reheat process 4 Reheat process 5 Connection processes Temp. beginning oftransforappleinbainite(Bs) Temp.instartgivestransformation inmartensit(Ms) Temp.instopofcoolthen Temp.instopofreheatedment Temp.instopofcoolthen Temp.instopofreheatedment Temp.instopofcoolthen Temp.instopofreheatedment TimeinretentionO Temp.instopofcoolthen Temp.instopofreheatedment Temp.instopofcoolthen Temp.instopofreheatedment Temp.inLink ° C ° C ° C ° C ° C ° C s ° C ° C ° C ° C ° C ° C ° C1 464 541 292 360 244 598 412 Ex. Inv. 2 458 525 335 379 273 318 378 567 346 Ex. Inv. 3 455 520 322 397 240 520 559 370 Ex. Inv. 4 456 547 328 397 253 560 360 Ex. Inv. 5 460 514 304 414 254 514 571 341 Ex. Inv. 6 429 527 273 417 236 440 279 Ex. Inv. 7 411 520 421 518 254 421 279 423 518 436 280 Ex. Inv. 8 441 516 267 392 243 450 299 Ex. Inv. 9 422 534 234 373 56 477 434 271 Ex. Inv. 10 483 513 311 385 279 570 402 Ex. Inv. 11 490 548 291 421 241 566 403 Ex. Inv. 12 312 412 218 397 505 568 387 Ex. Inv. 13 495 510 316 379 215 572 395 Ex. Inv. 14 459 520 331 370 237 570 392 Ex. Inv. 15 454 546 283 358 235 504 295 Ex. Inv. 16 245 378 526 318 378 505 280 Ex. Inv. 17 475 536 253 387 260 497 280 Ex. Inv. 18 482 526 263 390 284 502 291 Ex. Inv. 19 476 534 255 362 216 500 284 Ex. Inv. 20 476 547 308 400 54 554 321 Ex. Inv. 21 458 545 305 406 60 565 324 Ex. Inv. 22 489 551 334 400 64 425 520 520 582 345 Ex. Inv.
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Table 11 (continued)
23 484 519 294 369 56 577 334 Ex. Inv. 24 453 526 318 388 71 388 504 504 565 326 Ex. Inv. 25 477 546 314 424 60 510 342 Ex. Inv. 26 464 545 326 359 212 537 368 Ex. Inv. 27 344 383 472 407 511 532 378 Ex. Inv. 28 478 521 336 404 246 545 384 Ex.Comp. 29 471 534 292 416 216 532 371 Ex. Inv. 30 463 531 225 362 64 526 265 Ex. Inv. 31 254 379 267 411 520 545 290 Ex. Inv. 32 483 509 191 366 532 504 219 Ex.Comp. 33 488 505 232 358 210 510 236 Ex. Inv. 34 466 517 483 518 262 374 261 518 523 292 Ex. Inv. 35 463 528 326 414 237 522 331 Ex. Inv.
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Table 12
Experiencedence Reheat process 1 Reheat process 2 Reheat process 3 Processinretention Reheat process 4 Reheat process 5 Connection process Temp.instartgivestransforappleinbainite(Bs) Temp.instartgivestransforappleinmartensita(Ms) Temp.instopofcoolthen Temp.instopofreheatedment Temp.instopofcoolthen Temp.instopofreheatedment Temp.instopofcoolthen Temp.instopofreheatedment Retention time Temp.instopofcoolthen Temp.instopofreheatedment Temp.instopofcoolthen Temp.instopofreheatedment Temp.inLink ° C ° C ° C ° C ° C ° C s ° C ° C ° C ° C ° C ° C ° C 36 488 546 276 419 519 318 378 542 355 Ex. Inv. 37 476 531 331 399 253 563 376 Ex. Comp. 38 445 543 451 501 239 368 257 501 469 264 Ex. Inv. 39 447 504 216 318 378 500 295 Ex. Inv. 40 443 526 338 408 368 464 349 Ex. Inv. 41 452 552 312 422 444 481 356 Ex. Inv. 42 276 387 431 408 517 451 308 Ex.Comp. 43 460 511 315 402 339 473 344 Ex. Inv. 44 454 543 313 369 388 543 479 352 Ex. Inv. 45 482 530 248 409 258 495 260 Ex. Inv. 46 471 533 267 416 255 417 525 319 379 499 267 Ex. Inv. 47 451 502 285 404 287 338 3 Ex. Inv. 48 481 532 280 250 377 506 278 Ex. Inv. 49 492 532 285 355 2245 476 514 290 Ex. Inv. 50 488 545 308 356 357 534 330 Ex. Inv. 51 464 536 232 358 225 471 269 Ex. Inv. 52 - - - - - - 253 - - - - 526 315 Ex. Inv. 53 466 540 289 399 277 503 305 Ex. Inv. 54 478 543 280 386 242 401 522 522 512 292 Ex. Inv. 55 472 552 482 512 297 386 74 553 383 Ex. Inv. 56 480 510 344 363 74 560 391 Ex. Inv.
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Table 12 (continued)
57 440 510 - - - - 225 - - - - 556 384 Ex. Comp. 58 462 527 306 381 217 561 396 Ex. Inv. 59 493 547 311 372 236 406 503 503 566 398 Ex. Inv. 60 441 553 304 361 290 458 307 Ex. Inv. 61 431 529 268 392 256 454 289 Ex. Inv. 62 - - - - 249 394 216 - - - - 437 251 Ex. Comp. 63 437 542 248 381 261 375 559 559 440 269 Ex. Inv. 64 463 539 327 411 316 481 344 Ex. Inv. 65 446 533 296 425 301 470 326 Ex. Inv. 66 420 513 433 508 - - 396 - - - - 454 302 Ex. Comp. 67 427 523 280 419 339 523 455 320 Ex. Inv. 68 494 540 345 367 366 591 370 Ex. Inv. 69 495 506 303 422 304 592 371 Ex. Inv. 70 - - - - 301 385 332 - - 304 396 585 361 Ex. Comp.
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Table 13
Experiencedence Reheat process 1 Reheat process 2 Reheat process 3 Processinretention Reheat process 4 Reheat process 5 Connection process Temp.instartgivestransforappleinbainite(Bs) Temp.instartgivestransforappleinmartensita(Ms) Temp.instopofcoolthen Temp.instopofreheatedment Temp.instopofcoolthen Temp.instopofreheatedment Temp.instopofcoolthen Temp.instopofreheatedment Retention time Temp.instopofcoolthen Temp.instopofreheatedment Temp.instopofcoolthen Temp.instopofreheatedment Temp.inLink ° C ° C ° C ° C ° C ° C s ° C ° C ° C ° C ° C ° C ° C 71 476 526 329 361 299 376 539 537 585 361 Ex. Inv. 72 487 513 308 379 273 585 415 ] Ex. Inv. 73 485 510 247 306 373 582 399 Ex. Inv. 74 469 530 335 397 7 568 395 Ex. Comp. 75 460 504 296 414 228 417 528 528 568 389 Ex. Inv. 76 486 515 473 523 215 414 238 498 249 Ex. Inv. 77 468 513 250 216 371 501 224 Ex. Inv. 78 472 554 250 367 3600 528 269 Ex. Comp. 79 487 545 232 395 269 396 521 521 526 257 Ex. Inv. 80 482 537 342 397 453 511 348 Ex. Inv. 81 487 536 296 417 431 496 330 Ex. Inv. 82 444 534 - - - - 488 440 515 - - 483 334 Ex. Comp. 83 458 527 292 409 492 515 353 Ex. Inv. 84 453 542 189 425 288 472 219 Ex. Inv. 85 489 551 490 520 263 406 509 227 366 504 266 Ex. Inv. 86 481 513 232 414 252 513 480 268 Ex. Inv. 87 454 535 257 400 244 505 281 Ex. Inv. 88 485 535 313 365 255 548 385 Ex. Inv. 89 330 411 210 414 506 318 378 529 348 Ex. Inv. 90 447 517 316 381 264 517 541 369 Ex. Inv. 91 493 505 462 512 291 393 276 332 364 547 380 Ex. Inv.
69 / Z17
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Table 13 (continued)
92 484 529 219 400 147 528 226 Ex. Inv. 93 248 392 131 514 285 Ex. Inv. 94 497 534 459 519 279 384 128 519 544 289 Ex. Inv. 95 458 535 469 504 239 402 125 382 513 258 357 532 271 Ex. Inv. 96 435 507 311 379 622444 322 Ex. Inv. 97 304 376 456 419 509 330 368 459 344 Ex. Inv. 98 427 504 306 364 537 451 337 Ex. Inv. 99 415 522 526 312 379 522 438 321 Ex. Inv. 100 472 527 289 365 61 591 408 Ex. Inv. 101 492 527 451 536 302 362 133 550 330 Ex. Inv. 102 459 504 323 359 534 504 551 354 Ex. Inv. 103 461 524 246 285 353 545 317 Ex. Inv. 104 453 517 288 409 372 521 373 Ex. Inv. 105 336 397 353 453 530 340 373 508 361 Ex. Inv.
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Table 14
Experiencedence Reheat process 1 Reheat process 2 Reheat process 3 Retention process Reheat process 4 Reheat process 5 Connection processes Temp. beginning oftransforappleinbainite(Bs) Temp. beginning oftransforappleinmartensiOK(Ms) Temp.instopofcoolthen Temp.instopofreheatedment Temp.instopofcoolthen Temp.instopofreheatedment Temp.instopofcoolthen Temp.instopofreheatedment TimeinretentionO Temp.instopofcoolthen Temp.instopofreactcementO Temp.instopofchillsment Temp.instopofreheatedment Temp.inLink ° C ° C ° C ° C ° C ° C s ° C ° C ° C ° C ° C ° C ° C 106 468 515 291 415 410 521 371 Ex. Inv. 107 495 552 465 502 309 381 232 441 539 519 362 Ex. Inv. 108 441 523 300 368 783 469 335 Ex. Inv. 109 422 519 309 419 625 449 316 Ex. Inv. 110 429 535 284 378 655 488 457 301 Ex. Inv. 111 441 541 444 518 285 299 378 466 305 Ex. Inv. 112 373 542 200 355 272 384 213 Ex. Inv. 113 373 540 213 422 220 387 245 Ex. Inv. 114 409 550 396 515 270 240 369 412 255 Ex. Inv. 115 399 536 218 409 286 410 252 Ex. Comp. 116 471 506 302 409 232 - - Ex. Comp. 117 477 527 289 377 284 595 401 Ex. Comp. 118 481 527 275 374 228 648 304 Ex. Comp. 119 438 540 275 319 375 449 300 Ex. Inv. 120 454 511 308 375 101 468 338 Ex. Inv. 121 344 379 106 365 503 500 485 366 Ex. Inv. 122 464 526 77 275 382 565 383 Ex. Inv. 123 357 399 100 380 519 517 558 373 Ex. Inv. 124 484 532 298 405 98 575 387 Ex. Inv. 125 343 370 87 361 509 503 574 385 Ex. Inv. 126 473 536 73 241 357 470 286 Ex. Inv. 127 297 380 100 349 508 498 487 314 Ex. Inv.
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50/69 [00107] In the annealing process, the steel sheets were initially heated to the maximum heating temperatures described in Tables 7 to 10 by the average heating rates between (maximum heating temperature - 20 ° C) to the temperature maximum heating of the average heating rates described in Tables 7 to 10. Next, in the first cooling process, (primary cooling), from the maximum heating temperature to 700 ° C, they were cooled by the average cooling rates described in the Tables 7 to 10. In addition, in the second cooling process, (secondary cooling) from 700 ° C to 500 ° C, they were cooled by the average cooling rates described in Tables 7 to 10.
[00108] After this, the steel sheets were reheated from Bs or 480 ° C or less to 500 ° C or more 1 to 3 times (reheating processes 1, 2 and 4) and, in addition, have been reheated since the point Ms or 350 ° C or less up to 350 ° C or more 1 or 2 times (reheating processes 3 and 5).
[00109] After the reheating process 3, the steel sheets were kept in the range of 300 to 450 ° C exactly for the times described in Tables 11 to 14 and then were treated by the reheating processes 4 and 5 and cooled to room temperature . [00110] After being cooled to room temperature, in Experiments 6 to 49, the steel sheets were cold rolled by 0.15%, in Experiments 60 to 83 the steel sheets were cold rolled by 0.30%, in Experiment 89 the steel sheet was cold rolled by 1.50%, in Experiment 93 the steel sheet was cold rolled by 1.00%, and in Experiments 96 to 118 and 120 to 127 the steel sheets were rolled cold by 0.25%.
[00111] The types of steel in the experiments are shown in the tables as cold rolled steel sheet (CR), cold rolled steel sheet
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51/69 hot dip (HR), electrolytically galvanized steel sheet (EG), hot dip galvanized steel sheet (GI), hot dip galvanized steel sheet (GA), and hot dip galvanized steel sheet hot rolled (HR-GA) (same in the tables shown below).
[00112] Experiments 13, 23, 33, 91.95, 107, and 114 are examples in which steel sheets were galvanized after the annealing process to obtain galvanized steel sheets (EG).
[00113] Experiments 4, 18, 43, 83, and 87 are examples in which after the second cooling process, the steel sheets are immersed in a galvanizing bath until the retention treatment in the range of 350 to 450 ° C to obtain hot-dip galvanized steel sheets (GI).
[00114] Experiments 48, 53, 58, 98, and 103 are examples in which after the retention treatment in the range of 300 to 450 ° C, the steel sheets are dipped in a galvanizing bath, and then are cooled down to at room temperature to obtain hot-dip galvanized steel sheets (GI).
[00115] Experiments 3, 5, 9, 34, 38, 44, 49, 67, 86, 90, 94, 99, 102, and 110 are examples in which after the second cooling process, the steel sheets are dipped in a galvanizing bath until it retains in the range of 350 to 450 ° C and is then treated for bonding at the temperatures described to obtain galvannealed steel sheets (GA).
[00116] Experiments 22, 24, 54, 59, 63, 71.75, 79, 121, 123, 125, and 127 are examples in which after the retention treatment in the range of 300 to 450 ° C the steel sheets they are dipped in a galvanizing bath and treated for bonding at the temperatures described to obtain hot-dip galvanized steel sheets (GA).
[00117] Experiments 9, 63, and 90 are examples in which
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52/69 surfaces of the coating layers are given films comprised of compound oxide based on P.
[00118] Tables 15 to 18 give the results of the analysis of the microstructures of the steel sheets of experiments 1a 127. In the microstructure fractions, the quantities of residual austenite (residual γ) were measured by x-ray diffraction in planes parallel to the plate thickness to 1/4 of the thickness. The remainder gives the results of measuring the microstructure fractions in the range of 1/8 of the thickness to 3/8 of the thickness. The cross sections of the sheet thickness parallel to the lamination direction were cut, polished to mirror surfaces, etched by Nital, and then examined using a field-scanning electron microscope (FE-SEM).
Table 15
Experiencedence Ingredientschemicals Steel type Results of microstructure observation Volume fraction F B BF TM M γresidual Others % % % % % % % 1 THE CR 12 6 41 32 0 8 1 Ex. Inv. 2 THE CR 55 5 17 18 1 4 0 Ex. Inv. 3 THE GA 54 6 25 10 0 5 0 Ex. Inv. 4 THE G I 54 18 9 15 1 3 0 Ex. Inv. 5 THE HR-GA 57 3 20 13 0 6 1 Ex. Inv. 6 B CR 36 8 23 21 1 10 1 Ex. Inv. 7 B CR 39 5 17 28 0 11 0 Ex. Inv. 8 B CR 26 4 42 15 0 13 0 Ex. Inv. 9 B GA 41 5 31 8 0 15 0 Ex. Inv. 10 Ç CR 13 11 31 39 0 6 0 Ex. Inv. 11 Ç CR 13 2 42 36 0 7 0 Ex. Inv. 12 Ç CR 27 3 28 36 1 5 0 Ex. Inv. 13 Ç EG 14 5 28 48 0 5 0 Ex. Inv. 14 Ç HR 17 4 50 20 2 5 2 Ex. Inv. 15 D CR 32 1 21 30 0 15 1 Ex. Inv. 16 D CR 33 2 26 28 0 11 0 Ex. Inv. 17 D CR 32 6 18 29 1 13 1 Ex. Inv. 18 D GI 31 2 17 33 0 17 0 Ex. Inv. 19 D HR 32 7 20 22 0 19 0 Ex. Inv. 20 AND CR 43 1 24 20 0 12 0 Ex. Inv. 21 AND CR 38 4 20 30 0 8 0 Ex. Inv. 22 AND GA 31 3 21 25 2 16 2 Ex. Inv. 23 AND EG 39 1 19 29 0 12 0 Ex. Inv. 24 AND HR-GA 42 9 22 15 1 11 0 Ex. Inv. 25 F CR 41 3 18 29 0 9 0 Ex. Inv. 26 F CR 15 0 29 46 0 9 1 Ex. Inv.
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Experiencedence Ingredientschemicals Steel type Results of microstructure observation Volume fraction F B BF TM M γresidual Others % % % % % % % 27 F CR 12 3 51 25 0 9 0 Ex. Inv. 28 F CR 0 23 35 35 0 6 1 Ex. Comp. 29 F HR 14 11 38 30 0 7 0 I Ex. Inv. 30 G CR 56 3 18 9 0 14 0 Ex. Inv. 31 G CR 50 0 22 11 0 17 0 Ex. Inv. 32 G CR 66 0 0 0 0 0 34 Ex. Comp. 33 G EG 55 0 23 10 0 12 0 Ex. Inv. 34 G HR-GA 53 3 13 22 0 8 1 Ex. Inv. 35 H CR 37 7 17 26 0 13 0 Ex. Inv.
Tabe a 16
Experiencedence Ingredienteschemicals Steel type Results of microstructure observation Volume fraction F B BF TM M ^l residual γ Others % % % % % % % 36 H CR 21 7 31 29 0 11 1 Ex. Inv. 37 H CR 0 6 45 39 0 10 0 Ex. Comp. 38 H GA 58 2 12 15 0 13 0 Ex. Inv. 39 H HR 52 3 14 21 0 10 0 Ex. Inv. 40 I CR 50 4 18 23 0 5 0 Ex. Inv. 41 I CR 43 4 22 26 2 3 0 Ex. Inv. 42 I CR 67 18 2 5 0 0 8 Ex. Comp. 43 I GI 46 3 22 20 3 6 0 Ex. Inv. 44 I HR-GA 41 1 37 15 0 3 3 Ex. Inv. 45 J CR 38 7 14 28 0 13 0 Ex. Inv. 46 J CR 36 6 16 26 0 16 0 I Ex. Inv. 47 J CR 73 13 2 5 0 1 6 Ex. Comp. 48 J GI 32 2 17 30 0 19 0 Ex. Inv. 49 J HR-GA 27 10 30 17 0 16 0 Ex. Inv. 50 K CR 28 2 41 14 0 15 0 Ex. Inv. 51 K CR 53 9 18 10 0 10 0 Ex. Inv. 52 K CR 35 0 33 17 3 12 0 Ex. Comp. 53 K GI 42 1 33 13 0 11 0 Ex. Inv. 54 K HR-GA 42 3 17 25 1 11 1 Ex. Inv. 55 L CR 40 13 37 5 0 5 0 Ex. Inv. 56 L CR 26 4 50 15 1 4 0 Ex. Inv. 57 L CR 39 11 36 7 1 6 0 Ex. Comp. 58 L GI 24 5 49 17 0 4 1 Ex. Inv. 59 L HR-GA 26 14 36 20 0 4 0 Ex. Inv. 60 M CR 32 5 36 18 0 9 0 Ex. Inv. 61 M CR 42 5 21 20 0 12 0 Ex. Inv. 62 M CR 49 4 24 7 2 14 0 Ex. Comp. 63 M GA 47 0 19 20 2 12 0 Ex. Inv.
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Experiencedence Ingredienteschemicals Steel type Results of microstructure observation Volume fraction F B BF TM M l γresidual Others % % % % % % % 64 N CR 0 1 55 35 0 9 0 Ex. Inv. 65 N CR 19 4 42 25 1 9 0 Ex. Inv. 66 N CR 39 1 23 22 1 14 0 Ex. Comp. 67 N GA 27 0 44 16 0 13 0 Ex. Inv. 68 O CR 36 1 20 34 2 7 0 Ex. Inv. 69 O CR 35 3 43 13 0 6 0 Ex. Inv. 70 O CR 41 5 33 13 2 6 0 Ex. Comp.
Table 17
Experiencedence Ingredientschemicals Steel type Results of microstructure observation Volume fraction B BF TTM M R γresidual Others % % % % % % % 71 O GA 41 3 33 15 0 8 0 Ex. Inv. 72 P CR 0 5 39 46 1 9 0 Ex. Inv. 73 P CR 18 3 42 28 1 8 0 Ex. Inv. 74 P CR 35 4 31 13 8 9 0. Ex. Comp. 75 P GA 34 2 32 28 0 4 0 Ex. Inv. 76 Q CR 50 5 20 11 0 13 1 Ex. Inv. 77 Q CR 54 1 15 20 0 10 0 Ex. Inv. 78 Q CR 51 1 11 28 0 9 0 Ex. Comp. 79 Q GA 46 0 16 23 0 15 0 Ex. Inv. 80 R CR 36 0 30 25 0 7 2 Ex. Inv. 81 R CR 53 7 15 19 0 6 0 Ex. Inv. 82 R GA 55 4 13 20 2 6 0 Ex. Comp. 83 R GI 41 0 18 29 3 6 3 Ex. Inv. 84 s CR 52 10 13 11 0 14 0 Ex. Inv. 85 s CR 43 8 13 24 0 12 0 Ex. Inv. 86 s GA 50 5 15 17 0 13 0 Ex. Inv. 87 s GI 45 1 20 16 2 15 1 Ex. Inv. 88 T CR 3 4 60 27 1 5 0 Ex. Inv. 89 T CR 37 0 22 33 1 7 0 Ex. Inv. 90 T GA 15 2 35 40 0 7 1 Ex. Inv. 91 T EG 12 1 57 21 0 8 1 Ex. Inv. 92 U CR 57 2 17 9 1 13 1 Ex. Inv. 93 U CR 52 6 23 9 0 10 0 Ex. Inv. 94 U GA 46 5 22 16 0 11 0 Ex. Inv. 95 U EG 53 0 21 17 0 9 0 Ex. Inv. 96 V CR 30 5 42 13 2 7 1 Ex. Inv. 97 V CR 14 5 36 36 1 7 1 Ex. Inv.
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Experiencedence Ingredientschemicals Steel type Results of microstructure observation Volume fraction B BF TTM M R γresidual Others % % % % % % % 98 V GI 15 1 30 44 0 10 0 Ex. Inv. 99 V GA 32 4 28 30 0 6 0 Ex. Inv. 100 W CR 17 11 33 30 1 7 1 Ex. Inv. 101 W CR 68 1 9 18 0 4 0 Ex. Inv. 102 W GA 65 5 9 14 0 6 1 Ex. Inv. 103 W GI 65 1 22 9 0 3 0 Ex. Inv. 104 X CR 38 5 20 28 0 7 2 Ex. Inv. 105 X CR 47 1 27 21 0 4 0 Ex. Inv.
Table 18
Experiencedence Ingredienteschemicals Steel type Results of microstructure observation Volume fraction F B BF TM MM residual γ Others % % % % % % % 106 X CR 38 5 35 15 1 6 0 Ex. Inv. 107 X EG 47 4 26 19 0 3 1 Ex. Inv. 108 Y CR 41 1 31 18 0 8 1 Ex. Inv. 109 Y CR 54 4 29 8 0 5 0 Ex. Inv. 110 Y GA 52 13 15 14 0 6 0 Ex. Inv. 111 Y CR 48 3 19 19 1 10 0 Ex. Inv. 112 Z CR 59 3 23 6 0 9 0 Ex. Inv. 113 Z CR 62 1 13 15 0 9 0 Ex. Inv. 114 Z EG 59 5 10 17 0 9 0 Ex. Inv. 115 Z CR 60 7 10 12 0 9 2 Ex. Comp. 116 AA CR 98 0 0 0 0 0 2 Ex. Comp. 117 AB CR 35 31 8 23 0 0 3 Ex. Comp. 118 B.C CR 72 15 0 9 0 0 4 Ex. Comp. 119 B HR 31 5 34 13 0 17 0 Ex. Inv. 120 AD CR 48 7 24 15 0 6 0 Ex. Inv. 121 AD GA 22 21 37 16 0 4 0 Ex. Inv. 122 AE CR 4 31 33 19 1 11 1 Ex. Inv. 123 AE GA 16 28 38 10 0 8 0 Ex. Inv. 124 AF CR 7 0 31 45 2 13 2 Ex. Inv. 125 AF GA 9 7 43 28 0 12 1 Ex. Inv. 126 AG CR 36 6 23 21 0 14 0 Ex. Inv. 127 AG GA 22 31 22 14 2 9 0 Ex. Inv.
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56/69 [00119] Tables 19 to 22 show the results of measuring the residual austenite fractions and the amounts of the solid C solution in the residual austenite after the deep cooling treatment tests. These were measured by X-ray diffraction in planes parallel to the plate thickness at 1/4 of the thickness. The Msr point was measured by preparing liquid nitrogen (-198 ° C) and cooled ethanol using liquid nitrogen in increments of 20 ° C from 0 ° C to 100 ° C, keeping the steel sheets at those temperatures for 1 hour, then measuring the residual austenite fractions and using the maximum temperatures at which the austenite fractions fall as the Msr points of the residual austenite phase.
Tabe a 19
Experiencedessences Ingredienteschemicals Steel type Transformation temperature of residual γ Msr Point Volume fraction after diving in liquid nitrogen Amount of solid solution 1st 3rd 5th ° C % 1 THE CR <-198 G G G 0.93 Ex. Inv. 2 THE CR <-198 G G G 0.88 Ex. Inv. 3 THE GA <-198 G G G 0.89 Ex. Inv. 4 THE GI <-198 G G G 1.07 Ex. Inv. 5 THE HR-GA <-198 G G G 0.89 Ex. Inv. 6 B CR <-198 G G G 0.95 Ex. Inv. 7 B CR <-198 G G G 1.02 Ex. Inv. 8 B CR <-198 G G G 1.07 Ex. Inv. 9 B GA <-198 G G G 0.96 Ex. Inv. 10 Ç CR <-198 G G G 0.96 Ex. Inv. 11 Ç CR <-198 G G G 0.90 Ex. Inv. 12 Ç CR -100 to -80 P 1.01 Ex. Inv. 13 Ç EG <-198 G G G 1.01 Ex. Inv. 14 Ç HR <-198 G G G 0.99 Ex. Inv. 15 D CR <-198 G G G 0.98 Ex. Inv. 16 D CR <-198 G G G 1.03 Ex. Inv. 17 D CR -100 to -80 P 0.92 Ex. Inv. 18 D GI <-198 G G G 0.88 Ex. Inv. 19 D HR <-198 G G G 0.95 Ex. Inv. 20 AND CR <-198 G G G 0.94 Ex. Inv.
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Experiencedessences Ingredienteschemicals Steel type Transformation temperature of residual γ Msr Point Volume fraction after diving in liquid nitrogen Amount of solid solution 1st 3rd 5th ° C % 21 AND CR <-198 G G G 1.05 Ex. Inv. 22 AND GA <-198 G G G 1.04 Ex. Inv. 23 AND EG <-198 G G G 0.88 Ex. Inv. 24 AND HR-GA <-198 G G G 0.96 Ex. Inv. 25 F CR <-198 G G G 1.01 Ex. Inv. 26 F CR <-198 G G G 1.02 Ex. Inv. 27 F CR <-198 G G G 1.05 Ex. Inv. 28 F CR <-198 G G G 0.97 Ex. Comp. 29 F HR <-198 G G G 0.93 Ex. Inv. 30 G CR <-198 G G G 0.98 Ex. Inv. 31 G CR <-198 G G G 1.07 Ex. Inv. 32 G CR No residual austenite Ex. Comp. 33 G EG <-198 G G G 1.04 Ex. Inv. 34 G HR-GA <-198 G G G 1.06 Ex. Inv. 35 H CR <-198 G G G 0.99 Ex. Inv.
Table 20
Experience Ingredienteschemicals Steel type Transformation temperature of residual γ Msr Point Volume fraction after diving in liquid nitrogen Amount of solid C solution 1st 3rd 5th ° C % 36 H CR <-198 G G G 0.99 Ex. Inv. 37 H CR <-198 G G G 1.06 Ex. Comp. 38 H GA <-198 G G G 0.92 Ex. Inv. 39 H HR <-198 G G G 0.97 Ex. Inv. 40 I CR <-198 G G G 0.91 Ex. Inv. 41 I CR <-198 G G G 0.90 Ex. Inv. 42 I CR No residual austenite Ex. Comp. 43 I GI <-198 G G G 1.03 Ex. Inv. 44 I HR-GA <-198 G G G 1.02 Ex. Inv. 45 J CR <-198 G G G 0.94 Ex. Inv. 46 J CR <-198 G G G 1.00 Ex. Inv. 47 J CR > 0 P 0.98 Ex. Comp. 48 J GI <-198 G G G 0.95 Ex. Inv. 49 J HR-GA <-198 G G G 1.03 Ex. Inv.
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Experience Ingredienteschemicals Steel type Transformation temperature of residual γ Msr Point Volume fraction after diving in liquid nitrogen Amount of solid C solution 1st 3rd 5th ° C % 50 K CR <-198 G G G 1.06 Ex. Inv. 51 K CR <-198 G G G 0.93 Ex. Inv. 52 K CR -40 to -20 P 0.99 Ex. Comp. 53 K GI <-198 G G G 0.88 Ex. Inv. 54 K HR-GA <-198 G G G 1.03 Ex. Inv. 55 L CR <-198 G G G 1.06 Ex. Inv. 56 L CR <-198 G G G 0.95 Ex. Inv. 57 L CR -60 to -40 P 0.98 Ex. Comp. 58 L GI <-198 G G G 0.97 Ex. Inv. 59 L HR-GA <-198 G G G 0.92 Ex. Inv. 60 M CR <-198 G G G 1.01 Ex. Inv. 61 M CR <-198 G G G 1.00 Ex. Inv. 62 M CR -40 to -20 P 0.93 Ex. Comp. 63 M GA <-198 G G G 1.02 Ex. Inv. 64 N CR <-198 G G G 0.96 Ex. Inv. 65 N CR <-198 G G G 0.91 Ex. Inv. 66 N CR -40 to -20 P 0.92 Ex. Comp. 67 N GA <-198 G G G 0.94 Ex. Inv. 68 O CR <-198 G G G 0.99 Ex. Inv. 69 O CR <-198 G G G 0.95 Ex. Inv. 70 O CR -60 to -40 P 0.94 Ex. Comp.
Table 21
Experienceco Ingredientschemicals Steel type Transformation temperature of residual γ Msr Point Volume fraction after diving in liquid nitrogen Amount of solid solution 1st 3rd 5th ° C % 71 O GA <-198 G G G 0.90 Inv. Ex. 72 P CR <-198 G G G 0.93 Inv. Ex. 73 P CR <-198 G G G 1.06 Inv. Ex. 74 P CR -20 to 0 P 0.74 Comp. ex. 75 P GA <-198 G G G 1.02 Inv. Ex. 76 Q CR <-198 G G G 1.04 Inv. Ex. 77 Q CR <-198 G G G 1.02 Inv. Ex. 78 Q CR -40 to -20 P 0.78 Comp. ex.
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Experienceco Ingredientschemicals Steel type Transformation temperature of residual γ Point Ms, Volume fraction after diving in liquid nitrogen Amount of solid solution 1st 3rd 5th ° C % 79 Q GA <-198 G G G 0.91 Inv. Ex. 80 R CR <-198 G G G 1.05 Inv. Ex. 81 R CR <-198 G G G 0.97 Inv. Ex. 82 R GA -40 to -20 P 0.94 Comp. ex. 83 R GI <-198 G G G 1.01 Inv. Ex. 84 s CR <-198 G G G 0.90 Inv. Ex. 85 s CR <-198 G G G 1.02 Inv. Ex. 86 s GA <-198 G G G 0.99 Inv. Ex. 87 s GI <-198 G G G 1.05 Inv. Ex. 88 T CR <-198 G G G 1.03 Inv. Ex. 89 T CR <-198 G G G 1.03 Inv. Ex. 90 T GA <-198 G G G 1.03 Inv. Ex. 91 T EG <-198 G G G 1.03 Inv. Ex. 92 U CR <-198 G G G 0.89 Inv. Ex. 93 U CR <-198 G G G 1.02 Inv. Ex. 94 U GA <-198 G G G 0.99 Inv. Ex. 95 U EG <-198 G G G 0.92 Inv. Ex. 96 V CR <-198 G G G 0.95 Inv. Ex. 97 V CR <-198 G G G 0.94 Inv. Ex. 98 V GI <-198 G G G 1.05 Inv. Ex. 99 V GA <-198 G G G 0.95 Inv. Ex. 100 W CR <-198 G G G 0.89 Inv. Ex. 101 W CR <-198 G G G 0.93 Inv. Ex. 102 W GA <-198 G G G 1.07 Inv. Ex. 103 W GI <-198 G G G 0.92 Inv. Ex. 104 X CR <-198 G G G 1.05 Inv. Ex. 105 X CR <-198 G G G 1.00 Inv. Ex.
Tabe a 22
Experienceco Ingredienteschemicals Steel type Transformation temperature of residual γ ScoreMsr Volume fraction after diving in liquid nitrogen Quantity and solid solution 1st 3rd 5th ° C % 106 X CR <-198 G P 0.89 Ex. Inv. 107 X EG <-198 G G G 1.07 Ex. Inv. 108 Y CR <-198 G G G 0.96 Ex. Inv. 109 Y CR <-198 G G G 0.93 Ex. Inv.
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Experienceco Ingredienteschemicals Steel type Transformation temperature of residual γ ScoreMsr Volume fraction after diving in liquid nitrogen Quantity and solid solution 1st 3rd 5th ° C % 110 Y GA <-198 G G G 0.99 Ex. Inv. 111 Y CR <-198 G G G 1.04 Ex. Inv. 112 Z CR <-198 G G G 1.01 Ex. Inv. 113 Z CR <-198 G G G 0.91 Ex. Inv. 114 Z EG <-198 G G G 1.05 Ex. Inv. 115 Z CR <-198 G G G 0.95 Ex. Comp. 116 AA CR No residual austenite Ex. Comp. 117 AB CR No residual austenite Ex. Comp. 118 B.C CR No residual austenite Ex. Comp. 119 B HR <-198 G G G 0.90 Ex. Inv. 120 AD CR <-198 G G G 0.99 Ex. Inv. 121 AD GA <-198 G G G 0.89 Ex. Inv. 122 AE CR <-198 G G G 0.99 Ex. Inv. 123 AE GA <-198 G G G 0.86 Ex. Inv. 124 AF CR <-198 G G G 0.93 Ex. Inv. 125 AF GA <-198 G G G 0.90 Ex. Inv. 126 AG CR <-198 G G G 0.89 Ex. Inv. 127 AG GA <-198 G G G 0.87 Ex. Inv.
[00120] In the treatment of diving in liquid nitrogen, the operation from immersing the steel sheet in liquid nitrogen for 1 hour, and then removing it and letting it remain in the air until reaching room temperature is counted as a treatment. Residual austenite fractions were measured at the time points at the end of the first, third and tenth treatments. Steel sheets with fractions of residual austenite that did not change were rated as G (good) while steel sheets with fractions of residual austenite that decreased were rated as P (poor).
[00121] Tables 23 to 26 show the evaluation of the steel sheet properties of experiments 1 to 127. At that time, tensile specimens based on JIS 2201 were removed from the steel sheets of experiments 1 to 127 and were submitted to tensile tests based on JIS Z 2241 to measure the yield strength (YS), the tensile strength (TS) and the total elongation (EL).
[00122] FIG. 2 shows the relationship between the tensile strength (TS) and the
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Table 23
zxperiênciThe Ingredientschemicals Steel type Material measurement results TSxEL TS xλ YS TS EL λ MPa MPa % % MPa.% MPa.% 1 THE CR 943 1026 19 54 19494 55404 Ex. Inv. 2 THE CR 503 1004 19 39 19076 39086 Ex. Inv. 3 THE GA 474 982 20 37 19640 36315 Ex. Inv. 4 THE GI 492 998 19 40 18962 40202 Ex. Inv. 5 THE HR-GA 493 941 23 48 21643 45168 Ex. Inv. 6 B CR 777 1102 19 42 20938 46284 Ex. Inv. 7 B CR 729 1143 20 41 22860 46863 Ex. Inv. 8 B CR 872 1426 14 24 19964 34224 Ex. Inv. 9 B GA 674 1163 21 39 24423 45357 Ex. Inv. 10 Ç CR 835 980 23 45 22540 44100 Ex. Inv. 11 Ç CR 846 992 20 46 19840 45632 Ex. Inv. 12 Ç CR 778 969 20 27 19380 26163 Ex. Inv. 13 Ç EG 959 1074 20 47 21480 50478 Ex. Inv. 14 Ç HR 707 937 20 47 18740 43955 Ex. Inv. 15 D CR 906 1213 19 38 23047 46094 Ex. Inv. 16 D CR 873 1205 18 47 21690 56635 Ex. Inv. 17 D CR 830 1193 19 24 22667 28632 Ex. Inv. 18 D GI 1000 1306 17 37 22202 48322 Ex. Inv.
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zxperiênciThe Ingredientschemicals Steel type Material measurement results TSXEL TS xλ YS TS EL λ MPa MPa % % MPa.% MPa.% 19 D HR 752 1179 20 36 23580 42444 Ex. Inv. 20 AND CR 611 1094 17 43 18598 47042 Ex. Inv. 21 AND CR 694 1168 19 43 22192 50224 Ex. Inv. 22 AND GA 836 1093 19 39 20767 42627 Ex. Inv. 23 AND EG 723 1122 16 44 17952 49368 Ex. Inv. 24 AND HR-GA 657 1055 20 51 21100 53805 Ex. Inv. 25 F CR 578 1010 23 48 23230 48480 Ex. Inv. 26 F CR 762 1021 21 52 21441 53092 Ex. Inv. 27 F CR 945 1129 19 41 21451 46289 Ex. Inv. 28 F CR 1061 1137 8 14 9096 15918 Ex. Comp. 29 F HR 829 1078 18 44 19404 47432 Ex. Inv. 30 G CR 505 1093 22 41 24046 44813 Ex. Inv. 31 G CR 699 1160 18 50 20880 58000 Ex. Inv. 32 G CR 483 642 15 17 9630 10914 Ex. Comp. 33 G EG 581 1147 22 50 25234 57350 Ex. Inv. 34 G HR-GA 619 1158 17 48 19686 55584 Ex. Inv. 35 H CR 665 1071 16 46 17136 49596 Ex. Inv.
Table 24
Experienceco Ingredientschemicals Steel type Material measurement results TSXEL TSXλ YS TS EL λ MPa MPa % % MPa.% MPa.% 36 H CR 942 1155 18 52 20790 60060 Ex. Inv. 37 H CR 1017 1106 8 9 8848 9954 Ex. Comp.
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Experienceco Ingredientschemicals Steel type Material measurement results TSXEL TSXλ YS TS EL λ MPa MPa % % MPa.% MPa.% 38 H GA 477 1103 19 37 20957 40811 Ex. Inv. 39 H HR 590 1095 19 48 20805 52560 Ex. Inv. 40 I CR 546 935 23 49 21505 45815 Ex. Inv. 41 I CR 513 925 19 63 17575 58275 Ex. Inv. 42 I CR 460 861 13 2 11193 1722 Ex. Comp. 43 I GI 564 998 18 48 17964 47520 Ex. Inv. 44 I HR-GA 630 955 18 59 17190 56015 Ex. Inv. 45 J CR 680 1038 22 43 22836 44634 Ex. Inv. 46 J CR 606 991 22 50 21802 49550 Ex. Inv. 47 J CR 511 765 16 3 12240 2295 Ex. Comp. 48 J GI 652 977 24 45 23448 43965 Ex. Inv. 49 J HR-GA 743 1046 21 37 21966 38702 Ex. Inv. 50 K CR 820 1154 20 49 23080 56546 Ex. Inv. 51 K CR 584 1118 20 47 22360 52546 Ex. Inv. 52 K CR 895 1227 13 1 15951 1227 Ex. Comp. 53 K GI 720 1142 18 44 20556 50248 Ex. Inv. 54 K HR-GA 766 1141 16 40 18256 45640 Ex. Inv. 55 L CR 615 998 19 38 18962 37924 Ex. Inv. 56 L CR 687 925 22 47 20350 43475 Ex. Inv. 57 L CR 656 964 21 14 20244 13496 Ex. Comp. 58 L GI 736 1024 18 42 18432 42634 Ex. Inv. 59 L HR-GA 732 998 18 48 17964 47520 Ex. Inv. 60 M CR 1013 1346 16 30 21536 40380 Ex. Inv. 61 M CR 1076 1421 15 28 21315 39788 Ex. Inv. 62 M CR 826 1420 18 4 25560 5680 Ex. Comp.
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Experienceco Ingredientschemicals Steel type Material measurement results TSXEL TSXλ YS TS EL λ MPa MPa % % MPa.% MPa.% 63 M GA 915 1443 13 26 18759 37518 Ex. Inv. 64 N CR 1249 1443 14 29 20202 41847 Ex. Inv. 65 N CR 962 1375 16 31 22000 42625 Ex. Inv. 66 N CR 806 1333 17 8 22661 10664 Ex. Comp. 67 N GA 932 1353 19 30 25707 40590 Ex. Inv. 68 O CR 681 1019 20 49 20380 49931 Ex. Inv. 69 O CR 655 980 24 35 23520 34300 Ex. Inv. 70 O CR 615 1021 19 15 19399 15315 Ex. Comp.
Table 25
Experiencedence Ingredientschemicals Steel type Result of material measurement TSXEL TSXλ YS TS EL λ MPa MPa % % MPa.% MPa.% 71 O GA 659 1081 19 42 20539 45402 E.g. inv. 72 P CR 1002 1099 19 38 20881 41762 E.g. inv. 73 P CR 791 1034 18 39 18612 40672 E.g. inv. 74 P CR 707 980 19 4 18620 3920 Ex. Comp. 75 P GA 666 963 20 41 19260 39650 E.g. inv. 76 Q CR 642 1118 17 37 19006 41366 E.g. inv. 77 Q CR 569 1182 16 40 18912 47280 E.g. inv. 78 Q CR 598 1206 17 7 20502 8005 Ex. Comp. 79 Q GA 601 1101 22 50 24222 55050 E.g. inv. 80 R CR 709 1162 19 38 22078 44156 E.g. inv. 81 R CR 525 1070 20 38 21400 40660 E.g. inv. 82 R GA 582 1134 18 16 20412 18144 Ex. Comp. 83 R GI 732 1128 16 43 18048 48504 E.g. inv. 84 s CR 607 1228 16 39 19648 47892 E.g. inv. 85 s CR 724 1209 18 41 21762 49569 E.g. inv. 86 s GA 622 1211 20 54 24220 65394 E.g. inv.
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Experiencedence Ingredientschemicals Steel type Result of material measurement TSXEL TSXλ YS TS EL λ MPa MPa % % MPa.% MPa.% 87 s GI 740 1238 17 47 21046 58186 E.g. inv. 88 T CR 1107 1157 16 36 18512 41652 E.g. inv. 89 T CR 871 1224 17 38 20808 46512 E.g. inv. 90 T GA 916 1149 19 41 21831 47109 E.g. inv. 91 T EG 1089 1184 16 44 18944 52096 E.g. inv. 92 U CR 529 1130 20 54 22600 61020 E.g. inv. 93 U CR 597 1137 17 43 19329 48891 E.g. inv. 94 U GA 622 1052 20 52 21040 54704 E.g. inv. 95 U EG 559 1042 19 40 19798 41680 E.g. inv. 96 V CR 934 1210 15 41 18150 49610 E.g. inv. 97 V CR 1055 1247 17 47 21199 58609 E.g. inv. 98 V GI 900 1150 17 50 19550 57500 E.g. inv. 99 V GA 795 1155 15 44 17325 50820 E.g. inv. 100 W CR 878 982 22 45 21604 44190 E.g. inv. 101 W CR 366 977 23 40 22471 39080 E.g. inv. 102 W GA 375 934 21 51 19614 47634 E.g. inv. 103 W GI 391 1013 17 44 17221 44572 E.g. inv. 104 X CR 764 1104 16 47 17664 51610 E.g. inv. 105 X CR 626 1112 18 41 20016 45592 E.g. inv.
Tabe a 26
Experienceco Ingredienteschemicals Steel type Material measurement results TSXEL TSXλ YS TS EL Ex. Inv. MPa MPa % Ex.Inv. MPa.% MPa.% 106 X CR 707 1136 17 Ex.Inv. 19312 26201 Ex. Inv. 107 X EG 663 1079 20 46 21580 49634 Ex. Inv.
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Experienceco Ingredienteschemicals Steel type Material measurement results TSXEL TSXλ YS TS EL Ex. Inv. MPa MPa % Ex.Inv. MPa.% MPa.% 108 Y CR 742 1080 19 42 20520 45360 Ex. Inv. 109 Y CR 619 1128 19 39 21432 43992 Ex. Inv. 110 Y GA 543 1125 17 36 19125 40500 Ex. Inv. 111 Y CR 673 1188 19 47 22572 55836 Ex. Inv. 112 Z CR 606 1198 18 43 21564 51514 Ex. Inv. 113 Z CR 572 1245 17 33 21165 41085 Ex. Inv. 114 Z EG 583 1196 19 34 22724 40664 Ex. Inv. 115 Z CR 554 1152 4 16 4608 18432 Ex. Comp. 116 AA CR 323 424 38 107 16112 45368 Ex. Comp. 117 AB CR 683 766 15 28 11490 21448 Ex. Comp. 118 B.C CR 398 834 22 35 18348 29190 Ex. Comp. 119 B HR 833 1167 17 40 19839 46680 Ex. Inv. 120 AD CR 641 906 22 45 19932 40770 Ex. Inv. 121 AD GA 734 966 23 43 22218 41538 Ex. Inv. 122 AE CR 953 1156 20 39 23120 45084 Ex. Inv. 123 AE GA 890 1135 18 35 20430 39725 Ex. Inv.
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Experienceco Ingredienteschemicals Steel type Material measurement results TSXEL TSXλ YS TS EL Ex. Inv. MPa MPa % Ex.Inv. MPa.% MPa.% 124 AF CR 891 1169 18 56 21042 65464 Ex. Inv. 125 AF GA 879 1234 17 38 20978 46892 Ex. Inv. 126 AG CR 635 1152 19 39 21888 44928 Ex. Inv. 127 AG GA 701 1055 21 46 22155 48530 Ex. Inv.
[00123] Experiment 115 is an example in which the final temperature of the hot rolling mill is low. The microstructure is stretched in one direction making it irregular, so the ductility and the flanging capacity in the stretch are poor.
[00124] Experiments 12, 17, 106, and 111 are examples in which the heating rate since (maximum heating temperature 20 ° C) in the heating process is high. The residual austenite phase is unstable and the stretching flanging capacity is poor. [00125] Experiment 28 is an example in which the maximum heating temperature in the annealing process is high. The soft structure is not formed sufficiently and the ductility is poor.
[00126] Experiment 32 is an example in which the maximum heating temperature in the annealing process is low. A large number of crude iron-based carbides that are the starting points for fractures are included, so ductility and flanging capacity in the stretch are poor.
[00127] Experiment 37 is an example in which the average cooling rate in the first cooling process (cooling
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[00128] Experiment 42 is an example in which the average cooling rate in the first cooling process (primary cooling) is low. Crude iron-based carbides are formed, and the stretching flanging capacity is poor.
[00129] Experiment 47 is an example in which the cooling rate in the second cooling process (secondary cooling) is low. Crude iron-based carbides are formed, and the stretching flanging capacity is poor.
[00130] Experiment 52 is an example in which no reheat treatment is performed. The residual austenite phase is unstable, and the stretching flanging capacity is poor.
[00131] Experiments 57, 66, and 82 are examples in which only heating is performed from point Bs or 480 ° C or less to 500 ° C or more. The residual austenite phase is unstable and the stretching flanging capacity is poor.
[00132] Experiments 62 and 70 are examples where heating is carried out from the point Ms or 350 ° C or less to 350 ° C or more. The residual austenite phase is unstable and the stretching flanging capacity is poor.
[00133] Experiment 74 is an example where the treatment time in the range of 300 to 450 ° C is short. Carbon is not concentrated in the residual austenite, the residual austenite phase is unstable, and the flanging capacity in the stretch is poor.
[00134] Next, Experiment 78 is an example in which the retention time in the range of 300 to 450 ° C is long. Iron-based carbides form, the amount of solid C solution in the residual austenite drops, the residual austenite phase is unstable, and the flanging capacity
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[00135] In the following, Experiments 116 to 118 are examples in which the composition of ingredients has deviated from the predetermined range. In each case, sufficient properties could not be obtained.
[00136] From the results of the examples that have been explained above, it is clear that according to the high strength steel sheet and high strength galvanized steel sheet which are excellent in forming capacity and the production methods of the present invention, it is a high-strength steel plate is obtained which guarantees a maximum tensile strength of 900 MPa or more in high strength while excellent ductility and flanging capacity are given in the stretch and has sufficiently high forming capacity.
Industrial Applicability [00137] According to the present invention, for example, in applications such as members that are obtained by forming steel sheets by pressing work, etc., the maximum tensile strength of 900 MPa or higher it is guaranteed that excellent ductility and flanging capacity in the stretch are obtained and excellent strength and forming capacity are obtained simultaneously. Because of this, for example, in particular, by applying the present invention to the field of automotive parts etc., in particular by applying the invention to the field of automobiles, it is possible to take full advantage of the merits of improved safety together with increased resistance of the chassis, the shaping ability when working the members, etc. The contribution to society is immeasurable.
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权利要求:
Claims (9)
[1]
claims
1. High strength steel sheet which is excellent in forming capacity, characterized by the fact that the steel sheet consists, in mass%, of:
C: 0.075 to 0.300%,
Si: 0.70 to 2.50%,
Mn: 1.30 to 3.50%,
P: 0.001 to 0.030%,
S: 0.0001 to 0.0100%,
Al: 0.005 to 1.500%,
N: 0.0001 to 0.0100%, and
O: 0.0001 to 0.0100%, which contains, as optional elements, one or more elements between
Ti: 0.005 to 0.150%,
Nb: 0.005 to 0.150%,
B: 0.0001 to 0.0100%,
Cr: 0.01 to 2.00%,
Ni: 0.01 to 2.00%,
Cu: 0.01 to 2.00%,
Mo: 0.01 to 1.00%,
V: 0.005 to 0.150%, and one or more elements between Ca, Ce, Mg, Zr, Hf, and REM: 0.0001 to 0.5000% in total, and has a balance of iron and the inevitable impurities, where the steel sheet structure contains, in fraction of volume, residual austenite phase: 2 to 20%, ferrite phase: 10 to 75%, bainitic ferrite phase and / or bainite phase: 10 to 50%, tempered martensite phase: 10 to 50%, and
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[2]
2/4 “fresh” martensite phase: 10% or less; and the aforementioned residual austenite phase has a martensite transformation point of -60 ° C or less.
2. High strength steel sheet which is excellent in forming capacity, according to claim 1, characterized by the fact that the aforementioned residual austenite phase that transforms martensite at -198 ° C is, in fraction of volume , 2% or less of the total residual austenite phase.
[3]
3. High strength steel plate which is excellent in forming capacity, according to claim 1 or 2, characterized by the fact that the aforementioned residual austenite phase has a martensite transformation point of -198 ° C or less.
[4]
4. High strength galvanized steel sheet which is excellent in forming capacity, characterized by comprising the high strength steel sheet, as defined in claim 1 or 2, on whose surface the galvanized layer is formed.
[5]
5. Production method of high strength steel sheet which is excellent in forming capacity, characterized by comprising:
a hot-rolling process of heating a plate which consists, in mass%, of:
C: 0.075 to 0.300%,
Si: 0.70 to 2.50%,
Mn: 1.30 to 3.50%,
P: 0.001 to 0.030%,
S: 0.0001 to 0.0100%,
Al: 0.005 to 1.500%,
Petition 870180165792, of 12/20/2018, p. 78/85
3/4
N: 0.0001 to 0.0100%, and
O: 0.0001 to 0.0100%, which contains, as optional elements, one or more elements between
Ti: 0.005 to 0.150%,
Nb: 0.005 to 0.150%,
B: 0.0001 to 0.0100%,
Cr: 0.01 to 2.00%,
Ni: 0.01 to 2.00%,
Cu: 0.01 to 2.00%,
Mo: 0.01 to 1.00%,
V: 0.005 to 0.150%, and one or more elements between Ca, Ce, Mg, Zr, Hf, and REM: 0.0001 to 0.5000% in total, and has a balance of iron and the inevitable impurities directly, or after cooling once, to 1050 ° C or more, finish lamination to the point Ar3 or more to obtain a steel sheet, and wind it to a temperature of 500 to 750 ° C, a cold lamination process of stripping the coiled steel sheet, then cold roll it at a reduction rate of 35 to 75%, and an annealing process to heat the steel sheet after the cold rolling process to a maximum heating temperature of 740 to 1000 ° C, then cool it to an average cooling rate from the aforementioned maximum heating temperature to 700 ° C from 1.0 to 10.0 ° C / s and cool from 700 to 500 ° C at an average cooling rate of 5.0 to 200 ° C / s, then holding at 350 to 450 ° C for 30 to 1000 seconds, and then cooling to room temperature and, while cooling from that temperature maximum heating to room temperature, reheat from point Bs or less than 500 ° C to 500 ° C or more at least once and reheat
Petition 870180165792, of 12/20/2018, p. 79/85
4/4 from the point Ms or less than 350 ° C to 350 ° C or more at least once.
[6]
6. Production method of high strength galvanized steel sheet which is excellent in forming capacity characterized by producing high strength steel sheet by the production method according to claim 5, and then galvanizing it.
[7]
7. Production method of high strength galvanized steel sheet which is excellent in forming capacity, characterized by the production of high strength steel sheet by the production method according to claim 5, during whose annealing process, at the time of cool from the aforementioned maximum heating temperature to room temperature, immerse the steel plate after the mentioned cold rolling process in a zinc bath in order to galvanize it by hot immersion.
[8]
8. Method of production of a galvanized steel sheet that is excellent in forming capacity, characterized by producing high-strength steel sheet by the production method according to claim 5, after whose annealing process performs immersion galvanization hot.
[9]
9. Production method of high-strength galvanized steel sheet which is excellent in forming capacity according to claim 7 or 8, characterized by the execution of bonding treatment at a temperature of 470 to 650 ° C after the mentioned galvanization by hot immersion.

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PL2738276T3|2019-11-29|

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RU2557862C1|2015-07-27|

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法律状态:
2018-09-25| B07A| Technical examination (opinion): publication of technical examination (opinion)|

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2019-04-02| B09A| Decision: intention to grant|

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2019-04-24| B16A| Patent or certificate of addition of invention granted|Free format text: PRAZO DE VALIDADE: 20 (VINTE) ANOS CONTADOS A PARTIR DE 27/07/2012, OBSERVADAS AS CONDICOES LEGAIS. (CO) 20 (VINTE) ANOS CONTADOS A PARTIR DE 27/07/2012, OBSERVADAS AS CONDICOES LEGAIS |

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2019-11-12| 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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JP2011167722|2011-07-29|

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JP2011-167722|2011-07-29|

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PCT/JP2012/069223|WO2013018722A1|2011-07-29|2012-07-27|High-strength zinc-plated steel sheet and high-strength steel sheet having superior moldability, and method for producing each|

---