HIGH RESISTANCE HOT DIP GALVANIZED STEEL PLATE HIGH RESISTANCE HOT DIP GALVANIZED STEEL PLATE AND ME

专利摘要:
patent pending: "high strength hot dip galvanized steel sheet and high strength alloy hot dip galvanized steel sheet having excellent coating adhesion, bendability and tensile strength bore capacity" 980 mpa or more and method for its production ". The invention relates to a high strength hot dip galvanized sheet steel having excellent coating adhesion, bendability and bore expandability with a ultimate tensile strength of 980 mpa or more comprising a hot dip galvanized layer. hot formed on a surface of the base steel plate. said plate contains by weight% c: 0.05% to 0.4%; si: 0.01% to 3.0%; mn: 0.1% to 3.0%; al: 0.01 to 2.0%; in which si + al? 0.5%, wt: limited to 0.04% or less; s: limited to 0.05% or less; n: limited to 0.01% or less; and the balance including f and the inevitable impurities, the base steel plate microstructure contains 40% or more in total martensite and bainite volume fraction, 8% or more in residual austenite volume fraction, and a microstructure balance being ferrite or ferrite and 10% or less by volume fraction of perlite. martensite contains 10% or more per total volume fraction of two or more types between three types of martensites (1), (2) and (3), and hot-dip galvanized sheet contains less than 7% by mass. faith.
公开号:BR112014007496B1
申请号:R112014007496-8
申请日:2012-09-28
公开日:2019-02-12
发明作者:Chisato Wakabayashi；Masafumi Azuma；Nobuhiro Fujita；Kohichi Sano
申请人:Nippon Steel & Sumitomo Metal Corporation；
IPC主号:

专利说明:

Invention Patent Descriptive Report for HIGH RESISTANCE GALVANIZED HOT STEEL PLATE AND HIGH RESISTANCE GALVANIZED HOT STEEL PLATE AND METHOD FOR THEIR PRODUCTION.
[Technical Field] [001] The present invention relates to a high-strength steel sheet having excellent forming capacity (ductility and hole expansion capacity) and to a hot-dip galvanized steel sheet bonded using the phenomenon TRIP (Plasticity Induced by Transformation) and a method for its production.
[002] This application claims priority over Japanese Patent Application No. 2011-216967, filed on September 30, 2011, the content of which is incorporated herein by reference.
[Prior Art] [003] The high strength of a steel sheet that is a raw material is in progress in order to achieve both compatibility between the weight reduction of a chassis, components, and the like of a vehicle and safety. Generally, when the strength of the steel plate increases, the forming capacity (ductility and bore expansion capacity) is impaired. Therefore, a balance between strength and forming capacity is required to use the high strength steel plate in vehicle elements. For this requirement, so far, a TRIP steel sheet using the plasticity induced by the transformation of residual austenite has been suggested (for example, referring to Patent Literature 1 and Patent Literature 2). The high-strength steel plate for vehicles requires corrosion resistance depending on the component to be applied. A bonded hot-dip galvanized steel sheet is applied in such a case. However, Si is added to TRIP steel to
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2/63 and [improving ductility. When Si concentrated on the surface of the steel plate oxidizes, TRIP steel has a problem that galvanizing failures occur easily at the time of hot dip galvanizing.
[004] A method of producing a hot-dip galvanized steel sheet bonded has been described in Patent Literature 3 and 4 which can achieve the improvement of the wetting capacity of the coating and the reduction of the bonding temperature by performing the pre- Ni coating on a high strength steel plate with Si added and working the surface layer to activate. In this method, hot-dip galvanized steel sheet and bonded hot-dip galvanized steel sheet can be produced by reheating and coating a cold-rolled steel sheet, into which a material such as the original sheet is previously integrated, produced by a cold-annealing rolling process.
[005] In addition, a Technique has been proposed in Patent Literature 5 that produces a hot dip galvanized steel sheet bonded to the high elongation type using a Ni pre-coating technique. This method refers to the production of a high-strength steel sheet having excellent resistance to corrosion by producing a steel consisting of ferrite and martensite by controlling the steel components, the annealing conditions, the conditions of hot-dip galvanizing and connection or similar and then perform hot dip galvanizing.
[006] However, in hot-dip galvanized steel sheet and bonded hot-dip galvanized steel sheet, martensite, which is generated once, is softened when the steel sheet is reheated in the galvanizing process, and thus the desired strength cannot be achieved. Thus, it is difficult to achieve both high strength and forming capacity, and the
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3/63 hot-dip galvanized steel and hot-dip galvanized steel sheet bonded having good corrosion resistance with high tensile strength of 980 MPa or more and excellent forming capacity was desired.
[Prior Art Literature] [Patent Literature (s)] [Patent Literature 1] JP 61-217529A [Patent Literature 2] JP 5-59429A [Patent Literature 3] JP 2526320B [Patent Literature 4] JP 2526322B [Patent Literature 5] JP 2006-283071A [Summary of the invention] [Problem (s) to be solved by the invention] [007] The present invention should solve the problems described above and provide a hot-dip galvanized steel sheet of high strength and a hot-dip galvanized steel plate bonded with excellent ductility and bore expansion capacity by combining a rolling process with a heat treatment in a hot dip galvanizing line. [Means to solve the problem (s)] [008] The present inventors have examined in detail in a structure control due to heat treatment and the effects of work and heat treatment in relation to various steels in which the levels of C, Si, and Mn are varied. As a result, the present inventors have found that steel sheets having unique structures can be obtained by work and heat treatment using heat treatment for continuous annealing, rolling work, and heat treatment during the subsequent coating treatment. In addition, the inventors found that the steel sheet can have a final tensile strength of 980 MPa or more, which was a
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4/63 problem so far, excellent forming capacity (ductility and hole expansion capacity) and coating property. [009] The essence of the present invention is as follows.
[0010] [1] A high-strength hot-dip galvanized steel sheet having excellent coating adhesion, forming ability, and hole expansion capability with a final tensile strength of 980 MPa or more, the steel sheet hot dip galvanized comprising a hot dip galvanized layer formed on the surface of the base steel plate, where the base steel plate contains, in mass%,
C: 0.05% to 0.4%;
Si: 0.01% to 3.0%;
Mn: 0.1% to 3.0%;
Al: 0.01 to 2.0%; in which Si + Al> 0.5%
P: limited to 0.04% or less;
S: limited to 0.05% or less;
N: limited to 0.01% or less; and [0011] The balance including Fe and the inevitable impurities, [0012] the microstructure of the base steel plate contains 40% or more in fraction of total volume of martensite and bainite, 8% or more in fraction of volume of residual austenite, and the balance of the microstructure being ferrite or ferrite and 10% or less in fraction of volume of perlite, [0013] martensite contains 10% or more in fraction of total volume of two or more types of the three types of martensite (1), (2) and (3) below, and [0014] the hot dip galvanized layer contains less than 7% by weight of Fe, [0015] martensite (1): C concentration (when cementite precipitates, also including C in cementite); CM1 is less than
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0.8% by mass, and the Hit1 nano-hardness test satisfies Expression 1. Hit1 / (- 982.1 x (CM1) ² + 1676 x CM1 + 189} <0.50 ··· Expression 1 [0016] martensite (2): concentration of C (when there is precipitation of cementite, also including C in cementite); CM2 is 0.8% by mass or more, and the Hit2 nano-hardness test satisfies Expression 2. Hit2 / {- 982.1 x ( CM2) ² + 1676 x CM2 + 189} <0.50 ··· Expression 2 [0017] martensite (3): the concentration of C (when there is precipitation of cementite, also including C in cementite); CM3 is 0.8 Mass% or more, and the hardness test at the Hit3 nano-indentation satisfies Expression 3.
0.5 <Hit3 / {- 982.1 x (CM3) ² + 1676 x CM3 + 189} <0.80 ··· Expression 3 [0018] [2] High-strength hot-dip galvanized steel sheet having excellent coating adhesion, forming capacity, and hole expansion capacity with a final tensile strength of 980 MPa or more according to item [1], where the base steel plate also contains, in mass%, one or two or more elements between:
Cr: 0.05 to 1.0%;
Mo: 0.05 to 1.0%;
Ni: 0.05 to 1.0%; and
Cu: 0.05 to 1.0%.
[0019] [3] High-strength hot-dip galvanized steel sheet having excellent coating adhesion, forming capacity, and hole expansion capacity with the final tensile strength of 980 MPa or more as per item [1 ], where the base steel plate also contains, in% by mass, one or two or more elements between:
Nb: 0.005 to 0.3%;
Ti: 0.005 to 0.3%; and
V: 0.01 to 0.5%.
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6/63 [0020] [4] The high-strength hot-dip galvanized steel sheet having excellent coating adhesion, forming ability, and hole expansion capability with the ultimate tensile strength of 980 MPa or more as per item [1], where the base steel plate also contains B: 0.0001 to 0.1 %% by weight.
[0021] [5] High-strength hot-dip galvanized steel sheet having excellent coating adhesion, forming ability, and hole expansion capability with the ultimate tensile strength of 980 MPa or more as per item [1 ], where the base steel plate also contains, in% by mass, one or two or more elements between:
Ca: 0.0005 to 0.01%;
Mg: 0.0005 to 0.01%; and
REM: 0.0005 to 0.01%.
[0022] [6] A high-strength, hot-dip galvanized alloy steel sheet having excellent coating adhesion, forming ability, and hole expansion capability with the ultimate tensile strength of 980 MPa or more, bonded hot dip galvanized steel comprising a bonded hot dip galvanized layer on the surface of the base steel plate.
[0023] where the base steel plate contains, in% by mass:
C: 0.05% to 0.4%;
Si: 0.01% to 3.0%;
Mn: 0.1% to 3.0%;
Al: 0.01 to 2.0%; in which Si + Al> 0.5%
P: limited to 0.04% or less;
S: limited to 0.05% or less;
N: limited to 0.01% or less; and [0024] the balance including Fe and the inevitable impurities,
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7/63 [0025] the microstructure of the base steel plate contains 40% or more in fraction of total volume of residual austenite, and the balance of the microstructure being ferrite or ferrite and 10% or less in fraction of volume of perlite, [0026 ] martensite contains 10% or more in a total volume fraction of two or more among three types of martensites (1), (2), and (3) below, and [0027] the bonded hot dip galvanized layer contains 7 at 15% by mass of Fe, [0028] martensite (1): the concentration of C (when there is precipitation of cementite, also including C in cementite); CM1 is less than 0.8% by mass, and the Hit1 nano-hardness test meets Expression 1.
Hit1 / (- 982.1 x (CM1) ² + 1676 x CM1 + 189} <0.50 ··· Expression 1 [0029] Martensite (2): C concentration (when there is cementite precipitation, also including C in the cementite); CM2 is 0.8% by mass or more, and the Hit2 nano-hardness test satisfies Expression 2. Hit2 / {- 982.1 x (CM2) ² + 1676 x CM2 + 189} <0.50 ·· · Expression 2 [0030] martensite (3): concentration of C (when there is cementite precipitation, also including C in cementite); CM3 is 0.8% by mass or more, and the hardness test in the Hit3 nano-indentation satisfies the Expression 3.
0.5 <Hit3 / {- 982.1 x (CM3) ² + 1676 x CM3 + 189} <0.80 ··· Expression 3 [0031] [7] The high-alloyed hot-dip galvanized steel sheet strength having excellent coating adhesion, forming capacity, and hole expansion capacity with the final tensile strength of 980 MPa or more according to item [6], where the base steel plate also contains, in mass%, a or two or more elements between:
Cr: 0.05 to 1.0%;
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Mo: 0.05 to 1.0%;
Ni: 0.05 to 1.0%; and
Cu: 0.05 to 1.0%.
[0032] [8] The high-strength, hot-dip galvanized alloy steel sheet having excellent coating adhesion, forming capacity, and hole expansion capability with the ultimate tensile strength of 980 MPa or more as per item [ 6], where the base steel plate also contains, in% by mass, one or two or more elements between:
Nb: 0.005 to 0.3%;
Ti: 0.005 to 0.3%; and
V: 0.01 to 0.5%.
[0033] [9] The high-strength, hot-dip galvanized alloy steel sheet having excellent coating adhesion, forming capacity, and bore expansion capacity with the ultimate tensile strength of 980 MPa or more as per item [ 6], where the base steel plate also contains, in mass%: B: 0.0001 to 0.1%.
[0034] [10] The high-strength, hot-dip galvanized alloy steel sheet having excellent coating adhesion, forming capacity, and hole expansion capacity with the final tensile strength of 980 MPa or more as per item [ 6], where the base steel plate also contains, in% by mass, one or two or more elements between:
Ca: 0.0005 to 0.01%;
Mg: 0.0005 to 0.01%; and
REM: 0.0005 to 0.01%.
[0035] [11] A method of producing high-strength hot-dip galvanized steel sheet having excellent coating adhesion, forming ability, and
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9/63 bore expansion with a final tensile strength of 980 MPa or more, the production method comprising:
[0036] Regarding the steel bar containing, in% by mass:
C: 0.05% to 0.4%;
Si: 0.01% to 3.0%;
Mn: 0.1% to 3.0%;
Al: 0.01 to 2.0%; in which Si + Al> 0.5%
P: limited to 0.04% or less;
S: limited to 0.05% or less;
N: limited to 0.01% or less; and [0037] The balance including Fe and the inevitable Impurities, [0038] heat up to 1200 ° C or more and perform hot rolling at a transformation temperature Ar3 or more;
[0039] perform cold rolling on a base steel plate after hot rolling at a reduction rate of 40 to 70%;
[0040] annealing the base steel plate after cold rolling at 730 to 900 ° C;
[0041] cool the base steel sheet after annealing to a temperature of 650 to 750 ° C at an average cooling rate of 0.1 to 200 ° C / s, and cool the base steel sheet to 450 ° C or less from 650 to 750 ° C at an average cooling rate of 20 ° C / s or faster;
[0042] keep the base steel plate cooled to 450 ° C or less in a range of 350 to 450 ° C for 120 seconds or more;
[0043] to cool the base steel plate kept in the range of 350 to 450 ° C to 70 ° C or less at an average cooling rate of 5 ° C or faster;
[0044] to laminate the base steel sheet cooled to room temperature at an elongation percentage of 0.2 to 2%;
[0045] heat the laminated base steel sheet to 40 ° C until the
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10/63 temperature of the galvanizing bath + 50 ° C at an average rate of temperature increase of 10 ° C / s or faster;
[0046] dip and galvanize the base steel sheet heated to the temperature of the hot dip galvanizing bath - 40 ° C and the temperature of the hot dip galvanizing bath + 50 ° C in a galvanizing bath ; and [0047] to cool the hot dip galvanized steel sheet, which is hot dip galvanized, to 70 ° C or less at an average cooling rate of 5 ° C / s or faster.
[0048] [12] The production method of high-strength hot-dip galvanized steel sheet having excellent coating adhesion, forming ability, and hole expansion capability with the ultimate tensile strength of 980 MPa or more according to item [11], where the hot dip galvanizing bath flows at a flow rate of 10 m / min or more and 50 m / min or less at the time of hot dip galvanizing.
[0049] [13] The production method of high-strength hot-dip galvanized steel sheet having excellent coating adhesion, forming capacity and bore expansion capacity with the ultimate tensile strength of 980 MPa or more as per item [11], where before being heated to the temperature of the galvanizing bath - 40 ° C to the temperature of the hot dip galvanizing bath + 50 ° C, the base steel plate is subjected to pickling, and then to The base steel plate surface is polished and removed to a depth of 0.1 pm or more and is pre-coated with 0.2 to 2 g / m ² of Ni.
[0050] [14] A method of producing a high-strength hot-dip galvanized steel sheet having excellent coating adhesion, forming ability, and bore expansion capacity with a final tensile strength of 980
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MPa or more, the production method comprising:
[0051] Regarding the steel bar containing, in% by mass:
C: 0.05% to 0.4%;
Si: 0.01% to 3.0%;
Mn: 0.1% to 3.0%;
Al: 0.01 to 2.0%; in which Si + Al> 0.5%
P: limited to 0.04% or less;
S: limited to 0.05% or less;
N: limited to 0.01% or less; and [0052] the balance includes Fe and the inevitable impurities, [0053] heat up to 1200 ° C or more and perform hot rolling at a transformation temperature Ar3 or higher;
[0054] perform cold rolling on a base steel plate after hot rolling at a reduction rate of 40 to 70%;
[0055] annealing the base steel plate after cold rolling at 730 to 900 ° C;
[0056] cool the base steel layer after annealing to a temperature of 650 to 750 ° C at an average cooling rate of 0.1 to 200 ° C / s, and the base steel sheet to 450 ° C or less from 650 to 750 ° C at an average cooling rate of 20 ° C / s or faster;
[0057] keep the steel sheet cooled to 450 ° C or less, a range of 350 to 450 ° C for 120 seconds or more;
[0058] to cool the base steel plate maintained at a range of 350 to 450 ° C to 70 ° C or less at an average cooling rate of 5 ° C / s or faster;
[0059] laminate the base steel sheet cooled to room temperature at an elongation percentage of 0.2 to 2%;
[0060] heat the laminated base steel sheet to the temperature of the hot dip galvanizing bath - 40 ° C until the temperature
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12/63 rupture of the hot dip galvanizing bath + 50 ° C at an average temperature increase rate of 10 ° C / s or faster;
[0061] dip and galvanize the base steel sheet heated to the temperature of the hot dip galvanizing bath - 40 ° C until the temperature of the hot dip galvanizing bath + 50 ° C in a hot dip bath hot-dip galvanizing and perform the heat-bonding heating treatment of the hot-dip galvanizing bath - 40 ° C and 560 ° C or less in up to 40 seconds; and [0062] cooling the hot-dip galvanized steel sheet bonded, which is subjected to bonding heating treatment, to 70 ° C or less at an average cooling rate of 5 ° C / s or faster.
[0063] [15] The production method of the hot dip galvanizing bath flows at a flow rate of 10 m / min or more and 50 m / min or less at the time of hot dip galvanizing.
[0064] [16] The production method of high-strength hot-dip galvanized steel sheet having excellent coating adhesion, forming ability, and bore expansion capacity with the ultimate tensile strength of 980 MPa or more according to item [14], where before being heated to the temperature of the hot dip galvanizing bath - 40 ° C until the temperature of the hot dip galvanizing bath + 50 ° C, the base steel plate is subjected pickling, and then the surface of the base steel plate is polished and removed to a depth of 0.1 pm or more and is pre-coated with 0.2 to 2 g / m ² of Ni.
[Effect (s) of the invention] [0065] According to the present invention, it is possible to obtain a hot-dip galvanized steel sheet and a bonded hot-dip galvanized steel sheet having excellent capacity
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13/63 conformation with high resistance and contribute notably to the industry.
[Mode (s) for carrying out the invention] [0066] The present invention will be described in detail below. (Microstructure of the base steel plate) [0067] Initially, the microstructure of a base steel plate according to the present invention will be described. The microstructures of the base steel plate according to the present invention include bainite, martensite, and residual austenite. In addition, martensite includes two or more types among three types of martensites (1), (2), and (3) defined below.
[0068] Martensite (1): the concentration of C (when there is precipitation of cementite, also including C in cementite). CM1 is less than 0.8 by mass or more and the Hit1 nano-hardness test meets Expression 1.
Hit1 / {- 982.1 x (CM1) ² + 1676 x CM1 + 189} <0, .50 ··· Expression 1 [0069] Martensite (2): C concentration (when cementite is precipitated, also including C cementite). CM2 is 0.8 mass% or more and the Hit2 nano-hardness test meets Expression 2.
Hit2 / {- 982.1 x (CM2) ² + 1676 x CM2 + 189} <0.50 ··· Expression 2 [0070] Martensite (3): C concentration (when there is cementite precipitation, also including C in the cementite). CM3 is 0.8% by mass or more and the Hit3 nano-hardness test satisfies Expression 3. 0.5 <Hit3 / {- 982.1 x (CM3) ² + 1676 x CM3 + 189} <0.80 ·· · Expression 3 [0071] Although the detailed reason is not clear, when two or more types of martensite (1) to (3) are contained in 10% or more in fraction of total volume, both the resistance and the expansion capacity of hole are achieved. The martensite, which has the toughest structure of the structures contained in the base steel plate of the present invention, is essential to guarantee the ultimate tensile strength of 980
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MPa or more. On the other hand, in a hole expansion test, since martensite is a starting point for the formation of openings, it is known that martensite deteriorates the capacity of hole expansion. Therefore, to ensure the ability to expand the hole, deformation is avoided from concentrating on a specific martensite grain by mixing two or more types of martensite between three different types of martensites. As a result, a technique has to be discovered that does not impair the hole expansion capacity and that contributes to further reinforcement. This effect can be obtained when the total volume fraction of the two or more martensites among the three types of martensites is adjusted to be 10% or more. For this reason, the lower limit of the volume fraction of the three types of martensite (1) to (3) has been adjusted to be 10%. Preferably, the lower limit is 15% or more.
[0072] The martensite (1) is a temperate martensite, which has a low concentration of C and is not as hard. The C CM1 concentration of martensite (1) is less than 0.8% by weight. When cementite precipitates in martensite (1), C in cementite which is precipitated in martensite (1) is also contained. The cementite in the martensite mentioned here may be a precipitation in the martensite sheets, or between them, so that the effect of the present invention is shown. This structure originates from a new martensite to be formed at the time of cooling to 70 ° C or less after being kept at 350 to 450 ° C in an annealing process of the production method of the present invention. The martensite (1) is a tempered martensite in which the new martensite formed at the time of cooling to 70 ° C or less after being kept at 350 to 450 ° C is tempered during the immersion treatment in a hot dip galvanizing bath or in a bonding treatment.
[0073] The C CM1 concentration of martensite (1) is less than
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0.8% by mass. This also includes a case in which the C concentration was reduced to less than 0.8% by weight when the C in the new martensite was diffused into the austenite during the immersion treatment in the hot dip galvanizing bath or in the bonding treatment and so the new martensite was tempered even though the C concentration of the new martensite was 0.8% by weight or more, in addition to the case where the C concentration of the new martensite formed at the time of cooling to 70 ° C or less after being kept at 350 450 ° C it was less than 0.8% by mass.
[0074] Since martensite (1) has a low C CM1 concentration, less than 0.8% by weight, and is tempered, it is the softest of the three types of martensite (1) to (3). The hardness test in the nano-orientation Hit1 of martensite (1) satisfies Expression 1. When the volume fraction of martensite (1) is 60% or more of a microstructure of the base steel plate, the volume fraction of ferrite and the residual austenite becomes very low, and the ductility deteriorates, so that the upper limit is preferably 60%.
[0075] The martensite (2) has a high concentration of C, but it is a martensite that is softened by tempering. The C CM2 concentration of martensite (2) is 0.8% by weight or more. When cementite precipitates in martensite (2), C in cementite which is precipitated in martensite (2) is also contained. Similarly, cementite in martensite can be precipitation in or between layers of martensite. Martensite (2) originates from the stress-induced martensite transformation that is induced by rolling work and into which part of a residual austenite is transformed. Although the base steel plate is kept in a temperature range of 350 to 450 ° C after annealing, the transformation of bainite from the microstructure into the base steel plate continues, and thus the C is diffused into an untransformed austenite. Residual austenite, in which C is
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16/63 concentrate, is formed in the base steel plate which is cooled to 70 ° C or less. By transforming the residual austenite by the induced stress, in which C is concentrated, by rolling, the martensite which is the origin of the martensite (2) can be obtained. The martensite (2). The martensite (2) is a tempered martensite in which the transformation of the martensite by the induced stress generated by the rolling is tempered during the immersion treatment in the hot dip galvanizing bath or the bonding treatment.
[0076] Like martensite (1), martensite (2) is a temperate martensite, but it is harder than martensite (1) since the C concentration is high. The martensite Hit2 nano-hardness test (2) satisfies Expression 2. When the volume fraction of martensite (2) is 40% or more of the microstructure of the base steel plate, the ductility deteriorates, so the upper limit is preferably adjusted to be 60%.
[0077] The martensite (3) is a martensite that has a high concentration of C, is not tempered or has a low amount of temper. The C CM3 concentration of martensite (3) is 0.8% by weight or more. When cementite precipitates in martensite (3), C in cementite which is precipitated in martensite (3) is also contained. Similarly, cementite in martensite can be either from precipitation in, or between layers of martensite. Martensite (3) is a new martensite that is formed by transformation at the time of cooling to 70 ° C or less after galvanizing, by hot dip or bonding heat treatment. In addition, martensite (3) is also martensite that remains in a state of new martensite without being substantially tempered during heat bonding treatment (in a state other than martensites (1) and (2)).
[0078] Martensite (3) is the hardest structure of the three types of martensite (1) to (3). The Hit3 nano-hardness test of martensite (3) sa
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17/63 expresses Expression 3. For this reason, martensite (3) contributes to the high reinforcement, but it deteriorates the capacity of hole expansion. Consequently, to achieve both strength and forming capacity, the upper limit of martensite (3) is 10% in the volume fraction of the microstructure of the base steel plate. However, when the volume fraction of the martensite (3) becomes very small, it is difficult to guarantee the resistance which is the final tensile strength of 980 MPa or more, so that the lower limit is preferably adjusted to be 3% or more .
[0079] Bainite is effective in guaranteeing resistance. When a high-strength steel sheet having a tensile strength that exceeds 980 MPa contains martensite and bainite of 40% or more in total volume fraction, it is possible to guarantee the strength and obtain a high bore expansion capacity. When the total volume fraction is less than 40%, the tensile strength is less than 980 MPa. Consequently, the lower limit has been adjusted to be 40%.
[0080] Residual austenite is a structure to increase ductility, particularly elongation evenly by the plasticity induced by the transformation. To obtain a particularly good elongation, it is necessary to contain the residual austenite of 8% or more in fraction of volume. In addition, due to the transformation into martensite by work, residual austenite also contributes to obtain high strength.
[0081] In the microstructure of the base steel plate of the present invention, ferrite is not essential. However, since ferrite improves ductility, it may be contained. At the time of annealing, it is possible to control the volume fraction of the ferrite by performing the two-phase annealing. In addition, it is possible to control the volume fraction of ferrite by cooling after annealing. However, when the ferrite fraction increases, the resistance
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18/63 decreases. Although high strength can be obtained by reinforcing precipitation and reinforcing the solid solution, the volume fraction of the ferrite is preferably 40% or less.
[0082] Perlite can be contained as long as the volume fraction is 10% or less. When the volume fraction of perlite exceeds 10%, strength and ductility are reduced. Therefore, the upper limit has been adjusted to be 10%.
[0083] In addition, each phase of the microstructure such as martensite, bainite, austenite, perlite, and ferrite can be identified and their positions and volume fractions can be observed and measured quantitatively using an optical microscope having a magnification of 1000 times and a scan and electronically transmitted microscope having a magnification of 1000 times to 100000 times after the cross section of the steel sheet in the rolling direction or the cross section in the direction of a right angle to the rolling direction is etched using a Nital reagent and the reagent described in JP 59-219473A. The area fraction of each structure can be obtained by looking at 20 or more fields and applying the method of counting points or analyzing images. Then, the fraction of area obtained is defined as the fraction of each structure.
[0084] The method of classifying three types of martensite (1) to (3) is the hardness and the concentration of C. The hardness can be obtained by measuring the nanoreentance hardness test by three or more points in the martensite grains and calculating the average Hit hardness. In the base steel plate according to the present invention, since a large amount of additive elements is contained, the diameter of the crystal grain is small. In addition, on the base steel plate according to the present invention, there is a case in which the size of the recess is larger than the diameter of the martensite grain in the measurement using a Vickers hardness test. Therefore, the hardness measurement of a mi
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19/63 crorion was performed by a nano-teether. Cut samples parallel to the rolling direction are notched and then subjected to mirror polishing and electrolytic polishing. Then, the hardness measurement was performed on the polished samples. As test conditions, the biter depth was measured under the condition of 50 nm using a Berkovich type biter. In addition, this test method is small in bit depth, and is sensitive to the relationship between martensite diameter grains and the size of the recess, or surface irregularities. Therefore, as a preliminary test, electrolytic polishing in various conditions and the measurement of hardness in the condition with variation in the depth of the recess are performed and the conditions to obtain a good maximum reproducible value have been adjusted as test conditions.
[0085] The C concentration of the martensite grains can be measured by any measurement method that guarantees accuracy under the condition of obtaining a precise decomposition concentration. For example, the C concentration of the martensite grains can be obtained by carefully measuring the C concentration in a step of 0.5 pm or less using a ΕΡΜΑ attached to an FE-SEM. Therefore, martensites (1) to (3) are classified according to the hardness and the concentration of C.
[0086] In addition, in order to distinguish these martensites (1) to (3), Expressions 1 to 3 use an expression of the relationship between the quantities of C CM1 to CM3 and the Hit nano-hardness test in each martensite. The denominators on the left sides of Expressions 1,2, and 3, which are input values of the C concentration represent the hardness of the carbides-free martensites (new martensite) of the C concentration. The hardness of the martensite contained in the base steel plate of the present invention becomes less than the hardness of the new martensite by the precipitation of cementite in the grains and the quenching. Therefore, the
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20/63 classification is performed taking the ratio between the hardness of the new martensite of the denominator and the hardness of the martensite of a steel plate.
(Chemical composition of the base steel sheet) [0087] The following will describe the reasons for restricting the quantities of the components of the base steel sheet in the present invention. In addition,% in the composition represents% by mass.
[0088] C: C is added as an element that increases the strength of steel and stabilizes residual austenite to improve ductility. When its content is less than 0.05%, it is difficult to guarantee the tensile strength of 980 MPa or more. Ductility, weldability, and toughness are noticeably deteriorated by excessive addition exceeding 0.40%. Therefore, the C content was adjusted to be 0.05 to 0.4%. A more preferred range is 0.13% to 0.3%.
[0089] Si: Si is a useful element to increase the strength of the steel plate by reinforcing the solid solution. In addition, Si is an essential element that has the effect of promoting the concentration of C in austenite during the transformation of bainite and generates residual austenite during annealing, to suppress the formation of cementite. These effects are not shown when the content is less than 0.01%, the scaling exfoliation and the chemical conversion capacity generated in the hot rolling are remarkably deteriorated by an addition exceeding 3.0%. Thus, the Si content was adjusted to be 0.01 to 3.0%. [0090] Mn: Mn and an effective element to improve the hardening capacity. The effect of increasing the hardening capacity is not sufficiently shown when the content is less than 01% and the toughness is deteriorated by the excessive addition that exceeds 3.0%. Consequently, the Mn content was adjusted to be 0.1 to 3.0%.
[0091] Al: Al is an element that has the function of deoxidizing. In
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21/63 addition, Al is a stabilizing element of ferrite like Si and can also be used as an alternative to Si. This effect is not shown when the content is less than 0.01% and the toughness is deteriorated by the excessive addition that exceed 2.0%. Therefore, the Al content was adjusted to be 0.01 to 2.0%.
[0092] Al + Si: Al and Si are elements that have the same functions of stabilizing ferrite and suppressing cementite. Consequently, the amount of total addition of Al and Si is important. When the amount of total addition is 0.5% or less, the function of stabilizing ferrite and suppressing cementite becomes weak. Therefore, the content was added with an amount greater than 0.5%.
[0093] P: P is an impurity element that segregates at the grain edges to lower the resistance at the grain edges, thus deteriorating the toughness. Thus, its content is preferably reduced. The upper limit of the P content was limited to 0.04% taking into account current refining technology and production costs. The lower limit value of P is not particularly determined, but when the lower limit value is less than 0.0001%, it is economically disadvantageous, so that value is preferably as a lower limit value.
[0094] S: S is an impurity element that deteriorates hot workability and toughness, and its content is preferably reduced. Consequently, the upper limit was limited to 0.05%. The lower limit value of S is not particularly determined, but when the lower limit value is less than 0.0001%, it is economically disadvantageous, so that value is preferably adjusted as the lower limit value.
[0095] N: N forms crude nitrides to deteriorate the agglutination capacity and the hole expansion capacity. Therefore, it is necessary to delete the additional quantity. The reason is because the trend
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22/63 becomes notable when the N content exceeds 0.01%. Thus, the N content was in the range of 0.01% or less. In addition, this causes bubbles to occur at the time of welding, so the smaller the better. The effect of the present invention is presented without particularly determining the lower limit, but when the N content is less than 0.0005%, the cost of production increases substantially, then that value is a substantial lower limit value.
[0096] In addition, one or two or more elements between Cr, Mo, Ni, and Cu can be added. These elements are effective elements for improving ductility and toughness. However, when the Cr, Mo, Ni, and Cu content exceeds 1.0%, the toughness can be impaired due to an increase in strength. Consequently, the upper limit of these elements was adjusted to be 1.0%. In addition, to improve ductility and toughness, the required Cr content is 0.05% or more, the required Mo content is 0.05% or more, the necessary Ni content is 0.05% or more, and the necessary Cu content is 0.05% or more, so these values are adjusted to be the lower limit values, respectively.
[0097] In addition, one or two or more elements between Ti, Nb, and V can be added. These are elements that form fine carbides and are effective in suppressing the hardening of crystal grains, ensuring strength, and improving toughness. To ensure strength and improve toughness, it is necessary to add 0.005% or more of Ti and Nb and 0.01% or more of V. However, when these elements are excessively added, the precipitate becomes crude and the toughness can be deteriorated . Consequently, the amount of addition of Nb and Ti is preferably adjusted to be 0.3% or less, and the amount of addition of V is preferably adjusted to be 0.5% or less.
[0098] B: B is an element that secretes at the edges of the grains pa
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23/63 to suppress the segregation of P and S at the grain edges. In addition, this element is also effective in improving the curing ability. However, when the B content exceeds 0.1%, a crude precipitate occurs at the grain edges to impair hot workability and toughness. Consequently, the B content is adjusted to be 0.1% or less. In addition, to increase ductility, toughness and hot workability and to improve the hardening capacity by reinforcing the grain edges, the addition of B is preferably 0.0001% or more.
[0099] In addition, one or two or more elements between Ca, Mg and REM can be added. These elements are effective elements to control the forms of sulphide to suppress the deterioration of the hot workability and the toughness due to S. REM indicates a rare earth metal. However, even when these elements are added excessively, once the effect is saturated, it is preferable that 0.01% or less of Ca, 0.01% or less of Mg, and 0.01% or less of REM is added , respectively. To improve toughness, 0.0005% or more of Ca, 0.0005% or more of Mg, and 0.0005% or more of REM are preferably added, respectively. In addition, in the present invention, REM is generally added to a mischmetal, which in addition to La and Ce may also contain other elements of the lanthanide series in combination. The effects of the invention are presented even when the series of lanthanum elements other than La and Ce are contained as unavoidable impurities. However, the effects of the present invention are presented even when metals such as La and Ce are added.
[00100] (Chemical composition of the hot dip galvanized layer and the linked hot dip galvanized layer) [00101] In the present invention, the hot dip galvanized layer
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24/63 hot formed on the surface of the base steel plate contains less than 7% by weight of Fe, the balance being Zn and the inevitable impurities. In addition, a hot dip galvanized bonded layer contains 7 to 15 wt.% Fe, the balance being Zn and the inevitable impurities. The hot dip galvanized layer and the bonded hot dip galvanized layer can also contain 0.01 to 0.5% Al and more preferably they can contain 0.05 to 0.3% by weight. In addition, the galvanizing bath may contain Fe, Mg, Mn, Si, Cr and the like in addition to pure zinc and Al.
[00102] In a case where the spot welding ability and the coating property are desired, it is possible to improve these properties by forming a bonded hot-dip galvanized layer containing 7 to 15 wt% Fe on the surface of the base steel plate. Specifically, when the base steel plate is subjected to the bonding treatment while being immersed in the galvanizing bath, the Fe is incorporated into the galvanized layer, and thus the high strength bonded hot dip galvanized steel sheet having an excellent property of coating and spot welding capability can be obtained. When the Fe content after bonding treatment is less than 7% by mass, the spot welding capacity becomes insufficient. On the other hand, when the Fe content exceeds 15% by mass, the adhesion of the galvanized layer itself is impaired, and the galvanized layer is broken and removed during machining, thus causing scratches when forming by adhering to a mold. Consequently, the Fe content contained in the galvanized layer during the bonding treatment is within a range of 7 to 15% by mass.
[00103] Furthermore, in a case where the bonding treatment is not carried out, even when the Fe content contained in the galvanized layer is less than 7% by mass, the corrosion resistance, ca
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25/63 conformability, and the hole expansion capacity that are effects obtained by the connection are good, except the spot welding ability.
[00104] In addition, the galvanized layer may contain Al, Mg, Mn, Si, Cr, Ni, Cu or similar in addition to Fe.
[00105] To measure the content of Fe and Al contained in the galvanized layer, a method of dissolving the galvanized layer with an acid can be used and chemically analyzing the dissolved solution. For example, in relation to the bonded hot-dip galvanized steel sheet cut to 30 mm χ 40 mm, only the galvanized layer is dissolved while eluting the base steel sheet with an inhibitory 5% HCI aqueous solution. Then, the content of Fe and Al is quantified using signal intensities obtained by analyzing the ICP emission from the dissolved solution and the calibration curve prepared from the concentrations of the known solutions. In addition, taking into account the measured variation of the samples, an average value obtained by measuring at least three samples that are cut from the same hot-dip galvanized steel sheet is used.
[00106] The coated quantity of the coating is not particularly limited, but is preferably 5 g / m ² or more in the quantity coated on a single surface of the base steel plate from the point of view of corrosion resistance. In addition, the amount coated on the single surface is preferably not more than 100 g / m ² from the point of view of guaranteeing the adhesion of the coating.
[00107] (Steel sheet production method) [00108] The production method will be described below.
[00109] In the present invention, the steel consisting of the above compositions is cast by melting in a conventional manner. The steel bar obtained (ingot plate) is subjected to hot rolling. The sign
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26/63 ingot is directly cooled or cooled once and then heated to 1200 ° C or more, and the hot rolling is finished at a transformation temperature of Ar3 or more.
[00110] The base steel sheet (hot rolled steel sheet) subjected to hot rolling can be wound in a temperature region of 700 ° C or less. When the winding temperature exceeds 700 ° C, the structure of the hot-rolled steel sheet becomes a structure of crude or pearlite ferrite. As a result, the structure of a final steel sheet becomes a non-uniform structure, so it is difficult to obtain good hole expansion capacity. Therefore, the upper limit of the winding temperature is set to be 700 ° C. More preferably, the upper limit is 650 ° C or less and, more preferably, is 550 ° C in which the unique bainite phase is formed. The lower limit of the winding temperature is not particularly defined. However, when the lower limit is less than 300 ° C, the resistance of the hot-rolled sheet increases and causes interference from a cold rolling in some cases. Therefore, the lower limit is preferably 300 ° C or greater.
[00111] Then, the base steel plate (hot rolled steel plate) is subjected to pickling treatment as needed and then is subjected to cold rolling at a reduction rate of 40 to 70%. To refine the microstructure after annealing, cold rolling is carried out at a reduction rate of 40% or more. On the other hand, when the cold rolling reduction ratio exceeds 70%, the load is increased by hardening at work to cause loss of productivity. Consequently, the cold rolling reduction ratio is adjusted to be 40 to 70%.
[00112] After cold rolling, the base steel sheet is annealed at 730 to 900 ° C. To control the microstructure of the base steel plate, the annealing heating temperature and the cooling conditions
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27/63 are very important in the present invention. Annealing after cold rolling is carried out in the range of 730 to 900 ° C to obtain the austenite in which the C is sufficiently concentrated. When the annealing temperature is less than 730 ° C, carbides are melted and remain, so that the required amount of austenite cannot be obtained. When the annealing temperature exceeds 900 ° C. it is uneconomical. In addition, in a case where the annealing temperature exceeds 900 ° C, recrystallization proceeds and the grain diameter becomes larger, thereby deteriorating toughness and ductility. Therefore, the annealing temperature is adjusted to be 730 to 900 ° C.
[00113] After being subjected to annealing, the base steel plate is cooled to a temperature of 600 to 750 ° C at an average cooling rate of 0.1 to 200 ° C / s. Thereafter, the base steel sheet is cooled to a temperature of 450 ° C or less from a temperature of 600 to 750 ° C at an average cooling rate of 20 ° C / s or faster. The purpose of cooling the base steel plate to a temperature of 600 to 750 ° C at an average cooling rate of 0.1 to 200 ° C / s from the annealing temperature region is to suppress the formation of perlite that occurs during the cooling process. When the cooling rate is slower than 0.1 ° C / s, it is difficult to avoid the transformation of perlite and a part of the entire austenite is transformed into perlite, so it is difficult to obtain the high strength of 980 MPa or more . Therefore, the average cooling rate from the annealing temperature range to the temperature of 600 to 750 ° C is adjusted to be 0.1 ° C / s or faster. On the other hand, cooling at a cooling rate of 200 ° C / s or faster causes not only the saturation of the effect but also an excessive investment in equipment, outside of which economic efficiency becomes poor. Therefore, the upper limit of the cooling rate is set to be 200 ° C / s.
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28/63 [00114] When the cooling rate from the temperature of 600 to 750 ° C until the temperature of 450 ° C or lower and slow, the transformation of bainite continues and a large amount of carbides is formed in the bainite structure, so that austenite is broken down and so the ductility becomes weak. In addition, since three types of martensites (1) to (3) may not be obtained, the balance between strength and bore expansion capacity is low. For this reason, it is necessary to cool at an average cooling rate of 20 ° C / s or faster. In addition, the upper limit is not limited, but when the cooling rate is increased excessively, the production cost increases, and thus the upper limit is preferably 200 ° C / s or slower.
[00115] Next, the base steel plate is kept in the range of 350 to 450 ° C for 120 seconds more. In addition, as described above, when cooling is performed from a temperature of 600 to 750 ° C to a temperature of 450 ° C or less, the cooling stop temperature is adjusted to be 350 ° C or more, and then base steel plate can be kept in the range of 350 to 450 ° C for 120 seconds or more. Alternatively, when cooling is performed from a temperature of 600 ° C to 750 ° C to a temperature of 450 ° C or less, the cooling stop temperature is set to be less than 350 ° C, and then the steel plate base is reheated and can be kept in the 350 to 450 ° C range for 120 seconds or more. The reason is because the retention in the region of temperatures of 350 to 450 ° C is to control the stability of the austenite. When the retention time is short, stabilization of austenite is not achieved and residual austenite with 8% or more in fraction of volume cannot be achieved. As a result, the balance between resistance and ductility will fail. On the other hand, retention for a long time causes excessive stabilization of residual austenite, and thus martensite is not formed in the
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29/63 cooling process to room temperature to be subsequently performed and the three types of martensite (1) to (3) are not obtained. Consequently, the retention time is preferably adjusted to be 1000 seconds or shorter.
[00116] Subsequently, the base steel plate is cooled once to 70 ° C or less at an average cooling rate of 5 ° C / s or faster. The temperature of the cooling range can be room temperature. However, since the reach temperature varies depending on the season, the reach temperature can be 70 ° C or less in terms of securing the materials and can vary depending on the season. In addition, the average cooling rate up to 70 ° C needs to be adjusted to 5 ° C / s or faster. The upper limit is not particularly determined, but cooling at a cooling rate above 200 ° C / s causes not only the saturation of the effect, but also a large investment in equipment, so that economic efficiency becomes poor. Therefore, the upper limit of the cooling rate is preferably adjusted to be 200 ° C / s or less. For this reason, part of the austenite is transformed into martensite. By performing this heat treatment, the structure composed of bainite, residual austenite, and martensite can be obtained. However, the ferrite may be partially contained. In addition, the martensite obtained by cooling to room temperature is the new martensite, which is the origin of the martensite (1).
[00117] Next, the base steel sheet cooled to 70 ° C or less is laminated. A part of the residual austenite in the base steel plate is transformed by the working lamination, and thus the transformation of the martensite by the induced tension obtained by the lamination is the origin of the martensite (2). The austenite that remains at room temperature contains 0.8% by mass of C or more, and the martensite from the stress-induced transformation formed by the austenite transformation
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Above 30/63 becomes hard. To obtain a martensite by the induced stress transformation, the percentage of elongation (reduction ratio) of the lamination is adjusted to be 0.2 to 2%. The effect is not sufficient when the elongation percentage is less than 0.2%, and the yield ratio is significantly increased and the elongation deteriorates when the elongation percentage exceeds 2%.
[00118] Then, after being subjected to NI pre-coating if necessary, the base steel plate is subjected to galvanizing or galvanizing and bonding treatment. In the case of execution of NI pre-coating, after the base steel plate is subjected to pickling, the surface of the base steel plate is removed by polishing to 0.1 pm or more in depth and then the Ni is pre-coated on the surface of the base steel sheet with 0.2 to 2 g / m ² . In order to suppress galvanizing faults and carry out the connection, the surface of the steel plate is preferably subjected to polishing or pre-coating with Ni. The reason is because oxides are easily formed on the surface of the base steel plate and the galvanizing failures and the delay of the hot dip galvanizing bonding treatment occur easily through a plurality of heat treatment processes.
[00119] After annealing, oxides of Si, Mn, and the like exist in the surface layer of the base steel plate in some cases. When these oxides exist, even if the base steel plate is considered to be pre-coated with Ni, galvanizing failures occur in some cases. For this reason, it is necessary to remove the oxides by performing the polishing. Since the effect is notable for polishing 0.1 pm or more in depth from the surface layer of the base steel plate, the amount of polishing is adjusted to be 0.1 pm. The upper limit is not particularly determined. However, once the steel sheet has become
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31/63 in the fine and the product yield is reduced according to the amount of polishing, the amount of polishing is preferably small. [00120] When the NI coating quantity is adjusted to be 0.2 to 2 g / m ² , the galvanizing failures are suppressed at the time of subsequent hot dip galvanizing. In the amount of NI coating of less than 0.2 g / m ² , since the effect of suppressing the plating failures is not sufficiently obtained, its lower limit is adjusted to be 0.2 g / m ² . The effect of suppressing galvanizing failures can be obtained without specifically determining the upper limit, but an upper limit exceeding 2.0 g / m ² causes not only the saturation of the effect, but also an excessive investment in equipment, so it is undesirable that economic efficiency becomes poor. In addition, this requires an excessive investment in equipment or an extreme drop in the operation of the speed of passing the sheet, so it is undesirable that economic efficiency becomes poor.
[00121] The temperature of the base steel plate to be immersed in the hot dip galvanizing bath is in the range from a temperature that is less than 40 ° C compared to the temperature of the hot dip galvanizing bath up to a temperature that higher by 50 ° C compared to the temperature of the hot dip galvanizing bath. When the temperature of the base steel plate to be immersed is below the temperature of the hot dip galvanizing bath - 40 ° C, the heat loss on immersion in the galvanizing bath becomes grid and a part of the molten zinc is solidified, thus leading to the deterioration of the external appearance of galvanizing in some cases. In addition, when the temperature of the base steel plate is above the temperature of the hot dip galvanizing bath + 50 ° C, operational problems associated with increasing the temperature of the galvanizing bath
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32/63 are induced. In addition, the temperature of the galvanizing bath is controlled to be 440 to 4760 ° C. The decrease in the temperature of the galvanizing bath leads to the solidification of the hot-dip galvanization that exists in the bath and becomes the cause of galvanizing failures or becomes the cause of deterioration of appearance.
[00122] Thus, the laminated base steel sheet must be heated up to the temperature of the hot dip galvanizing bath 40 ° C to the temperature of the hot dip galvanizing bath + 50 ° C. Here, the base steel plate is heated to an average heating temperature of 10 ° C / s or more. Here, when the heating rate is slower than 10 ° C / s, the surface of the base steel plate is polished and removed while the pre-coating with Ni and the induced stress are relaxed, so that the effect of promoting link cannot be obtained. In addition, when the heating temperature is lower than the temperature of the hot dip galvanizing bath - 40, galvanizing failures occur easily during hot dip galvanizing. When the heating temperature is above the temperature of the hot dip galvanizing bath + 50 ° C, the surface of the base steel plate is polished and removed and the induced tension is relaxed, so that the effect of promoting the bond does not It can be obtained.
[00123] In a hot dip galvanizing tank, it is preferable that a jet flow of 10 m / min or more and 50 m / min or less is provided in the galvanizing bath to suppress galvanizing failures and promote bonding . The slag, which is an oxide film of Zn or Al, floats on the surface of the galvanizing bath. When the oxide film remains on the surface of the base steel plate in large quantities, the slag adheres to the surface of the base steel plate at the time of immersion in the galvanizing bath and galvanizing failures occur easily. In addition, the
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33/63 slag to the steel plate causes not only failures in galvanizing, but also delay in connection.
[00124] This property is particularly noticeable in the steel plate containing a lot of Si and Μη. The detailed mechanism is not clear, but it is considered that galvanizing failures and delay in bonding are facilitated by the reaction between Si or Mn oxide, which is formed on the surface of the base steel plate, and the slag that is similarly a oxide. The reason for adjusting the flow rate to be 10 m / min or more and 50 m / min or less is because the effect of suppressing the plating failures due to the jet flow cannot be achieved at a flow rate of less than 10 m / min. The reason for adjusting the flow rate to 50 m / min or less is because the effect of suppressing the galvanizing faults is saturated and a high cost is also avoided due to excessive investment in equipment.
[00125] In addition, the galvanizing bath may contain Fe, Al, Mg, Mn, Si, Cr and the like in addition to pure zinc.
[00126] Then, when the base steel plate is subjected to hot dip galvanizing or hot dip galvanizing and the bonding treatment by immersion in the hot dip galvanizing bath, the martensite in the base steel plate is temperate. That is, as described above, the new martensite which is the origin of martensite (1) and the martensite of the stress induced transformation which and the origin of martensite (2) are contained in the base steel plate to be dipped in the galvanizing bath by hot immersion. When the base steel plate is subjected to immersion and heat treatment of bonding in the hot dip galvanizing bath, the new martensite and the martensite from the induced transformation of the tension previously formed in the base steel plate are tempered. As a result, martensite (1) and martensite (2) are formed.
[00127] Next, the hot-dip galvanized steel sheet
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34/63 subjected to hot dip galvanizing or the hot-dip galvanized sheet steel subjected to hot dip galvanizing and bonding treatment is cooled to 70 ° C or less. The temperature of the cooling range can be adjusted to be room temperature. However, since the reach temperature varies depending on the season, the reach temperature can be 70 ° C or less in terms of securing the materials and can vary depending on the season. In addition, the average cooling rate up to 70 ° C needs to be adjusted to 5 ° C / s or faster. The upper limit is not particularly determined, but cooling at a cooling rate above 200 ° C / s causes not only the saturation of the effect, but also a large investment in facilities, so it is economically undesirable. Therefore, the upper limit of the cooling rate is preferably set to be 20 ° C / s or slower. Upon cooling, a part of the residual austenite in the base steel plate is transformed into martensite. The martensite generated from this outside becomes a martensite (3) that has a harder structure.
[00128] Only in heat treatment, only the decomposition of residual austenite is caused. However, in the present invention, the steel layer is previously subjected to lamination and thus the residual austenite is also processed. As a result, a part of the residual austenite is transformed into martensite during cooling after heat treatment. The martensite (3) obtained as a result becomes a reinforcing structure to achieve high strength. The detailed mechanism is not clear, but when the structure of the steel plate subjected to rolling was compared in detail with the structure of the steel plate, which was not subjected to hardening lamination, this martensite was not observed in the steel plate that did not was subjected to lamination. For this reason, displacement is considered
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35/63 induced during lamination contributes to the transformation of martensite at the time of heat treatment and subsequent treatment.
[00129] In addition, to obtain martensite (3), it is necessary to heat the base steel sheet to the temperature of the hot dip galvanizing bath - 40 (° C) or higher and 560 ° C or lower. When heating to the temperature of the hot dip galvanizing bath - 40 or less, martensite cannot be obtained during cooling to be carried out subsequently. On the other hand, when the base steel plate is heated to a temperature that exceeds 560 ° C, carbides are noticeably precipitated and austenite is decomposed, and thus it is difficult to obtain the amount of residual austenite that is needed to improve the elongation. For this reason, in the case of hot-dip galvanizing, the heating temperature of the base steel plate is set to be 560 ° C or less. In addition, when the time required for bonding heat treatment is long, austenite is decomposed. Consequently, the binding treatment time is preferably adjusted to be 40 seconds or shorter.
[00130] Furthermore, in an installation such as a continuous hot dip galvanizing installation that performs heat treatment and coating, the steel sheet is not cooled to room temperature in a medium run and is not subjected to lamination on a medium route. Consequently, structural controls to produce the three types of martensite as the present invention and to ensure residual austenite cannot be performed. As a result, it was difficult to achieve all the strength, ductility and bore expansion capacity at a high level.
[00131] In addition, when the surface layer of the base steel plate is pre-coated with Ni after being polished and removed to 0.1
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36/63 pm or more, bonding is promoted during bonding heat treatment after galvanizing to less than the heating temperature at the time of bonding treatment. For this reason, cementite is not generated during the heat treatment of bonding and deterioration of the hole expansion capacity is avoided. The mechanism of bonding is unclear, but the surface is considered to be activated due to the stress induced in the surface layer of the steel sheet by polishing. Examples of methods of polishing and removing the surface layer of the base steel plate may include brush polishing, sanding, or mechanical polishing. The Ni pre-coating method can be any of galvanizing, dip coating, and spray coating, and the coating weight of the surface layer is preferably about 0.2 to 2 g / m ² . When the amount of polishing and removal of the steel sheet surface layer is 0.1 pm or less and NI pre-coating is not performed, or when the weight of the pre-coating is 0.2 g / m ² or less or 2 g / m ² , the effect of promoting binding is not achieved and the binding temperature is inevitably increased. Thus, as described below, deterioration of the hole expansion capacity is not prevented. To also achieve the promotion of the bonding effect, the amount of polishing and removing the surface layer of the steel sheet is preferably adjusted to be 0.5 µm or more.
[00132] In addition, in the case of the production of hot-dip galvanized steel sheet, the effective concentration of Al in the galvanizing bath is preferably controlled in the range of 0.05 to 0.500% by mass to control the properties of the layer galvanized. Here, the effective concentration of Al in the galvanizing bath is a value obtained by subtracting the concentration of Fe in the galvanizing bath from the concentration of Al in the galvanizing bath.
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37/63 [00133] When the effective concentration of Al is less than 0.05% by mass, waste occurs significantly and a good appearance cannot be obtained. On the other hand, if the effective concentration of Al is greater than 0.500% by mass, binding is delayed and productivity is decreased. For this reason, the upper limit of the effective concentration of Al in the plating bath is adjusted to be 0.500% by mass.
[00134] To improve the coating property and the weldability, the surfaces of the hot dip galvanized steel sheet and the hot dip galvanized steel sheet of the present invention can be topcoated and to a variety of treatments, for example, chromate treatment, phosphate treatment, lubrication enhancement treatment, weldability enhancement treatment, and the like.
[00135] After hot dip galvanizing and bonding heat treatment, lamination is preferably carried out with the purpose of stabilizing the final shape and loss of elongation at the yield point. When the elongation percentage is less than 0.2%, the effect is not sufficient. On the other hand, when the elongation percentage exceeds 1%, the yield ratio increases substantially and the elongation deteriorates. Therefore, the elongation percentage is preferably adjusted to be 0.2 to 1%. In addition, before plunging into the galvanizing bath, the steel sheet can be subjected to pickling after annealing to remove the scalps generated during annealing.
[00136] [Example (s)] [00137] The effects of the present invention will now be described in greater detail using Examples. Incidentally, the conditions in the examples are exemplary conditions used to confirm
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38/63 the applicability and effects of the present invention, and the present invention is not limited to those exemplary conditions. The present invention can employ several conditions as long as the objective of the present invention is achieved without departing from the essence of the present invention. [00138] A hot-dip galvanized steel sheet and an alloyed hot-dip galvanized steel sheet were produced under the conditions indicated in Tables 2 and 3 by the molten steel having the compositions indicated in Table 1. Initially, steel plates each composition having been heated to the plate heating temperature (° C) and then the hot rolling was finished at a rolling end temperature (° C). The obtained hot-rolled steel sheet was cooled to a cooling temperature (° C) and then subjected to cold rolling at a cold rolling rate of 30% (cold rolling ratio less than 40%) and Scratching was considered when the sheet subsequently passed through an annealing facility, the pass sheet was abandoned. In addition, when cold rolling was performed at a cold rolling rate of 80% (cold rolling rate exceeding 70%), the rolling load became a maximum value and a predetermined sheet thickness was not obtained, so that cold rolling at 80% cold rolling rate has been abandoned.
[00139] After cold rolling, the base steel plate was annealed at the annealing temperature (° C), cooled (primary cooling) to a primary cooling temperature (° C) at a primary cooling rate (° C / s), and then cooled (secondary cooling) to the cooling stop temperature (° C) at a secondary cooling rate (° C / s). Then, the base steel plate was kept at a holding temperature (° C) for a holding time (s). [00140] Subsequently, the base steel plate was cooled to 70 ° C
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39/63 or less for the average cooling rate of 5 ° C / s or faster and then it was laminated at a lamination ratio (percentage of elongation) (%). The thickness of the plate was 1.4 mm. Subsequently, the surface of the base steel plate was polished and removed to a depth of surface polishing quantity (pm) and then subjected to pre-coating with Ni with the pre-coating weight of Ni (g / m ² ).
[00141] Next, the base steel plate was heated up to the heating temperature (° C) at a rate of temperature increase (° C / s) and then it was subjected to hot dip galvanization by immersion in the bath. hot dip galvanizing. In addition, the base steel plate was subjected to heat bonding treatment for a bonding time (s) at bonding temperature (° C), if necessary. In addition, the jet flow speed (m / min) in the galvanizing bath was provided in a hot dip galvanizing tank. In addition, the temperature of the galvanizing bath was controlled to 440 to 470 °.
[00142] Subsequently, the base steel plate was cooled to 70 ° C or less at an average cooling rate of 5 ° C / s or faster. [00143] Mechanical properties, bore expansion capacity (λ), the galvanized external appearance, the degree of bonding, and the coating adhesion of the obtained hot-dip galvanized steel sheet and the hot-dip galvanized steel sheet on were estimated (Table 4). The mechanical properties were estimated by a tensile test based on JISZ 2241. The tensile test (TS) and the total elongation (EL) were calculated from the stress-tension curve of the tensile test. Then, TSxEL and Τδχλ were calculated as an indication of work capacity. Hole expansion capacity was estimated by performing a hole expansion test based on the Japan Iron and Steel Federation Standard
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JFS T 1001 to measure the hole expansion ratio. It was determined that the forming capacity was good when TSxEL was 17000 MPa% or more and TSxÀ 40000 MPa% or more. The galvanized external appearance was estimated by the marks O and x by determining the presence or absence of the galvanization failures through visual observation. Here the O mark indicates that no galvanizing failures are present, and the x mark indicates that galvanizing failures are present. The Fe% bond indicates the mass% of Fe contained in the galvanized layer. In the hot-dip galvanized steel plate bonded to the bonding treatment, the 7 to 15% Fe content indicates that the bond has been well advanced. In hot-dip galvanized steel sheet that is not subjected to bonding treatment, the Fe content can be 7% or less.
[00144] Experiments ^Nos the ba, bt, c, d, e and fa, g, h, ht, i, j, k, I, m, n, and o are examples of the present invention in which all properties pass and the steel sheet with the desired property is obtained. On the other hand, in other experiments, in which the composition or the production method is outside the range of the present invention, several properties have failed to pass.
Petition 870180125061, of 9/3/2018, p. 47/81
41/63 ro φ _Q
ra o
O O O O O O O O O O O O O O O OO •frog frog frog frog frog frog frog frog frog frog frog frog frog frog frog >> O O O O O O O O O O O O O O O ç ç ç ç ç ç ç ç ç ç ç ç ç ç ç cofrog 0) 0) 0) 0) 0) 0) 0) 0) 0) 0) 0) 0) 0) a> 0) > > > > > > > > > > > > > > > ç ç ç ç ç ç ç ç ç ç ç ç ç ç ç ANDAND frog frog frog frog frog frog frog frog frog frog frog frog frog frog frog OO Ό Ό Ό Ό Ό Ό Ό Ό Ό Ό Ό Ό Ό Ό Ό OO O O O O O O O O O O O O O O O OO O O O O O O O O O O O O O O O OO < < < < < < < < < < < < < < < <1<1
to +. <
Cr: 0.96 'ίο>zCXI o o ofrog_l_the o<D O Mg: 0.0008 Ca: 0.008 m oo cocoa> m r- moo m m σ>co co r- co T— T— coCXI CXI T— CXI
Ti: 0.03 B: 0.001 Mo: 0.1 Cr: 0.8 Nb: 0.051 Ti: 0.056, B: 0.0053 Mo: 0.33 oo o 98 ‘ co 88 ‘ 723 533 816 CXI co xr oo xr xr CXI T- T- T- cxT co
< m oo co so color- so σ> m oo oo m co oo co CXI poo co CXI co oo xt O O CXI tn r- O r- xT O / O O O O OO O T- O O T- O O O Oθ ' O O O O O
co co CXI CXI xr σ> xr T— CXI xr co CXI co r- σ> m co xr CXI CXI CXI CXI co xr CXI coxr CXI co O O O O O O O OO O O O O O O O O O O O O O OO O O O O O OO O O O O O O O O O O O O O O O O to CXI o o co o o xr o o xr o o O cothe o co CXI o o xrthe o CXI o o the o CXI o o the o mthe o CXI xr o o CXI co o o rxr o o rco o oO O O OO O O O O O O O O O O O
θ-
0.01 0.012 0.011 0.013 0.012 0.01 0.02 0.01 0.02 0.03 0.02 0.03 0.013 900’0 0.011 0.013 0.014xr co m co xr m xr a>oo co m xr oo co m CXI CXI T- CXI T- CXI CXI CXI T- T- T- CXI CXI CXI T- CXI CXI
to
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Note Aco comDarativo Aco comDarativo IAco comDarativo IAco comDarativo IAco comDarativo Iinvention. Others Ca: 0.015 Ca: 0.003 Cr: 1.8 ITi: 0.9 IAl + Si 2,069 xr I 0.264 I2.89 1.78 < 690'0 2.360.164 0.02 0.08 Underlined values indicate that the numerical value is outside the presence range z 0.0012 0.005 0.005 0.002 0.0003 ω 0.0049 0.0015 0.0015 9000'0 0.0007 O. 0.014 0.08 0.08 0.0022 9000'0 Mn ΙΟΙ col 2.64 xr cxf co a> cxf ώ CXI m fx- O 2.87 rx- O 0.25 0.19 0.35 0.09 O Steel type co CXI CXI 23 24 25
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Steel of the present invention Steel of the present invention Comparative steel Comparative action Comparative action Comparative action o>ra lra Q E o oo o <1 o>ra lra Q E o oo o <1 O>ra lra Q E o oo o <1 o>ra lra Q E o oo o <1 o>ra lra Q E o oo o <1 o>ra lra Q E o oo o <1 o>ra lra Q E o oo o <1 Cooling stop temperature[° C] rCO o σ> CXI o oo CO o OO CO the rco o o xr the rco o CO OCXI xr o o xr o OO CO the CD CO the CD CO Secondary cooling rate [° C / s] the CXI the m the CO the CXI o oo 001 the CO the m the CO the m the r- the OO the CXI Primary cooling rate [° C / s] CXI o> ro m CO o d CXI oo CXI CD m rcxT CO cxT OO co Primary cooling temperature [° C] o σ> CO o to CO the rco o | CXI ml o CO The rco the xr r- Or- the color- the xr r- Or- the CXI r- Or- Annealing temperature [° C] o ao ao o CXI oo o | the r-l o σ> r- o o oo Ooõ Ooõ o CXI OO Ooõ o o OO o CXI OO Ooõ o CXI OO Cold rolling ratio[%] the m m m m m m m m m m m m m m m m m m m m m m m m m Cooling temperature [° C] o o m the xr CO o CO o σ> m the CXI CO the rm the coconut o OO m o o CO the CD m o OO m o o CO the the co Lamination termination temperature[° C] o o σ> o σ> oo o σ> oo o o σ> OCXI σ> Oσ> OCO σ> o σ> OO the CXI CD the CD OO o OO OO the CD OO o rσ> i ra S ™ õ £ θ „£ ² the CO CXI the CO CXI the CXI CXI o the CXI o oo o the CXI the CO CXI o the CXI The CD OCXI the CXI CXI OCXI o the CXI ooo cl ra ° _c i- <D Ό - CXI CXI CXI CXI CXI CXI CXI CXI CXI CXI CXI CXI  frogUJ 'C frog ra JO JO JO the OJ T3 JO 0) OJCD JO -C _Q5 * _Q Z
oo ο ι / Ί
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o>ra ra Q E o o o o <1 o>frogra Q E o o o o <1 o>frogra Q E o o o o <1 Comparative action Comparative action Comparative action Comparative action Steel of the present invention Steel of the present invention Steel of the present invention Steel of the present invention Cooling stop temperature[° C] 400 390 420 70 50 500 580 320 360 430 400 Secondary cooling rate [° C / s] 100 120 60 80 80 80 70 120 80 70 60 Primary cooling rate [° C / s] 3.8 3.8 m xr CXI CXI CXI CXI CXI xr CO co o> cxT Primary cooling temperature [° C] 710 680 680 680 690 680 680 690 690 690 690 Annealing temperature [° C] 820 830 820 820 830 820 820 820 880 850 870 Cold rolling ratio[%] 55 55 55 55 55 55 55 55 57 49 60 Cooling temperature [° C] 600 610 640 530 540 580 600 580 550 500 500 Lamination termination temperature[° C] 930 920 006 880 920 920 006 920 880 930 950 i ra S ™ õ £ θ „£ ² 1230 1210 1200 1200 1250 1240 1230 1230 1210 1230 1230 Steel type No. CXI CXI CXI CXI CXI CXI CXI CXI co xr m Experience n ° bm c _Q what dq σ n _Q ω _Q s O Ό 0)
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Steel of the present invention Comparative steel Comparative action Comparative action Comparative action o>ra lCQ Q E o oo o <1 o>ra lCQ Q E o oo o <1 o>ra lCQ Q E o oo o <1 o>ra lCQ Q E o oo o <1 o>ra lCQ Q E o oo o <1 o>ra lCQ Q E o oo o <1 o>ra lCQ Q E o oo o <1 o>ra lCQ Q E o oo o <1 o>ra lCQ Q E o oo o <1 Cooling stop temperature[° C] o σ> CO o o xr o o xr O5 o σ> CO OCO xr the m xr o ΓΟΟ o σ> CO o o xr o o xr o σ> CO o σ> CO o σ> CO Secondary cooling rate [° C / s] the m the o the CXI the xr col o oo the CO the m the r- the o the CO the CXI o σ> o oo Primary cooling rate [° C / s] m CO xr cxf xr cxf CO oO CD xr cxf CD CXI cxf CD oo cxf xr cxf CD in xr cxf CXI co Primary cooling temperature [° C] the CXI r- o oo CO o | CO ml o CO Γco the CXI Γ- o o r- The CXI Γ- OΓ- o σ> CD the CXI Γ- o o r- o σ> CD OΓ- Annealing temperature [° C] o oo oo o | oo col o CXI oo o o oo o xr oo o m oo o xr oo o m oo o xr oo the CD oo o CO oo o xr oo o m oo o xr oo Cold rolling ratio[%] oo xr the m the m the m the m the m the m the m the m the m the m the m the m the m Cooling temperature [° C] o o m o o CO the xr m o σ> xr o σ> m the CO m the coconut o σ> m the CD m o σ> m the CO CD OCXI xr the m m o σ> xr Lamination termination temperature[° C] o σ> oo o ΓΟΟ o σ> oo o o σ> OCO σ> o σ> oo o o σ> the CO σ> the m σ> OCXI σ> o o σ> the CO σ> o σ> oo o o σ> i ra S ™ õ £ θ „£ ² the CO CXI the CXI CXI o the CXI o σ> o the CXI the CO CXI o the CXI the CXI CXI the CXI CXI o the CXI OCXI the xr CXI o oo o the CXI ooo · o. ra ° _c i- <D Ό CO CO CO CO CO CO CO CO CD CD CO CO CO CO  frogUJ 'C £ _Q M— ££ it-C M— M—ANDM— c M—
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o>ra ra Q E o o o o <1 Comparative action Comparative action Comparative action Comparative action Steel of the present invention Steel of the present invention Comparative action Comparative action Comparative action Comparative action O>frogra Q E o o o o <1 o>frogra Q E o o o o <1 Cooling stop temperature[° C] 400 70 50 520 590 410 420 380 380 400 400 380 370 Secondary cooling rate [° C / s] 60 70 70 60 60 70 100 120 100 160 i 80 50 Primary cooling rate [° C / s] -st cxT -st cxT -st cxT -st cxT -st cxT 10.8 16.4 CD CD 0.06 -st CD oo Primary cooling temperature [° C] 710 700 680 680 680 680 740 680 530 660 690 730 680 Annealing temperature [° C] 830 810 810 810 810 830 880 650 840 830 800 780 810 Cold rolling ratio[%] 50 50 50 50 50 49 50 50 50 50 50 50 50 Cooling temperature [° C] 500 550 600 590 610 600 550 560 600 620 550 590 600 Lamination termination temperature[° C] 910 930 880 006 910 006 980 910 890 006 940 890 920 i ra φ ra õ £ θ „£ ² 1210 1230 1210 1240 1220 1250 1250 1220 1180 1200 1190 1210 1200 Steel type No. CO CO CO CO COoo oo oo oo oo oo oo Experience n ° £ Q_M—M— 42 CD there is hb O -C _Ç he M— -C O) -C
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ivo ivo ivo ivo ivo ivo ivo ivo ivo ivo ivo ivo Φ frog frog frog frog frog frog frog frog 2 2 2 2 Φ o φ '8.frog frog frog frog frog frog frog frog frog frog frog frogQ Q Q Q Q Q Q Q Q Q Q Q iz oAND AND AND AND AND AND AND AND AND AND AND AND Q. C - (DO O O O O O O O O O O O 5>O O O O O O O O O O O O TJ cO O O O O O O O O O O O OO O O O O O O O O O O O O*<1 <1 <1 <1 <1 <1 <1 <1 <1 <1 <1 <1 <  Ocooling plow temperature [° C] 410 400 390 390 380 360 430 400 70 81 520 009 200 1— CLSecondary cooling rate [° C / s] O 190 O O O O O O O O O O O COoo CO r- r- oo oo oo CO CO oo Ο ι _Λ Oό ra θ c 7 »ra 4 = £>x ω <1> E H xr oo xr CO oo oo CO CO CO CO CXI CXIcxT cxi cxi cxiin cxicxT ra φ E c “1- * - CL  c θ2 o <DE r 77 for ra θO O O O O O O O O O O O OCXI xr OO CO CXI oo oo σ> oo CO C i- -r- i- °.1sti— p r- r- r- r- r- r- r- r- CO CO CO CO CO annealing temperature[° C]O O O O O O O O O O O O O CO CO ooCXI CO CXI CO oo oo oo oo oo oo oo r- oo oo oo oo oo r- r- r- r- r- 1-ra ofor the .G « O O O O O O O O O O O O O ReasonIam tion <[°> m m m m m m m m m m m m m cooling temperature[° C] O O O O O O O O O O O O O r- oo oo m xr O CXI oo OO σ> r- m m xr m m CO CO m CO CO CO m m 1-frog3 P rà2 E Έ o 77 (D iCÜ LJ O O O O O O O O O O O O OO oo m CXI σ> CO CO O oo CO CXI oo Temp té da IaÇ[° a> σ> oo σ> σ> oo σ> σ> σ> oo σ> σ> oo  will£ ra õ £ θ „£ ² O O O O O O O O O O O O O σ> O σ> Oσ> O O CO m O CXI O x— CXI x— CXI CXI x— CXI CXI CXI CXI CXI CXI CXIOthe oO. frog1- <D oo oo oo oo oo oo oo oo oo oo oo oo oo ΌExperience n ° hh hkhm hn ho Q_ _C The _C -Ç ω _c
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Steel of the present invention Steel of the present invention Steel of the present invention Steel of the present invention Steel of the present invention Steel of the present invention Steel of the present invention Comparative action Comparative action Comparative action Cooling stop temperature[° C] 410 400 400 390 390 380 430 430 400 420 Secondary cooling rate [° C / s] 120 06 60 80 06 100 06 60 120 70 Primary cooling rate [° C / s] m cxT xr cxT o> 10.9 xr in CXI CO CXI CD o> 00 m cxT Primary cooling temperature [° C] 690 680 690 690 680 680 690 730 700 650 Annealing temperature [° C] 840 840 850 860 840 850 860 810 780 840 Cold rolling ratio[%] 50 50 45 60 50 50 50 60 50 50 Cooling temperature [° C] 630 620 650 550 530 560 600 500 600 650 Lamination termination temperature[° C] 920 890 870 930 940 910 950 950 960 920 i ra S ™ õ £ θ „£ ² 1230 1210 1230 1250 1220 1230 1240 1250 1230 1260 Steel type No. a> O - CXI CO xr m SI3 Experience n ° - -- AND ç O CL σ
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Comparative action Comparative action Comparative action Comparative action Cooling stop temperature[° C] 410 390 370 380 Secondary cooling rate [° C / s] 80 80 120 100 Primary cooling rate [° C / s] 10.9 CO 15.4 13.5 Primary cooling temperature [° C] 680 630 670 620 Annealing temperature [° C] 850 850 850 850 Cold rolling ratio[%] 50 50 50 50 Cooling temperature [° C] 450 490 420 560 Lamination termination temperature[° C] 890 910 006 006 ι ra ω ra õ £ θ „£ ² 1200 1260 1240 1230 Steel type No. 22 23 24 25 Experience n ° > 5 X
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(D OOOOOOOOOOOOO >>>>>>>>>>>>> - | _a ^ω o 01010101010101010101010101 KU <d frogfrogfrogfrogfrogfrogfrogfrogfrogfrogfrogfrog01 O* iz o QQQQQQQQQQQQ□ CD Q. C _ Φ ANDANDANDANDANDANDANDANDANDANDANDANDAND > -2> OOOOOOOOOOOOç ç TJ C OOOOOOOOOOOOOO OOOOOOOOOOOOOO* OOOOOOOOOOOO<1< <1<1<1<1<1<1<1<1<1<1<1<1<
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Note Aco comDarativo Aco comDarativo Comparative action Comparative action Aco comDarativo Steel of the present invention Steel of the present invention Steel of the present invention Steel of the present invention Steel of the present invention Comparative action Comparative action Comparative action ώ Q E <D I- rent rature [° C1 620 510 500 500 510 520 520 560 590 490 480 490 480 Connection time [s] m 20 20 20 20 25 35 CXI CO xr 20 CO 24 ώ ra õ Q, 9- 3 <D <D c O E Ό 3 φ <d ra σ c I- ^c 450 450 460 460 450 510 486 425 437 480 480 470 460 Rate of temperature rise [° C / s] 10.5 12.4 20.3 12.4 12.4 14.8 20.6 16.8 10.4 16.5 10.8 16.8 16.8 Jet flow speed in the plating bath [m / min] 20 m m 20 20 m 20 20 m 25 30 m O O 1 _n „σ i = ° Z FT o * 2 φ £ í = E £ E 8 S m xr o xr o xr o xr o 2.24 0.26 1.24 1.87 xr xr xr o 0.3 9'0 Amount of surface polishing[m] 0.46 0.22 0.24 0.18 0.21 0.24 0.17 0.26 0.13 0.24 0.22 0.23 0.16 Reduction ratio [%] 0.3 xr o xr o xr o xr o 0.3 xr o CXI o 0.3 0.3 xr o 0.3 xr o Q. φ O ¹⁰ O, _, c «-« ra oo «φ ω c £ m 150 150 150 150 150 220 170 120 190 400 500 260 500 Holding temperature [° C] 420 360 06 450 520 380 360 430 400 390 400 400 410 B- -g ° c I- ^ro CXI CXI CXI CXI CXI CXI CO xr m CO CO CO CO Experience n ° bo CL JD σ n _Q ω _Q s O Ό 0) £ _Q M— £
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Note ivo ivo ivo ivo ivo ivo ivo ivo ivo ivo ivo ivo ivo ivo ivo Steel of the present invention Aco comoarati Aco comoarati Aco comoarati Aco comoarati Aco comoarati Aco comoarati Aco comoarati Aco comoarati Aco comoarati Aco comoarati Aco comoarati Aco comoarati Aco comoarati Aco comoarati Aco comoarati Lead temperature[° C] 500 500 490 500 540 510 490 490 480 540 650 500 500 490 500 Connection time [s] 30 co 24 30 00 CO 30 24 30 200 28 28 28 28 24 30 ra õ Q, 9- 3 <D <D c O E TD 3 φ <d ra σ c 1- ra ^c 450 480 480 450 460 450 460 480 370 490 500 520 510 500 500 470 Rate of temperature rise [° C / s] 16.8 10.5 16.8 20.4 12.4 10.9 20.4 3 16.8 20.5 30.7 10.6 20.8 25.4 20.4 18.4 Jet flow speed in the plating bath [m / min] m m 20 m 25 20 M 20 45 20 20 20 20 20 20 30 O 1 _n „σ i = ° Z FT o * 2 ra £ í = E« ri> ^ω E £ E 8 S 0.3 xr o 0.3 xr o 0.3 HI 0.3 CXI o xr o 0.5 0.5 0.22 0.45 0.25 0.31 0.58 Amount of surface polishing[m] 0.26 CXI o 0.16 0.12 0.04 0.16 0.32 0.18 CXI o 0.16 0.22 0.43 0.62 0.26 0.14 0.34 Reduction ratio [%] 0.3 0.3 O | 3 8'0 8'0 purple 9'0 6'0 purple 8'0 CXI o 9'0 xr o 0.3 CXI o Q. φ O ¹⁰ O, _, c «-« ra oo «φ φ c JS m“ 500 HI 180 200 500 250 125 240 330 500 330 200 200 200 200 300 Holding temperature [° C] 390 430 450 370 390 400 400 390 390 390 400 370 08 450 540 410 B- -g ° c I- ^ro co CO CO CO CO CO CO CO CO CO CO CO CO CO CO rx- Experience n ° £ _c M— M—ANDM— c M— £ Q_M—M— 42 CD
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Note Steel of the present invention ivo ivo ivo ivo ivo ivo ivo ivo ivo ivo ivo ivo ivo ivo ivo Aco with parati Aco with parati Aco with parati Aco with parati Aco with parati Aco with parati Aco with parati Aco with parati Aco with parati Aco with parati Aco with parati Aco with parati Aco with parati Aco with parati Aco with parati Lead temperature[° C] 490 500 510 520 490 480 490 500 510 480 470 480 510 630 480 Connection time [s] 20 30 20 28 24 20 24 45 20 30 20 24 200 30 30 ώ ra õ Q, 9- 3 <D <D c O E Ό 3 φ <d ra σ c 1- ra ^c 459 455 460 470 480 455 480 500 460 460 480 500 290 460 480 470 Rate of temperature rise [° C / s] 19.3 20.3 19.6 14.5 20.5 10.8 15.6 16.8 30.8 20.4 18.6 3 18.2 20.8 26.8 10.8 Jet flow speed in the plating bath [m / min] 20 20 m 30 25 25 20 m 30 40 RDI 20 50 25 O m O 1 _n „σ ι = ° Z í o * 2 φ £ í = E «laughs> ^ω E £ E 8 S 0.24 9'0 0.3 mr 0.3 0.3 mr 0.3 mr 0.05 mr 8'0 CD 8'0 9'0 mr Amount of surface polishing[m] 0.16 0.12 0.18 0.22 0.18 0.24 0.24 0.16 0.06 0.18 0.24 0.16 0.12 0.16 0.16 0.22 Reduction ratio [%] CXI o mr 0.3 - mr 6'0 O | CNJ cnI 8'0 O 8'0 0.5 9'0 8'0 0.3 mr Q. φ O 9 _c «-« ra o o «φ ω c JS m 260 250 260 180 470 HI 190 320 450 260 180 220 180 460 280 330 Holding temperature [° C] 420 380 380 400 400 380 370 410 400 390 390 380 360 430 400 350 B- -g ° c I- ^ro oo oo oo oo oo oo oo oo oo oo oo oo oo oo oo oo Experience n ° there is hb hc hd he M— -C O) -C hh hkhm hn ho Q_ _C
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Note Aco comDarativo Aco comDarativo Comparative action Steel of the present invention Steel of the present invention Steel of the present invention Steel of the present invention Steel of the present invention Steel of the present invention Steel of the present invention Lead temperature[° C] 480 480 480 510 480 490 550 530 Connection time [s] 24 45 30 30 24 35 CXI CO ώ ration, 9- 3 <D <D c O E Ό 3 φ <d ra σ c 1- ra ^c 450 470 460 460 460 450 455 449 460 450 Rate of temperature rise [° C / s] 20.5 14.6 14.9 16.8 xr 25.5 36.5 19.7 20.8 oo oo Jet flow speed in the plating bath [m / min] 20 m 20 30 20 20 20 20 20 20 O 1 _n „σ i = ° Z í o * 2 φ £ í = E «laughs> ^ω E £ E 8 S 0.3 CXI o 9'0 CXI o 0.32 0.22 0.99 m 0.23 0.33 Amount of surface polishing[m] 0.14 0.32 0.28 0.62 0.15 0.19 0.26 0.24 0.18 O Reduction ratio [%] 0.5 xr o 0.3 xr o xr o CXI o 0.3 0.5 xr o 0.3 ο. ¹⁰ o ¹⁰ O, _, c «-« ra oo «φ ω c JS m“ 330 330 330 640 180 190 250 280 800 260 Holding temperature [° C] 08 450 550 380 410 400 400 390 390 380 B- -g ° c I- ^ro oo oo oo oo a> O - CXI CO xr Experience n ° The _C -Ç ω _c- -- AND ç
Petition 870180125061, of 9/3/2018, p. 61/81
55/63
Note Steel of the present invention ivo ivo ivo ivo ivo ivo ivo Aco with parati Aco with parati Aco with parati Aco with parati Aco with parati Aco with parati Aco with parati Lead temperature[° C] 480 479 510 490 475 480 Connection time[s] a> m CO30 25 a> ώ ration, 9- 3 <D <D c O E 70 3 φ <d ra σ c 1- ra ^c 455 462 435 458 428 437 461 478 Rate of temperature rise [° C / s] 30.9 10.6 10.8 m cxf 10.8 15.5 18.6 14.6 Jet flow speed in the plating bath [m / min] 20 40 20 20 O m 25 30 O 1 _n „σ i = ° Z FT o * 2 ra £ í = E« ri> ^ω E £ E 8 S 0.27 1.55 1.24 m 0.24 0.26 0.35 0.45 Amount of surface polishing[m] 90'0 0.16 0.24 0.52 0.12 0.12 0.15 0.15 Reduction ratio [%] 9'0 0.3 xr o 0.5 CXI o O 9'0 xr o Q. ^ra o ^ra 9, c «-« ra oo «φ ω c JS m“ 300 120 130 250 250 260 200 120 Holding temperature [° C] 430 430 400 420 410 390 370 380 B- -g ° c I- ^ro m 1618 CNI cxil cox cxil SI my cxil Experience n ° O CL σ> 5 X
Petition 870180125061, of 9/3/2018, p. 62/81
56/63 ro φ _Q
Note Steel of the present invention Steel of the present invention I Aco comDarativo II Aco comDarativo II Aco comDarativo II Aco comDarativo II Aco comDarativo II Aco comDarativo II Aco comDarativo II Aco comDarativo II Aco comDarativo Io>ra ra Q Q o o o o <lFe on the call[%] co rl 10.4 10.5 11.1 CD CXI 10.9 6’8 CO a> CO m xr CDGalvanized external appearance O O OOOOOOOXXXl 3 ω1- 58233 48624 145761 I121547 I119725 II 23896 II 27336 II 24888 II 50765 I144280 I142527 II 50082 ITSxEL 22701 25325 114343 I113374 I111835 I113184 I112529 II 26962 I114768 II 24600 II 22747 II 22586 ITHE[%&] 59 48 rcoa> CXIm CXIa> CXIxr CXIxr CXIm mm xrco xrsoEL [%] 23 25 CXIcomCO-CO CXICOm CXIco CXIco CXITS [MPa] 987 1013 683 co xr r-a> co r-xrCXI co11139 I11037 I1923 Ixr with CD| 6861CXI with CD1- ----<d ro xp CL Ξ 21 O O OíCXI CXI$ 2OOcoOOOo 2 T Ll c 21 28 38 the oCXI COm ma> xrpooa> corcoCD coxrpooi ^ra 3 C «« <«2 -D 21 co a> HI OOOCXICOCOI coCDOi + | «-«m «S 5 ra 64 43 HI co CXIco CXIpoothe COm xrCXI mwiththe mCXI m£ CO „CÜ C <*5 Ο π O co HI OOOCXIHI Ocococo1 ώ ίχΓ „ra c c-5 ο π co xr HI OOOxrHI CXIxrxrxr1 ώ O ra c Ip5 π π o ^ _ xr xr O | OOOpooOCOCOmmS ™ m c 21 47 32 Oco CXIco CXIpoo-m coxr cothe xrpoothe xrExperience.n ° CD ba JO JOIbc IΌ OJIbe I CD JO _c _Q 5 * _Q
Petition 870180125061, of 9/3/2018, p. 63/81
57/63 ο iCQ
Ο CD D _Ç Η — I c o O
Note 1 Aco comDarativoI Aco comDarativoI Aco comDarativoI Aco comDarativo1 Aco comDarativoI Aco comDarativoI Aco comDarativoo>frogCD Q E o o o <lSteel of the present invention Steel of the present invention Steel of the present invention CD c<D LL · Link[%]12.3 O) 13.9 COCD10.7 10.2 6'6 10.6 12.8 CD 12.4 C <g)CD Q <1 ex- tender aalvani- zada XXOOOOOOOO O ω1- 140221 I143516 I147073 II 34554 II 23759 II 34496 II 35028 II 34638 II 65065 I54292 55755 TSxEL 120601 II 22747 I112922 I115948 I111363 I19702 I114178 I112048 II 22022 I23268 24780 $ 5< n-Ν ’Ν’lda> COCO CNCN COCN Ν ’CO Ν ’m CO49 45 —1 LU cnCO CNΝ ’oo-Or-COCN CNCN 20 ω1- [MPa]1981 I| 6961923 I999 11033 I11078 IΝΟΩ ooWITH m-O O1108 1239 <D0. frog [%] O 18 OOCO CNCN COOO O Fer rita [%]a> COPOOrcoa> COthe Ν ’POOa> COCO N-a> CO24 23 Aus- tenite residual [%] ooa>Ν ’HI HI CNOOa>- O Baini- ok + Martensi- OK [%] CN mm moo Ν ’CO Ν ’COCN COoo COCN CNCN m65 67 Sea- tensi- ok (3) [%] CNCOOHI HI OOOCOCO O Sea- tensi- ok (2)[%] Ν ’mΝ ’HI HI OOOr-CO Ν ’ Sea- tensi-mΝ ’Ν ’mCN mm mmOOCO CO Bai- nita [%]Ν ’CO Ν ’Ο Ν ’oo COoor-POOCN CNa> CN53 55 <D Q. X LU laugh- the C(üΌZAND JOc _Qthe JDbp bq _Qω _QsO Ό
Petition 870180125061, of 9/3/2018, p. 64/81
58/63
Note Steel of the present invention Steel of the present invention I Aco comDarativo II Aco comDarativo I1 Aco comDarativo 1I Aco comDarativo II Aco comDarativo II Aco comDarativo II Aco comDarativo II Aco comDarativo II Aco comDarativo II Aco comDarativo IHow to use Fe on the call[%] ΓΟΟ a> r- 9’8 8’8 CO oo S‘6 ro 6'8 CO CXl xr 10.9 9'6 Galvanized external appearance O O O O O O O O O Xl Xl Xl Xl 3 ω1- 37470 40960 51264 I 32550 I130134 II 26976 I131152 I118830 I40760 42560 48960 41745 43316 TSxEL 19984 20480 114240 I114725 I113481 I112645 I111682 I20175 18152 I18240 17136 16445 20384 THE[%&] 30 32 72 42 38 32 24 xr 40 35 40 33 34 EL [%] co co 20 a> r- m a> m oo m xr co co TS [MPa] 1249 1280 712 775 793 843 1298 1345 1019 1216 1224 1265 1274 l— ----<d co xp Q. i = ÈL O O O 18 cmI my cxil O O O O O O O LL C 21 CXI O 100 54 a> xr 33 oo a> m a> oo - a> ^ra 3 C «« <«2 -D 21 co xr HI HI HI HI xri 23 CXII CXI co xr1 +, | |m «S 5 ra 66 76 HI 28 Sl 42 78 58 83 69 69 65 70 £ CO „GJ C <*5 ο π co a> HI HI HI O HI HI O co co O co 1 ώ ίχΓ „m c ο5 ji) π Γ-HI HI HI O co HI 27 a> a> O1 ώ Ora c Ip5 ji) π OO - O | O | O | O 65 - - CXI - - CXI S ™ m c 21 48 45 O oo CXI xr CXI CXI xr O rxr m xr CXI xr co xr xr xr xr Experience.n ° <D £ _Q M— ££ _c M— M—
Petition 870180125061, of 9/3/2018, p. 65/81
59/63
Grade I 1 Aco comDarativo 1I Aco comDarativo II Aco comDarativo II Aco comDarativo II Aco comDarativo II Aco comDarativo Io>ra ra Q Q o o o o <lSteel of the present invention Steel of the present invention I Aco comDarativo II Aco comDarativo II Aco comDarativo IHow to use ra c0) LL · Link[%]a> 14.7 CXICXI of 9’6 9’6 6’6 OO cxf rcxf 9’6 10.2 10.5 10.9 C <g)ra Q <1 ex- tender oalvani- zada XOOOOOOO O OOOO to1- 149134 II 33005 II 32970 I112168 I15588 II 24630 I118768 I52071 44950 144781 II 30488 II 25376 I25710 I TSxELI 119395 I114490 I114915 I19464 I18382 I113957 I114076 I24504 20300 115180 I114832 I112688 I5 $ 5< oo co5CXI xrσ>xrthe coxr CXIdog dog CD mrcoCXI co30 —1 LU mooσ> cor-oo24 xr the CXIoococo to1- [MPa]11293 Im o oom oo r-11352 I11397 ICXI ooCXI oo r-1021 1450 759 xrCXI oowith CD r-857 0)0. frog [%]O CXI coOOco CXICXI coO O Ocoscol Fer rita [%]r-cocooo CXIthe cooo cothe xr22 O the orco332 Aus- tenite residual [%] CXIOOcoi X-OOCXI oo HI OOHI Baini- ok + Martensi- OK [%] r-oo coCXI mσ> coσ> coσ> cooo CXI66 82 HI co CXI 37 Sea- tensi- ok (3) [%] mcoOHI HI OOO r- HI OOO Sea- tensi- ok (2)[%] CXIooOHI HI OOco O HI OOO Sea- tensi-CXIco-oo mthe coOO- co O | OOO 'ra m nita [%]CXI xrxrxr-σ>σ> cooo CXI49 52 Oco CXICD37 ώ Q. X LU laugh- the C(üΌANDM—c M—£Q_M—M—42CD there is _Q -CI hc I_Çhe
Petition 870180125061, of 9/3/2018, p. 66/81
60/63 ο iCQ
ΟCD D _Ç Η — I c o O
Note1 Aco comDarativoI Aco comDarativoI Aco comDarativoI Aco comDarativoI Aco comDarativo1 Aco comDarativoI Aco comDarativoI Aco comDarativoI Aco comDarativoI Aco comDarativoI Aco comDarativoI Aco comDarativoI Aco comDarativoo>ra lra Q E o o o o <1Fe on the call[%] 6'6 8'6 10.2 xr 10.7 O 9'8 oo 13.8 OO CDO ra> o> 6'6 Galvanized external appearance O O O Xl Xl Xl Xl Xl O O O O O O 3 ω1-111564 I110661 I43956 45888 47058 49708 46159 56316 I 33698 II 36000 I16356 I11601 II 25844 I122125 I1 TSxEL116608 I19799 112210 I18642 18538 20468 20846 19266 112782 I17875 I19534 I18005 I114768 I114160 ITHE[%&] r- r- 36 32 33 34 dog 38 29 32 xr28 25 EL [%]CO O CO CO xr xr CO - r- CO m CD CD TS [MPa] 1652 1523 1221 1434 1426 1462 1489 1482 11162 I11125 I1589 1601 923 885 l— ----<D CD xp 0- i = ÈL O O O O O O O O O SI O O 19 SI LL C 21 oo 22 O O oo O O O O O xrCXI rCXI 39 43 ^ra 3 C «« <«2 -D 21 m 29 m oo m m oo m RDI HI coi HI HI HI 1 + 1c 1 ωm «S 5 ra 67 49 95 82 67 85 82 85 95 76 73 73 42 33 Sea- έ SI -ί ω «1 HI HI O oo CO oo oo CO a> HI HI HI HI HI 1 ω ίχΓ „m c c-5 ji) π CXI HI 29 a> ooO O -2 HI HI HI HI HI 1 ώ Ora c Ip5 ji) π 55 m xr - - CO CXI xr CO 24 CD 60 r- O cõ ™ m c 21 O ρε 52 xr m CXI xr With 52 55 CXI CO 52 CXI CO m CO 33 Experience.n ° M— -C O) _C hh hk _ç hm hn ho hp hq -Ç hs
Petition 870180125061, of 9/3/2018, p. 67/81
61/63
Note Gift steel invention gift gift gift gift gift gift Steel of invention Steel of invention Steel of invention Steel of invention Steel of invention Steel of invention W ç O frog O* COmrCOmrCOFaith CO O) [%] OO CXIrcxfCD ç ex- frog c CO CD frog co ç > 0 CL < Φ ra CD ra N OOOOOOO OmOOmmrCXI> COCXICOmCOmr-xrCOxrxrOCXIOW r-COmCDCXICO I- xrmmxrxrxrxr-1 OmOr-r-mrCOLLJ xrxrcoCOCOX CO CXIr- mmw OOCDCXIOCXIO1- CXICXI* "CXICXICXICXIoa sp o * » mmCOOmCDxr< COxrxrmCOCOCOsp p Li mr-COCOr-CDr-LU -CXI frog COmmCOcoω Q. mcoOCDOcoO:> COT—CXItoCXIT—CXI1-'-' * *o>* * frog0) Q- sp o * » OOOOOOO frog0) cor-COCOCOxrr-LL CXICXICXICXICXICXICXI frogAus c Φ residing ra o Ό [%] CXIOOCDcoCDO +çli ώ sp o * » ra m frog frog c Φ frog tfj636465666763iL CO ώ c sΦ frog xrCOOxrxrxrmiL CO ώ c sΦ frog COxrxrCOxrCOCOli ώfrog ç _sΦ frog cSCXIxrCDxrcomco, _± COCOs OCXIT—xrOmxrm ç CXImmmmmxrώThe C Q. ç ra Ό X LU «D --, -ANDç
Petition 870180125061, of 9/3/2018, p. 68/81
62/63
Note Steel of the present invention Aco comDarativo II Aco comDarativo II Aco comDarativo II Aco comDarativo II Aco comDarativo II Aco comDarativo Io>ra lra Q E o o o o <lFe on the call[%]10.5 8’9 6’8 10.7 m cxf oo cxfGalvanized external appearance O OXOOOOO3 ω1- 44136 15850 II 24570 I144167 I121456 II 57474 II 20688 I121472 ITSxEL 19616 19750 I117010 I113707 I115198 I110197 I115516 I19394 ITHE[%&] 36 COCO CXIa> CXIxr CXICXI COxr CXICOEL [%] CO mooa>r--oo TS [MPa] 1226 11950 I945 11523Ixr σ> oorCXI σ>CXI CO oo11342 I1- ----<d ra xp CL Ξ 21 O OOOOOOOT 5 TLL C 21 20 OOOr-OOm σ>i ^ra 8 c «« <9 2 -D 21 a> mOCXICOOCOHI i + | «-«m w S 5 ra r- m oo29 oo σ> the orσ>mi 4 «co„<u ra o ^. r- OCOHI OOCOHI iL üi ν 'ra c o<u ra o ^. r- CXI CXImCOOO HI 1 ω O ra c Ip<u ra o ^. CO CO CDmm r-OooCXIO | frog ™ Tfm c 21 dog OCOOCOCXI σ>CXI COmExperience.n ° O Q.σ >5X>
Petition 870180125061, of 9/3/2018, p. 69/81
63/63 [Industrial Applicability]
The present invention provides the high strength galvanized steel sheet having excellent forming capacity with final tensile strength of 980 MPa or more, which is suitable for a structural element, a reinforcement element, and an automobile suspension element. Consequently, the present invention can contribute greatly to reducing the weight of automobiles and has extremely significant effects on the industry.

权利要求:
Claims (6)
[1]
1. High-strength hot-dip galvanized steel sheet, characterized by the fact that it consists of a hot-dip galvanized layer formed on a surface of a base steel plate, in which the base steel plate consists, in% in large scale,
C: 0.05% to 0.4%;
Si: 0.01% to 3.0%;
Mn: 0.1% to 3.0%;
Al: 0.01 to 2.0%; in which Si + Al> 0.5%
P: limited to 0.04% or less;
S: limited to 0.05% or less;
N: limited to 0.01% or less; and optionally one or two or more elements between: in bulk;
Cr: 0.5 to 1.0%;
Mo: 0.05 to 1.0%;
Ni: 0.05 to 1.0%; and
Cu: 0.05 to 1.0%.
Nb: 0.005 to 0.3%;
Ti: 0.005 to 0.3%; and
V: 0.01 to 0.5%.
B: 0.0001 to 0.1%
Ca: 0.0005 to 0.01%;
Mg: 0.0005 to 0.01%;
REM: 0.0005 to 0.01%; and the compound balance of Fe and the inevitable impurities, the microstructure of the base steel plate contains 40% or more in fraction of total volume of martensite and bainite, 8% or more in fraction of volume of residual austenite, and the balance of the microstructure
Petition 870180125061, of 9/3/2018, p. 71/81
[2]
2/6 being ferrite and 10% or less in fraction of volume of perlite, martensite contains 10% or more in total volume fraction of two or more types of three types of martensites (1), (2) and (3) below, and the hot dip galvanized layer contains less than 7% Fe by weight, martensite (1): the concentration of C (where there is precipitation of cementite, also including C in cementite); CM1 is less than 0.8% by mass, and the Hit1 nano-hardness test satisfies Expression 1, Hit1 / {- 982.1 x (CM1) ² + 1676 x CM1 + 189} <0.50 ··· Expression 1 martensite (2): the concentration of C (when cementite is precipitated, also including C in cementite); CM2 is 0.8% by mass or more, and the Hit2 nano-hardness test meets Expression 2,
Hit2 / {- 982, x (CM2) ² + 1676 x CM2 + 189} <0.50 ··· Expression 2 to martensite (3): the concentration of C (when cementite is precipitated, also including C in cementite) ; CM3 is 0.8% by mass or more, and the Hit3 nano-hardness test meets Expression 3, 0.5 <Hit3 / {- 982.1 x (CM3) ² + 1676 x CM3 + 189} <0.80 · ·· Expression 3
2. High strength hot-dip galvanized alloy steel sheet, characterized by the fact that it consists of a hot-dip galvanized bonded layer formed on the surface of the base steel plate, in which the base steel plate consists, in% by mass, C: 0.05% to 0.4%;
Si: 0.01% to 3.0%;
Mn: 0.1% to 3.0%;
Al: 0.01 to 2.0%; in which Si + Al> 0.5%
P: limited to 0.04% or less;
S: limited to 0.05% or less;
N: limited to 0.01% or less;
Petition 870180125061, of 9/3/2018, p. 72/81
[3]
3/6 optionally one or two or more elements between: bulk;
Cr: 0.5 to 1.0%;
Mo: 0.05 to 1.0%;
Ni: 0.05 to 1.0%; and
Cu: 0.05 to 1.0%.
Nb: 0.005 to 0.3%;
Ti: 0.005 to 0.3%; and
V: 0.01 to 0.5%.
B: 0.0001 to 0.1%
Ca: 0.0005 to 0.01%;
Mg: 0.0005 to 0.01%;
REM: 0.0005 to 0.01%; and the compound balance of Fe and the inevitable impurities, the microstructure of the base steel plate contains 40% or more in fraction of total volume of martensite and bainite, 8% or more in fraction of volume of residual austenite, and the balance of the microstructure being ferrite and 10% or less of perlite in fraction of volume, martensite contains 10% or more in fraction of total volume of two or more types among three types of martensites (1), (2) and (3) below, and the hot-dip galvanized bonded layer contains
7 to 15% by weight of Fe, martensite (1): the concentration of C (when there is precipitation of cementite, also including C in cementite); CM1 is less than 0.8% by mass, and the Hit1 nano-hardness test meets Expression 1,
Hit1 / {- 982.1 x (CM 1) ² + 1676 x CM1 + 189} <0.50 ··· Expression 1 to martensite (2): the C concentration (when there is cementite precipitation, also including C cementite); CM2 is 0.8%
Petition 870180125061, of 9/3/2018, p. 73/81
[4]
4/6 by mass or more, and the Hit2 nano-hardness test meets Expression 2,
Hit2 / {- 982.1 x (CM2) ² + 1676 x CM2 + 189} <0.50 ··· Expression 2 to martensite (3): the C concentration (when there is cementite precipitation, also including C in the cementite); CM3 is 0.8% by mass or more, and the Hit3 nano-hardness test meets Expression 3,
0.5 <Hit3 / {- 982.1 x (CM3) ² + 1676 x CM3 + 189} <0.80 ··· Expression 3
3. Method of production of hot-dip galvanized steel sheet comprising:
in relation to the steel bar consisting, in% by mass:
C: 0.05% to 0.4%;
Si: 0.01% to 3.0%;
Mn: 0.1% to 3.0%;
Al: 0.01 to 2.0%; in which Si + Al> 0.5%
P: limited to 0.04% or less;
S: limited to 0.05% or less;
N: limited to 0.01% or less;
optionally one or two or more elements between: in bulk;
Cr: 0.5 to 1.0%;
Mo: 0.05 to 1.0%;
Ni: 0.05 to 1.0%; and
Cu: 0.05 to 1.0%.
Nb: 0.005 to 0.3%;
Ti: 0.005 to 0.3%; and
V: 0.01 to 0.5%.
B: 0.0001 to 0.1%
Ca: 0.0005 to 0.01%;
Mg: 0.0005 to 0.01%;
Petition 870180125061, of 9/3/2018, p. 74/81
[5]
5/6
REM: 0.0005 to 0.01%; and the compound balance of Fe and the inevitable impurities, characterized by the fact that it comprises the steps:
heat to 1200 ° C or more and perform hot rolling at a transformation temperature Ar3 or higher;
perform cold rolling on a base steel plate after hot rolling at a reduction rate of 40 to 70%;
annealing the base steel plate after cold rolling at 730 to 900 ° C;
cool the base steel sheet after annealing to a temperature of 650 to 750 ° C at an average cooling rate of 0.1 to 200 ° C / s, and cool the base steel sheet to 450 ° C or less from from 650 to 750 ° C at an average cooling rate of 20 ° C / s or faster;
retain the base steel sheet cooled to 450 ° C or less in a range of 350 to 450 ° C for 120 seconds or more;
cooling the base steel plate maintained in the range of 350 to 450 ° C to 70 ° C or less at an average cooling rate of 5 ° C / s or faster;
laminate the base steel sheet cooled to room temperature at an elongation percentage of 0.2 to 2%;
heat the laminated base steel sheet to the temperature of the hot dip galvanizing bath - 40 ° C the temperature of the hot dip galvanizing bath + 50 ° C at an average rate of temperature increase of 10 ° C / s or faster;
dip and galvanize the base steel sheet heated to the temperature of the hot dip galvanizing bath - 40 ° C the temperature of the hot dip galvanizing bath + 50 ° C in a hot dip galvanizing bath hot; and
Petition 870180125061, of 9/3/2018, p. 75/81
[6]
6/6 to cool hot-dip galvanized steel sheet, which is hot-dip galvanized, to 70 ° C or less at an average cooling rate of 5 ° C / s or faster.
4. Method of producing a hot-dip galvanized steel sheet, according to claim 3, characterized by the fact that it comprises dipping and hot-dip galvanizing the base steel sheet heated to the temperature of the galvanizing bath by hot dip - 40 ° C ”at the temperature of the hot dip galvanizing bath + 50 ° C” in a hot dip galvanizing bath and perform the heat bonding treatment at the temperature of the hot dip galvanizing bath - 40 ° C or higher and 560 ° C or lower within 40 seconds.
5. Production method of high-strength hot-dip galvanized steel sheet, according to claim 3 or 4, characterized by the fact that the hot-dip galvanizing bath flows at a flow rate of 10 m / min or more and 50 m / min or less at the time of hot dip galvanizing.
6. Method of production of hot-dip galvanized steel sheet, according to claim 3 or 4, characterized by the fact that before being heated to the temperature of the hot-dip galvanizing bath - 40 ° C ”a hot dip galvanizing bath temperature + 50 ° C ”, the base steel plate is subjected to pickling, and then the surface of the base steel plate is polished and removed to a depth of 0.1 pm or more and is pre-coated with 0.2 to 2 g / m ² NI.

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BR102012025656A2|2018-01-02|HIGH-RESISTANCE TYPE HIGH-RESISTANCE STEEL PLATE, HIGH-RESISTANCE COLD HIGH RESISTANCE TYPE Cold Rolled Steel, HIGH-PERFORMANCE GALVANIZED HIGH-RESISTANCE TYPE STEEL PLATE HIGH RESISTANCE TYPE HOT RESISTANCE, HOT GALVANIZED STEEL PLATE AND HIGH RESISTANCE TYPE HOT, COLD HIGH RESISTANCE COLD LAMINATED STEEL SHEET METHOD REASON OF INCOME, METHOD FOR PRODUCTION OF HIGH RESISTANCE HOT GALVANIZED STEEL PLATE, AND METHOD FOR PRODUCTION OF HIGH RESISTANCE HOT AND RECOZED HIGH RESISTANCE TYPE OF GALVANIZED STEEL

同族专利:

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公开号 | 公开日

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KR20140068222A|2014-06-05|

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US20140342183A1|2014-11-20|

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ZA201402970B|2015-04-29|

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RU2586386C2|2016-06-10|

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CN103827336A|2014-05-28|

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ES2670893T3|2018-06-01|

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EP2762592B1|2018-04-25|

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US20170369979A1|2017-12-28|

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RU2014116634A|2015-11-10|

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WO2013047830A1|2013-04-04|

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EP2762592A1|2014-08-06|

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MX2014003712A|2014-07-09|

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BR112014007496A2|2017-04-04|

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IN2014DN03212A|2015-05-22|

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PL2762592T3|2018-08-31|

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CA2850101C|2017-01-17|

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CN103827336B|2016-01-06|

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JP5403185B2|2014-01-29|

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CA2850101A1|2013-04-04|

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TW201323655A|2013-06-16|

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TWI523975B|2016-03-01|

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US10465272B2|2019-11-05|

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EP2762592A4|2015-07-08|

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JPWO2013047830A1|2015-03-30|

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US9783878B2|2017-10-10|

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KR101607786B1|2016-03-30|

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法律状态:
2018-06-05| B06A| Patent application procedure suspended [chapter 6.1 patent gazette]|

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2018-12-11| B09A| Decision: intention to grant [chapter 9.1 patent gazette]|

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2019-02-12| B16A| Patent or certificate of addition of invention granted [chapter 16.1 patent gazette]|Free format text: PRAZO DE VALIDADE: 20 (VINTE) ANOS CONTADOS A PARTIR DE 28/09/2012, OBSERVADAS AS CONDICOES LEGAIS. (CO) 20 (VINTE) ANOS CONTADOS A PARTIR DE 28/09/2012, OBSERVADAS AS CONDICOES LEGAIS |

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

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2021-08-10| B21F| Lapse acc. art. 78, item iv - on non-payment of the annual fees in time|Free format text: REFERENTE A 9A ANUIDADE. |

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2021-11-30| B24J| Lapse because of non-payment of annual fees (definitively: art 78 iv lpi, resolution 113/2013 art. 12)|Free format text: EM VIRTUDE DA EXTINCAO PUBLICADA NA RPI 2640 DE 10-08-2021 E CONSIDERANDO AUSENCIA DE MANIFESTACAO DENTRO DOS PRAZOS LEGAIS, INFORMO QUE CABE SER MANTIDA A EXTINCAO DA PATENTE E SEUS CERTIFICADOS, CONFORME O DISPOSTO NO ARTIGO 12, DA RESOLUCAO 113/2013. |

优先权:

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申请号 | 申请日 | 专利标题

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JP2011216967|2011-09-30|

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JP2011-216967|2011-09-30|

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PCT/JP2012/075230|WO2013047830A1|2011-09-30|2012-09-28|High-strength hot-dipped galvanized steel sheet and high-strength alloyed hot-dipped galvanized steel sheet, each having tensile strength of 980 mpa or more, excellent plating adhesion, excellent formability and excellent bore expanding properties, and method for producing same|

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