WO2023218576A1 - 亜鉛めっき鋼板、部材およびそれらの製造方法 - Google Patents

亜鉛めっき鋼板、部材およびそれらの製造方法 Download PDF

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WO2023218576A1
WO2023218576A1 PCT/JP2022/019991 JP2022019991W WO2023218576A1 WO 2023218576 A1 WO2023218576 A1 WO 2023218576A1 JP 2022019991 W JP2022019991 W JP 2022019991W WO 2023218576 A1 WO2023218576 A1 WO 2023218576A1
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steel sheet
galvanized steel
bending
area ratio
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PCT/JP2022/019991
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English (en)
French (fr)
Japanese (ja)
Inventor
由康 川崎
悠佑 和田
秀和 南
達也 中垣内
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Ｊｆｅスチール株式会社
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Application filed by Ｊｆｅスチール株式会社 filed Critical Ｊｆｅスチール株式会社
Priority to PCT/JP2022/019991 priority Critical patent/WO2023218576A1/ja
Priority to PCT/JP2023/006924 priority patent/WO2023218730A1/ja
Priority to CN202380038649.XA priority patent/CN119173645A/zh
Priority to EP23803217.1A priority patent/EP4502217A4/en
Priority to KR1020247036701A priority patent/KR20240172211A/ko
Priority to JP2023565496A priority patent/JP7601256B2/ja
Publication of WO2023218576A1 publication Critical patent/WO2023218576A1/ja
Priority to MX2024013687A priority patent/MX2024013687A/es

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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
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Definitions

  • the present invention relates to galvanized steel sheets, members made from the galvanized steel sheets, and methods of manufacturing them.
  • high-strength steel plates are used for the main structural members and reinforcing members (hereinafter also referred to as automobile frame structural members) that are assembled into the frame of the car cabin.
  • the number of applications of high-strength steel plates of 780 MPa or higher is increasing.
  • high-strength steel plates used for automobile frame structural members and the like are required to have high member strength when press-formed.
  • YR yield ratio
  • YS yield stress
  • TS yield stress
  • impact absorption energy the impact absorption energy at the time of a car collision increases.
  • a crash box has a bent portion. Therefore, from the viewpoint of press formability, it is preferable to use a steel plate having high bendability for such parts.
  • steel sheets used as materials for automobile parts are often galvanized. Therefore, it is desired to develop a hot-dip galvanized steel sheet that not only has high strength but also has excellent press formability and impact resistance.
  • Patent Document 1 as a steel plate that is a material for such automobile parts, C is 0.04 to 0.22%, Si is 1.0% or less, and Mn is 3.0%. % or less, P is 0.05% or less, S is 0.01% or less, Al is 0.01-0.1%, and N is 0.001-0.005%, with the balance being Fe and unavoidable impurities. It is composed of a ferrite phase as a main phase and a martensite phase as a second phase, and the maximum grain size of the martensite phase is 2 ⁇ m or less and its area ratio is 5% or more.
  • a high-strength steel plate with excellent stretch flangeability and collision resistance characteristics is disclosed.
  • Patent Document 2 describes a cold-rolled steel sheet whose surface layer has been polished to a thickness of 0.1 ⁇ m or more and which is pre-plated with Ni at 0.2 g/m2 or more and 2.0 g/m2 or less .
  • Containing two or more types of martensite [3] of three types of martensite [1], [2], and [3], 1% or more of bainite, and 0 to 10% of pearlite, and containing the three types of martensite [1], [2], and [3] are volume fractions, respectively: martensite [1]: 0% or more, 50% or less, martensite [2]: 0% or more, less than 20%, martensite [3] : 1% or more and 30% or less, and has a hot-dip galvanized layer containing less than 7% Fe, with the remainder consisting of Zn, Al and inevitable impurities, and has a tensile strength TS (MPa), Plating adhesion characterized by having a total elongation rate EL (%) and a hole expansion rate ⁇ (%) of TS x EL of 18000 MPa % or more, TS x ⁇ of 35000 MPa % or more, and a tensile strength of 980 MP
  • High-strength hot-dip galvanized steel sheet with excellent formability (martensite [1]: C concentration (CM1) is less than 0.8%, hardness Hv1 is Hv1/(-982.1 ⁇ CM1 2 +1676 ⁇ CM1+189) ⁇ 0.60, martensite [2]: C concentration (CM2) is 0.8% or more, hardness Hv2 is Hv2/(-982.1 ⁇ CM2 2 +1676 ⁇ CM2+189) ⁇ 0.60, martensite [3]: It is disclosed that the C concentration (CM3) is 0.8% or more and the hardness Hv3 is Hv3/(-982.1 ⁇ CM3 2 +1676 ⁇ CM3+189) ⁇ 0.80.
  • Patent Document 3 in mass %, C: 0.15% or more and 0.25% or less, Si: 0.50% or more and 2.5% or less, Mn: 2.3% or more and 4.0% or less. , P: 0.100% or less, S: 0.02% or less, Al: 0.01% or more and 2.5% or less, with the balance consisting of Fe and unavoidable impurities.
  • Martensite phase 30% or more and 73% or less, ferrite phase: 25% or more and 68% or less, retained austenite phase: 2% or more and 20% or less, other phases: 10% or less (including 0%), and The other phases include martensitic phase: 3% or less (including 0%), bainitic ferrite phase: less than 5% (including 0%), and the average grain size of the tempered martensitic phase is 8 ⁇ m.
  • Patent Document 4 discloses an alloyed hot-dip galvanized steel sheet having an alloyed hot-dip galvanized layer on the surface of the steel sheet, in which the steel sheet has a carbon content of 0.03% or more and 0.35% or less in mass %. , Si: 0.005% or more and 2.0% or less, Mn: 1.0% or more and 4.0% or less, P: 0.0004% or more and 0.1% or less, S: 0.02% or less, sol. It has a chemical composition consisting of Al: 0.0002% or more and 2.0% or less, N: 0.01% or less, and the balance is Fe and impurities, and is stretched in the rolling direction at a depth of 50 ⁇ m from the surface of the steel plate.
  • the average spacing in the direction perpendicular to the rolling direction of the enriched regions where Mn and/or Si are concentrated is 1000 ⁇ m or less, and the number density of cracks with a depth of 3 ⁇ m or more and 10 ⁇ m or less on the surface of the steel sheet is 3 pieces/mm or more and 1000 pieces/mm or less, and contains bainite: 60% or more, retained austenite: 1% or more, martensite: 1% or more, and ferrite: 2% or more and less than 20%, and
  • the alloyed hot-dip galvanized steel sheet has a steel structure in which the average distance between the ultrahard phases, which is the average value of the closest distance between martensite and retained austenite, is 20 ⁇ m or less, and the alloyed hot-dip galvanized steel sheet has a tensile strength (TS) of 780 MPa or more.
  • TS tensile strength
  • TS tensile strength
  • the yield stress YS (hereinafter sometimes simply referred to as YS) and the yield ratio YR (hereinafter simply referred to as YR) are ) is effective.
  • YS and YR of a steel sheet are increased, press formability, particularly properties such as ductility, hole expandability, and bendability are generally reduced.
  • the steel sheets disclosed in Patent Documents 1 to 4 also have a TS of 780 MPa or more, high YS and YR, excellent press formability (ductility, hole expandability, and bendability), and impact resistance. It cannot be said that it has rupture properties (bending rupture properties and axial crush properties).
  • the present invention was developed in view of the above-mentioned current situation, and has a tensile strength TS of 780 MPa or more, a high yield stress YS, a high yield ratio YR, and excellent press formability (ductility, hole expandability).
  • the object of the present invention is to provide a galvanized steel sheet having good properties (bending properties and bending properties) and fracture resistance upon collision (bending fracture properties and axial crushing properties), and a method for manufacturing the same.
  • Another object of the present invention is to provide a member made of the above-mentioned galvanized steel sheet and a method for manufacturing the same.
  • the galvanized steel sheet here refers to a hot-dip galvanized steel sheet (hereinafter also referred to as GI) or an alloyed hot-dip galvanized steel sheet (hereinafter also referred to as GA).
  • GI hot-dip galvanized steel sheet
  • GA alloyed hot-dip galvanized steel sheet
  • the tensile strength TS is measured by a tensile test based on JIS Z 2241.
  • high yield stress YS and yield ratio YR means that YS measured in a tensile test based on JIS Z 2241 is one of the following (A) or (B) depending on the TS measured in the tensile test. Indicates that the formula is satisfied.
  • B When 980MPa ⁇ TS, 600MPa ⁇ YS and 0.61 ⁇ YR
  • excellent hole expansion property refers to a critical hole expansion rate ( ⁇ ) of 30% or more measured in a hole expansion test based on JIS Z 2256.
  • R (limit bending radius)/t (plate thickness) measured in a V-bending test based on JIS Z 2248 is expressed by the following formula (A) or (B) depending on the TS. It refers to satisfying the following.
  • excellent axial crushing properties means that the critical spacer thickness (ST) in the U-bending + close-contact bending test satisfies the following formula (A) or (B) depending on the TS.
  • ST critical spacer thickness
  • having excellent axial crushing characteristics means that the stroke at maximum load (SFmax) measured in the V-bending + orthogonal VDA bending test satisfies the following formula (A) or (B) depending on the TS. Point.
  • SFmax stroke at maximum load measured in the V-bending + orthogonal VDA bending test
  • having excellent bending rupture properties means that the critical spacer thickness (ST) in the above U-bending + close-contact bending test satisfies the above formula (A) or (B) depending on the TS, and It means that the stroke at maximum load (SFmax) measured in the bending + orthogonal VDA bending test satisfies the above formula (A) or (B) depending on the TS.
  • the above El (ductility), ⁇ (stretch flangeability), and R/t (bendability) are characteristics that indicate the ease of forming a steel plate during press forming (the degree of freedom in forming for press forming without cracking). It is.
  • the U-bending + close bending test is a test that simulates the deformation and fracture behavior of the vertical wall part in a collision test, and the critical spacer thickness (ST) measured in the U-bending + close bending test is It is an index showing the resistance to cracking (impact resistance properties for absorbing impact energy without breaking) of steel plates and components of automobile bodies.
  • V-bending + orthogonal VDA bending test is a test that simulates the deformation and fracture behavior of the bending ridge line part in a collision test, and the stroke (SFmax) at the maximum load measured in the V-bending + orthogonal VDA bending test is the energy This is an index showing the resistance of the absorbent member to cracking.
  • the present inventors have made extensive studies and have obtained the following knowledge.
  • the area ratio of tempered martensite is controlled to 10.0% or more, the island-like hard second phase (martensite + retained austenite) in contact with the ferrite grain boundaries is reduced, and the area ratio within the ferrite grains is reduced.
  • the ratio of the isolated fine island-like hard second phase (martensite + retained austenite)
  • the The critical spacer thickness (ST) measured in a U-bending + close bending test that simulates the deformation and fracture behavior of vertical walls in a crash test, which is an indicator of the impact resistance properties of steel plates and components of a car body
  • SFmax stroke at maximum load
  • a galvanized steel sheet comprising a base steel plate and a galvanized layer formed on the base steel plate, the base steel plate comprising: In mass%, C: 0.030% or more and 0.250% or less, Si: 0.01% or more and 0.75% or less, Mn: 2.00% or more and less than 3.50%, P: 0.001% or more and 0.100% or less, S: 0.0200% or less, Al: 0.010% or more and 2.000% or less, N: 0.0100% or less, , with the remainder consisting of Fe and unavoidable impurities;
  • Ferrite area ratio 20.0% or more and 80.0% or less
  • Fresh martensite area ratio 15.0% or less
  • Area ratio of retained austenite 3.0% or less
  • the component composition further includes, in mass%, Nb: 0.200% or less, Ti: 0.200% or less, V: 0.200% or less, B: 0.0100% or less, Cr: 1.000% or less, Ni: 1.000% or less, Mo: 1.000% or less, Sb: 0.200% or less, Sn: 0.200% or less, Cu: 1.000% or less, Ta: 0.100% or less, W: 0.500% or less, Mg: 0.0200% or less, Zn: 0.0200% or less, Co: 0.0200% or less, Zr: 0.1000% or less, Ca: 0.0200% or less, Se: 0.0200% or less, Te: 0.0200% or less, Ge: 0.0200% or less, As: 0.0500% or less, Sr: 0.0200% or less, Cs: 0.0200% or less, Hf: 0.0200% or less, Pb: 0.0200% or less,
  • the surface layer has a soft surface layer whose Vickers hardness is 85% or less with respect to the Vickers hardness at the 1/4 position of the plate thickness, Nano hardness of 300 points or more in a 50 ⁇ m x 50 ⁇ m area of the plate surface at 1/4 position and 1/2 depth in the plate thickness direction of the surface soft layer from the surface of the base steel plate, respectively.
  • the proportion of measurements where the nano-hardness of the plate surface at 1/4 of the depth in the thickness direction of the soft surface layer from the surface of the base steel sheet is 7.0 GPa or more is 1/4 of the depth in the thickness direction of the soft surface layer.
  • the standard deviation ⁇ of the nano-hardness of the plate surface at a position 1/4 of the thickness direction depth of the surface soft layer from the base steel plate surface is 1.8 GPa or less
  • the standard deviation ⁇ of the nano-hardness of the plate surface at a position 1/2 the thickness direction depth of the surface soft layer from the base steel plate surface is 2.2 GPa or less.
  • a galvanizing step is performed on the steel sheet to obtain a galvanized steel sheet; Applying a tension of 2.0 kgf/mm 2 or more to the galvanized steel sheet in a temperature range of 300 ° C. or higher and 450 ° C. or lower, Thereafter, the galvanized steel sheet is passed through 5 passes or more while being in contact with a roll having a diameter of 500 mm or more and 1500 mm or less for 1/4 rotation of the roll per pass, Then, a second cooling step of cooling to a cooling stop temperature of 250° C. or less; a reheating step of reheating the galvanized steel sheet to a temperature range of not less than the cooling stop temperature and not more than 440° C.
  • a method for producing a galvanized steel sheet comprising a cold rolling step of cold rolling a steel sheet at a rolling reduction of 20% or more and 80% or less to obtain a cold rolled steel sheet.
  • the method for producing a galvanized steel sheet according to [10] above wherein the annealing in the annealing step is performed in an atmosphere with a dew point of -30°C or higher.
  • a method for manufacturing a member comprising the step of subjecting the galvanized steel sheet according to [1] or [2] to at least one of forming and bonding to produce a member.
  • a method for producing a member including the step of subjecting the galvanized steel sheet according to [3] above to at least one of forming and bonding to produce a member.
  • a method for manufacturing a member comprising the step of subjecting the galvanized steel sheet according to [4] above to at least one of forming and bonding to produce a member.
  • a method for producing a member comprising the step of subjecting the galvanized steel sheet according to [5] above to at least one of forming and bonding to produce a member.
  • the tensile strength TS is 780 MPa or more, high yield stress YS and yield ratio YR, excellent press formability (ductility, hole expandability, and bendability), and rupture resistance at the time of collision.
  • a galvanized steel sheet having the following properties (bending fracture properties and axial crush properties) is obtained.
  • the members made of the galvanized steel sheet of the present invention have high strength and excellent press formability and impact resistance, so they are extremely advantageously applicable to automobile frame members and impact energy absorbing members. can do.
  • FIG. 13 This is an example of a SEM image of the present invention (Invention Example No. 13 of Examples).
  • (a) is a diagram for explaining the U-bending process (primary bending process) in the U-bending + close-contact bending test of the example.
  • (b) is a diagram for explaining the close bending process (secondary bending process) in the U-bending + close bending test of the example.
  • (a) is a diagram for explaining the V-bending process (primary bending process) in the V-bending + orthogonal VDA bending test of the example.
  • (b) is a diagram for explaining the orthogonal VDA bending process (secondary bending process) in the V-bending + orthogonal VDA bending test of the example.
  • (a) is a front view of a test member manufactured for carrying out an axial crush test of an example, in which a hat-shaped member and a steel plate are spot-welded.
  • (b) is a perspective view of the test member shown in FIG. 1(d).
  • (c) is a schematic diagram for explaining the axial crush test of the example.
  • the galvanized steel sheet of the present invention is a galvanized steel sheet comprising a base steel sheet and a galvanized layer formed on the surface of the base steel sheet, wherein the base steel sheet has a C: 0.030 in mass%.
  • the area ratio of ferrite is 20.0% or more and 80.0% or less
  • the area ratio of fresh martensite is 15.0% or less
  • the area ratio of retained austenite is 3.0% or less.
  • the area ratio of tempered bainite is 10.0% or less, the area ratio of tempered martensite is 10.0% to 70.0%, and island-like fresh martensite and island-like residual It has a steel structure in which the average grain size of austenite is 2.0 ⁇ m or less, the amount of diffusible hydrogen contained in the base steel sheet is 0.50 mass ppm or less, and the tensile strength is 780 MPa or more.
  • compositions First, the composition of the base steel sheet of the galvanized steel sheet according to one embodiment of the present invention will be described. Note that the units in the component compositions are all “mass %”, but hereinafter, unless otherwise specified, they will simply be expressed as "%".
  • C 0.030% or more and 0.250% or less C is an effective element for producing an appropriate amount of tempered martensite, bainite, tempered bainite, etc., and ensuring a TS of 780 MPa or more, high YS, and high YR. It is.
  • the C content is less than 0.030%, the area ratio of ferrite increases and it becomes difficult to make the TS 780 MPa or more. It also causes a decrease in YS and YR.
  • the C content exceeds 0.250%, the area ratio of fresh martensite increases, TS becomes excessively high, and El decreases.
  • the C content is set to 0.030% or more and 0.250% or less.
  • the C content is preferably 0.050% or more. Further, the C content is preferably 0.130% or less.
  • Si 0.01% or more and 0.75% or less Si promotes ferrite transformation during annealing and during the cooling process after annealing. That is, Si is an element that affects the area ratio of ferrite. Here, if the Si content is less than 0.01%, the area ratio of ferrite decreases and ductility decreases.
  • the Si content is set to 0.01% or more and 0.75% or less.
  • the Si content is preferably 0.10% or more. Further, the Si content is preferably 0.70% or less.
  • Mn 2.00% or more and less than 3.50%
  • Mn is an element that adjusts the area ratio of tempered martensite, bainite, and further tempered bainite.
  • the Mn content is less than 2.00%, the area ratio of ferrite increases and it becomes difficult to make the TS 780 MPa or more. It also causes a decrease in YS and YR.
  • the Mn content is 3.50% or more, the martensite transformation start temperature Ms (hereinafter also simply referred to as the Ms point or Ms) decreases, and the martensite generated in the first cooling step decreases.
  • the Mn content is set to 2.00% or more and less than 3.50%.
  • the Mn content is preferably 2.20% or more. Further, the Mn content is preferably 3.00% or less.
  • P 0.001% or more and 0.100% or less
  • P is an element that has a solid solution strengthening effect and increases the TS and YS of the steel sheet.
  • the P content is set to 0.001% or more.
  • P segregates at prior austenite grain boundaries and embrittles the grain boundaries. Therefore, during the V-bending test, voids are generated and cracks grow along the prior austenite grain boundaries, making it impossible to obtain the desired R/t.
  • the P content is set to 0.001% or more and 0.100% or less.
  • the P content is preferably 0.030% or less.
  • S 0.0200% or less S exists as a sulfide in steel.
  • the S content exceeds 0.0200%, voids are generated and cracks propagate starting from the sulfides during the V-bending test, making it impossible to obtain the desired R/t.
  • the S content is set to 0.0200% or less.
  • the S content is preferably 0.0080% or less. Note that although the lower limit of the S content is not particularly specified, it is preferable that the S content is 0.0001% or more due to constraints on production technology.
  • Al 0.010% or more and 2.000% or less
  • Al promotes ferrite transformation during annealing and during the cooling process after annealing. That is, Al is an element that affects the area ratio of ferrite.
  • the Al content is set to 0.010% or more and 2.000% or less.
  • Al content is preferably 0.015% or more. Further, the Al content is preferably 1.000% or less.
  • N 0.0100% or less N exists as a nitride in steel.
  • the N content exceeds 0.0100%, voids are generated and cracks propagate starting from the nitride during the V-bending test, making it impossible to obtain the desired R/t.
  • the N content is set to 0.0100% or less.
  • the N content is preferably 0.0050% or less. Note that, although the lower limit of the N content is not particularly specified, it is preferable that the N content is 0.0005% or more due to constraints on production technology.
  • the basic component composition of the base steel sheet of the galvanized steel sheet according to one embodiment of the present invention has been explained above, but the base steel sheet of the galvanized steel sheet according to one embodiment of the present invention contains the above-mentioned basic components and other than the above-mentioned basic components.
  • the remainder has a composition containing Fe (iron) and unavoidable impurities.
  • the base steel sheet of the galvanized steel sheet according to one embodiment of the present invention contains the above-mentioned basic components, with the remainder consisting of Fe and inevitable impurities.
  • the base steel sheet of the galvanized steel sheet according to one embodiment of the present invention may contain at least one selected from the following optional components.
  • the effects of the present invention can be obtained for the optional components shown below as long as they are contained in amounts below the upper limit shown below, so no lower limit is set in particular.
  • the following arbitrary elements are contained below the preferable lower limit value mentioned later, the said elements shall be contained as an unavoidable impurity.
  • Nb 0.200% or less
  • Ti 0.200% or less
  • V 0.200% or less
  • B 0.0100% or less
  • Cr 1.000% or less
  • Ni 1.000% or less
  • Mo 1.000% or less
  • Sb 0.200% or less
  • Sn 0.200% or less
  • Cu 1.000% or less
  • Ta 0.100% or less
  • W 0.500% or less
  • Mg 0.200% or less
  • Nb 0.200% or less Nb increases TS, YS, and YR by forming fine carbides, nitrides, or carbonitrides during hot rolling or annealing.
  • the Nb content is 0.001% or more.
  • the Nb content is more preferably 0.005% or more.
  • the Nb content exceeds 0.200%, large amounts of coarse precipitates and inclusions may be generated. In such cases, coarse precipitates and inclusions become starting points for voids and cracks during hole expansion tests, V-bending tests, U-bending + close bending tests, and V-bending + orthogonal VDA bending tests, so that the desired ⁇ , R/t, ST and SFmax may not be obtained. Therefore, when Nb is contained, the Nb content is preferably 0.200% or less.
  • the Nb content is more preferably 0.060% or less.
  • Ti 0.200% or less Like Nb, Ti increases TS, YS, and YR by forming fine carbides, nitrides, or carbonitrides during hot rolling or annealing. In order to obtain such an effect, it is preferable that the Ti content is 0.001% or more. The Ti content is more preferably 0.005% or more. On the other hand, if the Ti content exceeds 0.200%, a large amount of coarse precipitates and inclusions may be formed.
  • the Ti content is preferably 0.200% or less.
  • the Ti content is more preferably 0.060% or less.
  • V 0.200% or less Like Nb and Ti, V increases TS and YS by forming fine carbides, nitrides, or carbonitrides during hot rolling or annealing. In order to obtain such an effect, it is preferable that the V content is 0.001% or more. The V content is more preferably 0.005% or more. The V content is more preferably 0.010% or more, and even more preferably 0.030% or more. On the other hand, when the V content exceeds 0.200%, large amounts of coarse precipitates and inclusions may be generated.
  • V content is preferably 0.200% or less.
  • the V content is more preferably 0.060% or less.
  • B 0.0100% or less
  • B is an element that improves hardenability by segregating at austenite grain boundaries. Further, B is an element that controls the generation and grain growth of ferrite during cooling after annealing. In order to obtain such an effect, it is preferable that the B content is 0.0001% or more. The B content is more preferably 0.0002% or more. The B content is more preferably 0.0005% or more, and even more preferably 0.0007% or more. On the other hand, if the B content exceeds 0.0100%, cracks may occur inside the steel sheet during hot rolling.
  • the internal crack becomes the starting point of the crack, so the desired ⁇ , R/t, ST and SFmax can be obtained. may not be possible. Therefore, when B is included, the B content is preferably 0.0100% or less. The B content is more preferably 0.0050% or less.
  • the Cr content is preferably 0.0005% or more. Further, the Cr content is more preferably 0.010% or more. Cr is more preferably 0.030% or more, and even more preferably 0.050% or more. On the other hand, if the Cr content exceeds 1.000%, the area ratio of fresh martensite increases, hole expandability and V-bending test bendability decrease, and the desired ⁇ and R/t may not be obtained. There is. Therefore, when Cr is contained, the Cr content is preferably 1.000% or less. Further, the Cr content is more preferably 0.800% or less, still more preferably 0.700% or less.
  • Ni 1.000% or less
  • Ni is an element that improves hardenability, and the addition of Ni produces a large amount of tempered martensite, thereby increasing TS, YS, and YR.
  • the Ni content be 0.005% or more.
  • the Ni content is more preferably 0.020% or more.
  • the Ni content is more preferably 0.040% or more, and even more preferably 0.060% or more.
  • the Ni content exceeds 1.000%, the area ratio of fresh martensite increases, hole expandability and V-bending test bendability decrease, and the desired ⁇ and R/t may not be obtained. There is. Therefore, when Ni is contained, the Ni content is preferably 1.000% or less.
  • the Ni content is more preferably 0.800% or less.
  • the Ni content is more preferably 0.600% or less, and even more preferably 0.400% or less.
  • Mo 1.000% or less
  • Mo is an element that improves hardenability, and the addition of Mo generates a large amount of tempered martensite, thereby increasing TS, YS, and YR.
  • the Mo content is 0.010% or more.
  • Mo content is more preferably 0.030% or more.
  • the Mo content exceeds 1.000%, the area ratio of fresh martensite increases, hole expandability and V-bending test bendability decrease, and the desired ⁇ and R/t may not be obtained. There is. Therefore, when Mo is contained, the Mo content is preferably 1.000% or less.
  • the Mo content is more preferably 0.500% or less, still more preferably 0.450% or less, and even more preferably 0.400% or less.
  • the Mo content is more preferably 0.350% or less, and even more preferably 0.300% or less.
  • Sb 0.200% or less
  • Sb is an effective element for suppressing the diffusion of C near the surface of the steel sheet during annealing and controlling the formation of a soft layer near the surface of the steel sheet. If the soft layer increases excessively near the surface of the steel sheet, it may be difficult to increase the TS to 780 MPa or more. Furthermore, there is a possibility that YS will be lowered. Therefore, it is preferable that the Sb content is 0.002% or more. The Sb content is more preferably 0.005% or more. On the other hand, when the Sb content exceeds 0.200%, a soft layer is not formed near the surface of the steel sheet, which may lead to a decrease in ⁇ , R/t, ST, and SFmax. Therefore, when Sb is contained, the Sb content is preferably 0.200% or less. The Sb content is more preferably 0.020% or less.
  • Sn 0.200% or less
  • Sn is an effective element for suppressing the diffusion of C near the surface of the steel sheet during annealing and controlling the formation of a soft layer near the surface of the steel sheet. If the soft layer increases excessively near the surface of the steel sheet, it may be difficult to increase the TS to 780 MPa or more. Furthermore, there is a possibility that YS will be lowered. Therefore, it is preferable that the Sn content is 0.002% or more. The Sn content is more preferably 0.005% or more. On the other hand, if the Sn content exceeds 0.200%, a soft layer will not be formed near the surface of the steel sheet, which may cause a decrease in ⁇ , R/t, ST, and SFmax. Therefore, when Sn is contained, the Sn content is preferably 0.200% or less. The Sn content is more preferably 0.020% or less.
  • Cu 1.000% or less
  • Cu is an element that improves hardenability, so adding Cu generates a large amount of tempered martensite, increasing TS, YS, and YR.
  • the Cu content is 0.005% or more.
  • the Cu content is more preferably 0.008% or more, and even more preferably 0.010% or more.
  • the Cu content is more preferably 0.020% or more.
  • the area ratio of fresh martensite may increase excessively. Further, a large amount of coarse precipitates and inclusions may be generated.
  • the Cu content is preferably 1.000% or less.
  • the Cu content is more preferably 0.200% or less.
  • Ta 0.100% or less Like Ti, Nb, and V, Ta increases TS, YS, and YR by forming fine carbides, nitrides, or carbonitrides during hot rolling and annealing. let In addition, Ta is partially dissolved in Nb carbides and Nb carbonitrides to form composite precipitates such as (Nb, Ta) (C, N). This suppresses coarsening of precipitates and stabilizes precipitation strengthening. This further improves TS and YS. In order to obtain such an effect, the Ta content is preferably 0.001% or more. The Ta content is more preferably 0.002% or more, and even more preferably 0.004% or more.
  • the Ta content is preferably 0.100% or less.
  • the Ta content is more preferably 0.090% or less, and even more preferably 0.080% or less.
  • W 0.500% or less
  • W is an element that improves hardenability, and the addition of W generates a large amount of tempered martensite, thereby increasing TS, YS, and YR.
  • the W content is 0.001% or more.
  • the W content is more preferably 0.030% or more.
  • the W content exceeds 0.500%, the area ratio of fresh martensite increases, hole expandability and V-bending test bendability decrease, and the desired ⁇ and R/t may not be obtained. There is. Therefore, when W is contained, the W content is preferably 0.500% or less.
  • the W content is more preferably 0.450% or less, still more preferably 0.400% or less. It is even more preferable that the W content is 0.300% or less.
  • Mg 0.0200% or less
  • Mg is an effective element for spheroidizing the shape of inclusions such as sulfides and oxides and improving the hole expandability and bendability of the steel sheet.
  • the Mg content is 0.0001% or more.
  • the Mg content is more preferably 0.0005% or more, and even more preferably 0.0010% or more.
  • the Mg content exceeds 0.0200%, large amounts of coarse precipitates and inclusions may be formed. In such cases, excessively coarse precipitates and inclusions become starting points for voids and cracks during the hole expansion test, V-bending test, U-bending + close-contact bending test, and V-bending + orthogonal VDA bending test.
  • the Mg content is preferably 0.0200% or less.
  • the Mg content is more preferably 0.0180% or less, and even more preferably 0.0150% or less.
  • Zn 0.0200% or less
  • Zn is an effective element for spheroidizing the shape of inclusions and improving the hole expandability and bendability of the steel sheet.
  • the Zn content is preferably 0.0010% or more.
  • the Zn content is more preferably 0.0020% or more, and even more preferably 0.0030% or more.
  • the Zn content exceeds 0.0200%, large amounts of coarse precipitates and inclusions may be formed.
  • the Zn content is preferably 0.0200% or less.
  • the Zn content is more preferably 0.0180% or less, and even more preferably 0.0150% or less.
  • Co 0.0200% or less
  • Co is an effective element for spheroidizing the shape of inclusions and improving the hole expandability and bendability of the steel sheet.
  • the Co content is preferably 0.0010% or more.
  • the Co content is more preferably 0.0020% or more, and even more preferably 0.0030% or more.
  • the Co content exceeds 0.0200%, a large amount of coarse precipitates and inclusions may be formed. In such cases, excessively coarse precipitates and inclusions become starting points for voids and cracks during hole expansion tests, V-bending tests, U-bending + close bending tests, and V-bending + orthogonal VDA bending tests. ⁇ , R/t, ST and SFmax may not be obtained. Therefore, when Co is contained, the Co content is preferably 0.0200% or less.
  • the Co content is more preferably 0.0180% or less, and even more preferably 0.0150% or less.
  • Zr 0.1000% or less
  • Zr is an effective element for making the shape of inclusions spherical and improving the hole expandability and bendability of the steel sheet.
  • the Zr content is preferably 0.0010% or more.
  • the Zr content exceeds 0.1000%, excessively coarse precipitates and inclusions may be detected in hole expansion tests, V-bending tests, U-bending + close bending tests, and V-bending + orthogonal VDA bending tests.
  • the desired ⁇ , R/t, ST and SFmax may not be obtained because it becomes a starting point for voids and cracks. Therefore, when Zr is contained, the Zr content is preferably 0.1000% or less.
  • the Zr content is more preferably 0.0300% or less, and even more preferably 0.0100% or less.
  • Ca 0.0200% or less Ca exists as inclusions in steel.
  • the Ca content is preferably 0.0200% or less.
  • the Ca content is preferably 0.0020% or less.
  • the Ca content is more preferably 0.0019% or less, and even more preferably 0.0018% or less.
  • the lower limit of the Ca content is not particularly limited, but the Ca content is preferably 0.0005% or more.
  • the Ca content is more preferably 0.0010% or more.
  • Se 0.0200% or less, Te: 0.0200% or less, Ge: 0.0200% or less, As: 0.0500% or less, Sr: 0.0200% or less, Cs: 0.0200% or less, Hf: 0.0200% or less, Pb: 0.0200% or less, Bi: 0.0200% or less, and REM: 0.0200% or less Se, Te, Ge, As, Sr, Cs, Hf, Pb, Bi, and REM are all is also an effective element for improving the hole expandability and bendability of steel sheets. In order to obtain such an effect, it is preferable that the content of Se, Te, Ge, As, Sr, Cs, Hf, Pb, Bi, and REM is each 0.0001% or more.
  • the content of Bi and REM is preferably 0.0200% or less, and the content of As is preferably 0.0500% or less.
  • the Se content is more preferably 0.0005% or more, and even more preferably 0.0008% or more.
  • the Se content is more preferably 0.0180% or less, and even more preferably 0.0150% or less.
  • the Te content is more preferably 0.0005% or more, and even more preferably 0.0008% or more.
  • the Te content is more preferably 0.0180% or less, and even more preferably 0.0150% or less.
  • the Ge content is more preferably 0.0005% or more, and even more preferably 0.0008% or more.
  • the Ge content is more preferably 0.0180% or less, and even more preferably 0.0150% or less.
  • As content it is more preferred that it is 0.0010% or more, and it is still more preferred that it is 0.0015% or more.
  • As content it is more preferred that it is 0.0400% or less, and it is still more preferred that it is 0.0300% or less.
  • the Sr content is more preferably 0.0005% or more, and even more preferably 0.0008% or more.
  • the Sr content is more preferably 0.0180% or less, and even more preferably 0.0150% or less.
  • the Cs content is more preferably 0.0005% or more, and even more preferably 0.0008% or more.
  • the Cs content is more preferably 0.0180% or less, and even more preferably 0.0150% or less.
  • the Hf content is more preferably 0.0005% or more, and even more preferably 0.0008% or more.
  • the Hf content is more preferably 0.0180% or less, and even more preferably 0.0150% or less.
  • the Pb content is more preferably 0.0005% or more, and even more preferably 0.0008% or more.
  • the Pb content is more preferably 0.0180% or less, and even more preferably 0.0150% or less.
  • the Bi content is more preferably 0.0005% or more, and even more preferably 0.0008% or more.
  • Bi is more preferably 0.0180% or less, and even more preferably 0.0150% or less.
  • REM is more preferably 0.0005% or more, and even more preferably 0.0008% or more.
  • REM is more preferably 0.0180% or less, and even more preferably 0.0150% or less.
  • Area ratio of ferrite 20.0% or more and 80.0% or less
  • Soft ferrite is a phase that improves ductility. It is also a necessary phase to generate isolated island-like fresh martensite and isolated island-like retained austenite within grains, and to suppress the connection of voids and the propagation of cracks.
  • the area ratio of ferrite is set to 20.0% or more.
  • the area ratio of ferrite increases excessively, it becomes difficult to increase the TS to 780 MPa or more. It also causes a decrease in YS and YR. Therefore, the area ratio of ferrite is set to 80.0% or less. Further, the area ratio of ferrite is preferably 30.0% or more.
  • Fresh martensite area ratio 15.0% or less (including 0.0%)
  • the area ratio of fresh martensite is set to 15.0% or less.
  • the area ratio of fresh martensite is preferably 10.0% or less. Note that the lower limit of the area ratio of fresh martensite is not particularly limited, and may be 0.0%.
  • the fresh martensite referred to here is martensite that is still quenched (not tempered).
  • the fresh martensite referred to herein also includes (isolated) island-like fresh martensite within ferrite grains, which will be described later.
  • Area ratio of retained austenite 3.0% or less (including 0.0%)
  • the area ratio of retained austenite is set to 3.0% or less.
  • the area ratio of retained austenite is preferably 2.5% or less, more preferably 2.0% or less.
  • the lower limit of the area ratio of retained austenite is not particularly limited, but is preferably 0.1% or more, more preferably 0.2% or more.
  • the retained austenite referred to herein also includes (isolated) island-like retained austenite within ferrite grains, which will be described later.
  • a tension of 2.0 kgf/mm 2 or more is applied in a temperature range of 300°C or more and 450°C or less, and then the steel plate is heated to a diameter of 500 mm or more and 1500 mm or less per pass.
  • untransformed austenite undergoes deformation-induced transformation to become fresh martensite, and in the subsequent reheating process, the fresh martensite is tempered.
  • the area ratio of fresh martensite to 15.0% or less and the volume ratio of retained austenite to 3.0% or less, it is possible to secure the desired area ratio of tempered martensite. Become.
  • the value obtained by dividing the sum of the area ratios of island-like fresh martensite and island-like retained austenite in the ferrite grains by the sum of the area ratio of fresh martensite and retained austenite in the entire steel sheet 0.65 or more , as shown in Figure 1, isolated island-like fresh martensite (M') and isolated island-like retained austenite (RA') within ferrite (F) grains are tempered martensite (TM) existing at ferrite grain boundaries. It is finer than the hard second phase (fresh martensite (M) + retained austenite (RA)), and although it can serve as a void generation site, it is a structure that is unlikely to be involved in void connection or crack propagation.
  • the value obtained by dividing the total area ratio of isolated island-like fresh martensite and isolated island-like retained austenite in the ferrite grain by the sum of the area ratio of fresh martensite and retained austenite ((M'+RA' )/(M+RA)) shall be 0.65 or more. Further, the value obtained by dividing the sum of the area ratios of isolated island-like fresh martensite and isolated island-like retained austenite in the ferrite grain by the sum of the area ratio of fresh martensite and retained austenite is preferably 0. It is 70 or more.
  • the upper limit of the value obtained by dividing the sum of the area ratios of isolated island-like fresh martensite and isolated island-like retained austenite in the ferrite grain by the sum of the area ratio of fresh martensite and the volume ratio of retained austenite is not particularly limited, but This value is preferably 0.94 or less, more preferably 0.92 or less.
  • Area ratio of bainite and tempered bainite 10.0% or less (including 0.0%) If the area ratio of the tempered bainite produced in the first cooling process and the bainite produced in the reheating process is tempered, the desired area ratio of tempered martensite cannot be obtained, and the TS of 780 MPa or more It will be difficult to secure. Therefore, the area ratio (B+BT) of bainite and tempered bainite is 10.0% or less. Further, the area ratio of bainite and tempered bainite is preferably 8.0% or less. The area ratio of bainite and tempered bainite may be 0.0% or less.
  • tempered martensite Area ratio of tempered martensite: 10.0% or more and 70.0% or less
  • the hard second phase fresh martensite + retained austenite
  • tempered martensite is produced by applying a tension of 2.0 kgf/mm2 or more in a temperature range of 300°C to 450°C during the second cooling step in the manufacturing method described later, and then applying a tension of 2.0 kgf/mm2 or more to the galvanized steel sheet in one pass.
  • the untransformed austenite undergoes deformation-induced transformation to become fresh martensite by contacting a roll with a per-diameter of 500 mm or more and 1500 mm or less for 1/4 rotation of the roll and passing the roll for 5 or more passes.
  • This structure is obtained by tempering the sites and exists mostly at ferrite grain boundaries.
  • the above-mentioned tempered martensite has a structure necessary to obtain desired ⁇ , R/t, ST and SFmax. Therefore, the area ratio of tempered martensite is set to 10.0% or more.
  • the area ratio of tempered martensite is preferably 20.0% or more.
  • the area ratio of tempered martensite is 70.0% or less.
  • the area ratio of tempered martensite is preferably 60.0% or less.
  • Average crystal grain size of island-like fresh martensite and island-like retained austenite within ferrite grains 2.0 ⁇ m or less
  • the average crystal grain size of island-like fresh martensite and island-like retained austenite (M'+RA') within the ferrite grains is set to 2.0 ⁇ m or less.
  • the average crystal grain size of the island-like fresh martensite and the island-like retained austenite within the ferrite grains is preferably 1.0 ⁇ m or less.
  • the average crystal grain size of the island-like fresh martensite and the island-like retained austenite in the ferrite grains is preferably 0.1 ⁇ m or more, more preferably 0.2 ⁇ m or more.
  • the area ratio of the remaining structures other than those mentioned above is preferably 10.0% or less.
  • the area ratio of the remaining tissue is more preferably 5.0% or less. Further, the area ratio of the remaining tissue may be 0.0%.
  • the residual structure is not particularly limited, and examples thereof include carbides such as pearlite and cementite.
  • the type of residual tissue can be confirmed, for example, by observation using a scanning electron microscope (SEM).
  • the area ratio of ferrite, bainite, tempered bainite, tempered martensite, and hard second phase is measured as follows at the 1/4 thickness position of the base steel plate. That is, the sample is cut out so that the plate thickness cross section (L cross section) parallel to the rolling direction of the steel plate serves as the observation surface. Next, the observation surface of the sample is polished with diamond paste, and then final polished with alumina. Next, the observation surface of the sample was exposed to 3 vol. % nital to reveal the tissue. Next, the observation position is set at 1/4 of the thickness of the steel plate, and 5 fields of view are observed using an SEM at a magnification of 3000 times.
  • the area of each constituent structure (ferrite, bainite, tempered bainite, tempered martensite, and hard second phase (fresh martensite + retained austenite)) was measured using Adobe Photoshop from Adobe Systems. The area ratio divided by is calculated for five fields of view, and these values are averaged to determine the area ratio of each tissue.
  • Ferrite A black region with a block-like shape. In addition, it contains almost no carbide. Furthermore, isolated island-like fresh martensite and isolated island-like retained austenite within the ferrite grains are not included in the area ratio of ferrite.
  • Bainite and tempered bainite A black to dark gray area, with a lumpy or irregular shape. It also contains a relatively small amount of carbide.
  • Tempered martensite A gray area with an amorphous shape. It also contains a relatively large number of carbides. Hard second phase (retained austenite + fresh martensite): This is a white to light gray region with an amorphous shape. Also, it does not contain carbide. Carbide: A white region with a dotted or linear shape. It is included in bainite, tempered bainite, and tempered martensite. Remnant structure: Examples include the above-mentioned pearlite and cementite, and their forms are known.
  • the total area of isolated island-like fresh martensite and isolated island-like retained austenite within ferrite grains can be calculated as follows: The average area is determined by dividing by the number of island-like retained austenites, and the 1/2 power is taken as the average crystal grain size.
  • the area ratio of retained austenite is measured as follows. That is, the base steel plate is mechanically ground in the thickness direction (depth direction) to a position of 1/4 of the plate thickness, and then chemically polished with oxalic acid to form an observation surface. Then, the observation surface is observed by X-ray diffraction. MoK ⁇ rays were used for the incident X-rays, and the diffraction intensity of the (200), (211) and (220) planes of BCC iron was compared with the (200), (220) and (311) planes of FCC iron (austenite). The ratio of the diffraction intensities of each surface is determined, and the volume fraction of retained austenite is calculated from the ratio of the diffraction intensities of each surface. Then, assuming that the retained austenite is three-dimensionally homogeneous, the volume fraction of the retained austenite is defined as the area fraction of the retained austenite.
  • the area ratio of fresh martensite is determined by subtracting the area ratio of retained austenite from the area ratio of the hard second phase determined as described above.
  • [Area ratio of fresh martensite (%)] [Area ratio of hard second phase (%)] - [Area ratio of retained austenite (%)]
  • Amount of diffusible hydrogen (in steel) contained in the base steel sheet 0.50 mass ppm or less
  • the amount of diffusible hydrogen in the steel sheet exceeds 0.50 mass ppm, the desired ⁇ , R/t, ST and SFmax I can't get it.
  • the amount of diffusible hydrogen in the steel sheet is preferably 0.25 mass ppm or less.
  • the lower limit of the amount of diffusible hydrogen in the steel sheet is not particularly specified, it is preferable that the amount of diffusible hydrogen in the steel sheet is 0.01 mass ppm or more due to constraints on production technology.
  • the base steel plate on which the amount of diffusible hydrogen is measured may be a high-strength steel plate before plating, or a base steel plate that is a high-strength galvanized steel plate after galvanizing and before processing.
  • it may be a base steel plate of a steel plate that has been subjected to processes such as punching and stretch flange forming after galvanizing, or it may be a base part of a product manufactured by welding the processed steel plate. I don't mind.
  • the method for measuring the amount of diffusible hydrogen in a steel sheet is as follows. A test piece with a length of 30 mm and a width of 5 mm is taken, and the hot-dip galvanized layer or the alloyed hot-dip galvanized layer is alkali-removed. Thereafter, the amount of hydrogen released from the test piece is measured by temperature programmed desorption analysis. Specifically, after continuously heating from room temperature (-5 to 55°C) to 300°C at a heating rate of 200°C/h, the test piece was cooled to room temperature, and the cumulative hydrogen released from the test piece from room temperature to 210°C was measured. The amount is measured and taken as the amount of diffusible hydrogen in the steel sheet.
  • the room temperature should be within the range of local temperature changes over a one-year period, taking into account production in various countries around the world. Generally, the temperature is preferably in the range of 10 to 50°C.
  • the base steel sheet of the galvanized steel sheet according to one embodiment of the present invention preferably has a soft surface layer on the surface of the base steel sheet.
  • the soft surface layer contributes to suppressing the propagation of bending cracks during press molding and car body collisions, further improving the bending fracture resistance.
  • the surface soft layer means a decarburized layer, and is a surface layer region having a Vickers hardness of 85% or less of the Vickers hardness of the cross section at the 1/4 thickness position.
  • the surface soft layer is formed in an area of 200 ⁇ m or less in the thickness direction from the surface of the base steel sheet.
  • the lower limit of the thickness of the surface soft layer is not particularly determined, it is preferably 8 ⁇ m or more, and more preferably more than 17 ⁇ m. Vickers hardness is measured based on JIS Z 2244-1 (2020) with a load of 10 gf.
  • the proportion of measurements where the nanohardness of the plate surface at 1/4 of the depth in the thickness direction of the surface soft layer from the surface of the base steel sheet was 7.0 GPa or more was the same as the thickness of the surface soft layer.
  • the ratio of the number of measurements where the nanohardness of the plate surface at 1/4 of the depth in the thickness direction of the soft layer is 7.0 GPa or more is relative to the total number of measurements at 1/4 of the depth in the thickness direction of the surface soft layer. is preferably 0.10 or less.
  • the ratio of nanohardness of 7.0 GPa or more is 0.10 or less, it means that the ratio of hard structures (martensite, etc.), inclusions, etc. is small; It becomes possible to further suppress the generation and connection of voids during press molding and collision, as well as the propagation of cracks, resulting in excellent R/t and SFmax.
  • the standard deviation ⁇ of the nano-hardness of the plate surface at a position 1/4 of the depth in the thickness direction of the surface soft layer from the steel plate surface is 1.8 GPa or less, and The standard deviation ⁇ of the nanohardness of the plate surface at the 1/2 position is 2.2 GPa or less.
  • the standard deviation ⁇ of the nano-hardness of the plate surface at 1/4 of the depth in the thickness direction of the soft layer is 1.8 GPa or less, and furthermore, the standard deviation ⁇ of the nanohardness of the plate surface at 1/4 of the depth in the thickness direction of the surface soft layer from the steel plate surface is 1/2 of the depth in the thickness direction of the surface soft layer.
  • the standard deviation ⁇ of the nanohardness of the plate surface is 2.2 GPa or less.
  • the standard deviation ⁇ of the nano-hardness of the plate surface at a position 1/4 of the depth in the thickness direction of the surface soft layer from the steel plate surface is 1.8 GPa or less, and If the standard deviation ⁇ of the nanohardness of the plate surface at the 1/2 position is 2.2 GPa or less, it means that the difference in microstructure hardness in the micro region is small, and it is difficult to prevent the formation and connection of voids during press forming and collision. It becomes possible to further suppress the propagation of cracks, and excellent R/t and SFmax can be obtained.
  • a preferable range of the standard deviation ⁇ of the nanohardness of the plate surface at a position 1/4 of the thickness direction depth of the surface soft layer from the base steel plate surface is preferably 1.7 GPa or less.
  • a more preferable range of the standard deviation ⁇ of the nano-hardness of the plate surface at 1/2 the thickness direction depth of the surface soft layer from the base steel plate surface is 2.1 GPa or less.
  • the nanohardness of the plate surface at the 1/4 position and 1/2 position of the depth in the thickness direction is the hardness measured by the following method.
  • Nanohardness is measured using Hysitron's tribo-950 with a Berkovich-shaped diamond indenter under the conditions of load: 500 ⁇ N, measurement area: 50 ⁇ m ⁇ 50 ⁇ m, and dot spacing: 2 ⁇ m. Further, mechanical polishing is performed to 1/2 the depth in the thickness direction of the surface soft layer, buff polishing with diamond and alumina, and further colloidal silica polishing. Then, the nanohardness is measured using Hysitron's tribo-950 with a Berkovich-shaped diamond indenter under the conditions of load: 500 ⁇ N, measurement area: 50 ⁇ m ⁇ 50 ⁇ m, and dot spacing: 2 ⁇ m.
  • the galvanized steel sheet according to an embodiment of the present invention has a metal plating layer (first plating layer, pre-plating layer) (in addition, a metal plating layer (first plating layer) on one or both surfaces of the base steel sheet. ) preferably has a hot-dip galvanized layer (excluding the galvanized layer of the alloyed hot-dip galvanized layer).
  • the metal plating layer is preferably a metal electroplating layer, and below, the metal electroplating layer will be explained as an example.
  • the metal electroplating layer on the outermost layer contributes to suppressing the occurrence of bending cracks during press forming and when a vehicle body collides, so that the bending rupture resistance is further improved.
  • the thickness of the soft layer can be increased, and the axial crushing properties can be made very excellent.
  • the present invention by having a metal plating layer, it is possible to obtain the same axial crushing characteristics as when the soft layer thickness is large even if the soft layer thickness is small and the dew point is ⁇ 20° C. or lower.
  • the metal species of the metal electroplating layer include Cr, Mn, Fe, Co, Ni, Cu, Ga, Ge, As, Ru, Rh, Pd, Ag, Cd, In, Sn, Sb, Os, Ir, Rt, Any of Au, Hg, Ti, Pb, and Bi may be used, but Fe is more preferable.
  • a Fe-based electroplated layer will be explained as an example.
  • the amount of the Fe-based electroplated layer deposited is more than 0 g/m 2 , preferably 2.0 g/m 2 or more.
  • the upper limit of the amount of the Fe-based electroplated layer per side is not particularly limited, but from the viewpoint of cost, it is preferable that the amount of the Fe-based electroplated layer applied per side is 60 g/m 2 or less.
  • the amount of the Fe-based electroplated layer deposited is preferably 50 g/m 2 or less, more preferably 40 g/m 2 or less, and even more preferably 30 g/m 2 or less.
  • the adhesion amount of the Fe-based electroplating layer is measured as follows. A sample with a size of 10 x 15 mm is taken from a Fe-based electroplated steel plate and embedded in resin to form a cross-sectional embedded sample. Three arbitrary points on the same cross section were observed using a scanning electron microscope (SEM) at an accelerating voltage of 15 kV and a magnification of 2,000 to 10,000 times depending on the thickness of the Fe-based plating layer. By multiplying the average value by the specific gravity of iron, it is converted into the amount of adhesion per one side of the Fe-based plating layer.
  • SEM scanning electron microscope
  • Fe-based electroplating layers include Fe-B alloy, Fe-C alloy, Fe-P alloy, Fe-N alloy, Fe-O alloy, Fe-Ni alloy, Fe-Mn alloy, Fe- An alloy plating layer such as Mo alloy or Fe-W alloy can be used.
  • the composition of the Fe-based electroplated layer is not particularly limited, but 1 selected from the group consisting of B, C, P, N, O, Ni, Mn, Mo, Zn, W, Pb, Sn, Cr, V, and Co.
  • the composition contains two or more elements in a total of 10% by mass or less, with the remainder consisting of Fe and unavoidable impurities.
  • the C content is preferably 0.08% by mass or less.
  • the tensile strength of the galvanized steel sheet according to one embodiment of the present invention is 780 MPa or more.
  • the yield stress (YS), yield ratio (YR), total elongation (El), critical hole expansion ratio ( ⁇ ), and critical spacer in the U-bending + close-contact bending test of the zinc-based plated steel sheet according to an embodiment of the present invention The reference values for the thickness (ST) and the stroke at maximum load (SFmax) in the V-bending + orthogonal VDA bending test, and the presence or absence of fracture (appearance cracking) in the axial crushing test are as described above.
  • tensile strength (TS), yield stress (YS), yield ratio (YR), and total elongation (El) are measured by a tensile test based on JIS Z 2241, which will be described later in Examples.
  • the critical hole expansion rate ( ⁇ ) is measured by a hole expansion test based on JIS Z 2256, which will be described later in Examples.
  • the critical spacer thickness (ST) is measured by the U-bending + close-contact bending test described later in Examples.
  • the stroke (SFmax) at maximum load in the V-bending + orthogonal VDA bending test is measured by the V-bending + orthogonal VDA bending test described later in the Examples.
  • the presence or absence of fracture (appearance cracking) in the axial crushing test is determined by the axial crushing test described later in Examples.
  • Galvanized layer (second plating layer)
  • a galvanized steel sheet according to an embodiment of the present invention has a galvanized layer formed on a base steel sheet (on the surface of the base steel sheet or on the surface of the metal plating layer if a metal plating layer is formed), and The plating layer may be provided only on one surface of the base steel plate, or may be provided on both surfaces. That is, the steel sheet of the present invention has a base steel plate, and a second plating layer (a galvanized layer, an aluminum plating layer, etc.) may be formed on the base steel plate.
  • a metal plating layer (a first plating layer (excluding the second plating layer of the galvanized layer)) and a second plating layer (a zinc plating layer, an aluminum plating layer, etc.) may be formed in this order on the base steel sheet.
  • the galvanized layer here refers to a plating layer containing Zn as a main component (Zn content is 50.0% or more), and includes, for example, a hot-dip galvanized layer and an alloyed hot-dip galvanized layer.
  • the hot-dip galvanized layer is preferably composed of, for example, Zn, 20.0% by mass or less of Fe, and 0.001% by mass or more and 1.0% by mass or less of Al.
  • the hot-dip galvanized layer may optionally include one selected from the group consisting of Pb, Sb, Si, Sn, Mg, Mn, Ni, Cr, Co, Ca, Cu, Li, Ti, Be, Bi, and REM.
  • the total content of a species or two or more elements may be 0.0% by mass or more and 3.5% by mass or less.
  • the Fe content of the hot-dip galvanized layer is more preferably less than 7.0% by mass. Note that the remainder other than the above elements are unavoidable impurities.
  • the alloyed hot-dip galvanized layer is preferably composed of, for example, 20% by mass or less of Fe and 0.001% by mass or more and 1.0% by mass or less of Al. Additionally, the alloyed hot-dip galvanized layer may optionally be selected from the group consisting of Pb, Sb, Si, Sn, Mg, Mn, Ni, Cr, Co, Ca, Cu, Li, Ti, Be, Bi, and REM. One or more types of elements may be contained in a total amount of 0% by mass or more and 3.5% by mass or less.
  • the Fe content of the alloyed hot-dip galvanized layer is more preferably 7.0% by mass or more, and still more preferably 8.0% by mass or more. Further, the Fe content of the alloyed hot-dip galvanized layer is more preferably 15.0% by mass or less, still more preferably 12.0% by mass or less. Note that the remainder other than the above elements are unavoidable impurities.
  • the amount of plating deposited on one side of the galvanized layer is not particularly limited, but is preferably 20 g/m 2 or more and 80 g/m 2 or less.
  • the plating adhesion amount of the galvanized layer is measured as follows. That is, a treatment solution is prepared by adding 0.6 g of a corrosion inhibitor for Fe (Ivit 700BK (registered trademark) manufactured by Asahi Chemical Co., Ltd.) to 1 L of a 10% by mass hydrochloric acid aqueous solution. Next, a galvanized steel sheet serving as a test material is immersed in the treatment liquid to dissolve the galvanized layer. Then, by measuring the amount of mass loss of the test material before and after melting, and dividing that value by the surface area of the base steel sheet (the surface area of the part covered with plating), the amount of plating coating (g/m 2 ) is calculated.
  • a corrosion inhibitor for Fe Ivit 700BK (registered trademark) manufactured by Asahi Chemical Co., Ltd.
  • the thickness of the galvanized steel sheet according to an embodiment of the present invention is not particularly limited, but is preferably 0.5 mm or more. Further, the thickness of the galvanized steel sheet is preferably 3.5 mm or less.
  • the method for producing a galvanized steel sheet of the present invention includes a hot rolling process in which a steel slab having the above-mentioned composition is hot-rolled at a finish rolling temperature of 820°C or higher to obtain a hot-rolled steel sheet; A temperature raising step in which the steel plate after the hot rolling step is heated in a temperature range of 350°C or more and 600°C or less at an average heating rate of 7°C/sec or more, an annealing temperature: 750°C or more and 900°C or less, Annealing time: Annealing under the conditions of 20 seconds or more, and after the annealing step, the average cooling rate from (annealing temperature -30°C) to 650°C is 7°C/second or more, and from 650°C to 500°C.
  • a tension of 2.0 kgf/mm 2 or more is applied to the steel sheet in a temperature range of 300°C or higher and 450°C or lower, and then the galvanized steel sheet is rolled by 1/4 of a roll with a diameter of 500 mm or more and 1500 mm or less per pass.
  • a second cooling step is performed in which the galvanized steel sheet is passed through 5 passes or more while being in contact with the surrounding area, and then cooled from room temperature to a cooling stop temperature of 250°C or less.
  • the method of melting the steel material is not particularly limited, and any known melting method such as a converter or an electric furnace is suitable.
  • the steel slab (slab) is preferably manufactured by a continuous casting method, but it is also possible to manufacture it by an ingot method, a thin slab casting method, or the like.
  • the steel slab is charged into a heating furnace as a hot piece without being cooled to room temperature, or it is slightly heat-retained. Energy-saving processes such as direct rolling and direct rolling, which involve rolling immediately after rolling, can also be applied without problems.
  • the slab heating temperature is preferably 1100° C. or higher from the viewpoint of dissolving carbides and reducing rolling load. Further, in order to prevent an increase in scale loss, the slab heating temperature is preferably 1300° C. or lower. Note that the slab heating temperature is the temperature of the slab surface. In addition, slabs are roughly rolled into sheet bars under normal conditions, but if the heating temperature is lower, from the perspective of preventing trouble during hot rolling, a bar heater etc. is used to roll the slabs into sheets before finishing rolling. Preferably, the bar is heated.
  • Finish rolling temperature 820°C or higher Finish rolling increases the rolling load and the reduction rate in the non-recrystallized state of austenite, which develops an abnormal structure that is elongated in the rolling direction, resulting in poor ductility and holes in the final material. Decreases spreadability and bendability. For this reason, the finish rolling temperature is set to 820°C or higher.
  • the finish rolling temperature is preferably 830°C or higher, more preferably 850°C or higher. Further, the finish rolling temperature is preferably 1080°C or lower, more preferably 1050°C or lower.
  • the coiling temperature after hot rolling is not particularly limited, but it is necessary to consider the case where the ductility, hole expandability, and bendability of the final material are reduced. For this reason, the coiling temperature after hot rolling is preferably 300°C or higher. Further, the coiling temperature after hot rolling is preferably 700°C or less.
  • the rough rolled plates may be joined together during hot rolling and finish rolling may be performed continuously. Alternatively, the rough rolled plate may be wound up once. Further, in order to reduce the rolling load during hot rolling, part or all of the finish rolling may be performed as lubricated rolling. Performing lubricated rolling is also effective from the viewpoint of uniformity of the shape of the steel sheet and uniformity of material quality. Note that the friction coefficient during lubricated rolling is preferably in the range of 0.10 or more and 0.25 or less.
  • pickling process The hot rolled steel sheet produced as described above may be pickled. Since pickling can remove oxides on the surface of the steel sheet, it can be carried out to ensure good chemical conversion treatment properties and plating quality in the final high-strength steel sheet. Further, the pickling may be carried out once or may be carried out in multiple steps.
  • the hot-rolled pickled plate or hot-rolled steel plate obtained as described above is subjected to cold rolling, if necessary.
  • the pickled plate may be cold rolled after hot rolling, or cold rolling may be performed after heat treatment. Further, optionally, the cold rolled steel sheet obtained after cold rolling may be pickled.
  • Cold rolling is performed, for example, by multi-pass rolling that requires two or more passes, such as tandem multi-stand rolling or reverse rolling.
  • cold rolling reduction rate 20% or more and 80% or less
  • the cold rolling reduction rate (cumulative reduction rate) is not particularly limited, but should be 20% or more and 80% or less. It is preferable. If the rolling reduction ratio in cold rolling is less than 20%, the steel structure tends to become coarse and non-uniform in the annealing process, and there is a risk that the TS and bendability of the final product will deteriorate. On the other hand, if the rolling reduction ratio in cold rolling exceeds 80%, the steel sheet tends to be defective in shape, and the amount of zinc plating deposited may become uneven.
  • Metal plating (metal electroplating, first plating) process
  • metal plating is applied to one or both sides of the steel plate after the hot rolling process (or after the cold rolling process if cold rolling is performed) and before the temperature raising process.
  • the method may include a first plating step of forming a plating layer (first plating layer).
  • first plating layer the surface of the hot-rolled steel sheet or cold-rolled steel sheet obtained as described above may be subjected to a metal electroplating treatment to obtain a pre-annealed metal electroplated steel sheet in which a pre-annealed metal electroplating layer is formed on at least one side.
  • the metal plating mentioned here excludes zinc plating (secondary plating).
  • the metal electroplating method is not particularly limited, but as described above, it is preferable that the metal electroplating layer is formed on the base steel sheet, so it is preferable to perform the metal electroplating process.
  • a sulfuric acid bath, a hydrochloric acid bath, or a mixture of both can be used in the Fe-based electroplating bath.
  • the amount of deposited metal electroplating layer before annealing can be adjusted by adjusting the current application time and the like.
  • pre-annealed metal electroplated steel sheet means that the metal electroplated layer has not undergone an annealing process, and refers to a hot rolled steel sheet before metal electroplating, a pickled sheet after hot rolling, or a cold rolled steel sheet that has been annealed in advance. This does not exclude such aspects.
  • the metal species of the electroplating layer include Cr, Mn, Fe, Co, Ni, Cu, Ga, Ge, As, Ru, Rh, Pd, Ag, Cd, In, Sn, Sb, Os, Ir, Any of Rt, Au, Hg, Ti, Pb, and Bi may be used, but Fe is more preferable, so a method for producing Fe-based electroplating will be described below.
  • the Fe ion content in the Fe-based electroplating bath before the start of current application is preferably 0.5 mol/L or more as Fe 2+ . If the Fe ion content in the Fe-based electroplating bath is 0.5 mol/L or more as Fe 2+ , a sufficient amount of Fe deposition can be obtained. Further, in order to obtain a sufficient amount of Fe deposited, it is preferable that the Fe ion content in the Fe-based electroplating bath before the start of current application is 2.0 mol/L or less.
  • the Fe-based electroplating bath contains Fe ions and at least one selected from the group consisting of B, C, P, N, O, Ni, Mn, Mo, Zn, W, Pb, Sn, Cr, V, and Co. It can contain one type of element.
  • the total content of these elements in the Fe-based electroplating bath is preferably such that the total content of these elements in the Fe-based electroplated layer before annealing is 10% by mass or less.
  • the metal element may be contained as a metal ion, and the non-metal element may be contained as a part of boric acid, phosphoric acid, nitric acid, organic acid, or the like.
  • the iron sulfate plating solution may contain a conductivity aid such as sodium sulfate or potassium sulfate, a chelating agent, or a pH buffer.
  • the temperature of the Fe-based electroplating solution is preferably 30° C. or higher, and preferably 85° C. or lower, in view of constant temperature retention.
  • the pH of the Fe-based electroplating bath is not particularly specified, it is preferably 1.0 or higher from the viewpoint of preventing a decrease in current efficiency due to hydrogen generation, and considering the electrical conductivity of the Fe-based electroplating bath, .0 or less is preferable.
  • the current density is preferably 10 A/dm 2 or more from the viewpoint of productivity, and preferably 150 A/dm 2 or less from the viewpoint of facilitating control of the amount of Fe-based electroplated layer deposited.
  • the plate passing speed is preferably 5 mpm or more from the viewpoint of productivity, and preferably 150 mpm or less from the viewpoint of stably controlling the amount of adhesion.
  • degreasing treatment and water washing can be performed to clean the steel sheet surface, and furthermore, pickling treatment and water washing can be performed to activate the steel sheet surface.
  • pickling treatment can be performed to activate the steel sheet surface.
  • Fe-based electroplating treatment is performed.
  • the method of degreasing and washing with water is not particularly limited, and ordinary methods can be used.
  • various acids such as sulfuric acid, hydrochloric acid, nitric acid, and mixtures thereof can be used. Among these, sulfuric acid, hydrochloric acid, or a mixture thereof is preferred.
  • the acid concentration is not particularly defined, it is preferably about 1 to 20 mass% in consideration of the ability to remove an oxide film and the prevention of rough skin (surface defects) due to overacid washing.
  • the pickling treatment liquid may contain an antifoaming agent, a pickling accelerator, a pickling inhibitor, and the like.
  • metal plating after the hot rolling process (if cold rolling is performed, after the cold rolling process, and/or if metal plating to form a metal plating layer (first plating layer) is performed, includes a temperature raising step of raising the temperature of the steel plate in a temperature range of 350° C. or higher and 600° C. or lower at an average heating rate of 7° C./sec or higher.
  • Average heating rate in the temperature range of 350°C to 600°C: 7°C/second or more by increasing the average heating rate in the temperature range of 350°C to 600°C, isolated fine particles within the ferrite grains By increasing the ratio of the island-like hard second phase (martensite + retained austenite), improvements in ⁇ , R/t, ST, and SFmax can be realized. Therefore, the average heating rate in the temperature range from 350°C to 600°C is 7°C/s or more. It is preferably 9°C/s or more.
  • the upper limit is not particularly limited, but the average heating rate in the temperature range from 350°C to 600°C is preferably 100°C/s or less, more preferably 90°C/s or less.
  • the average heating rate (°C/s) is calculated from (heating end temperature (°C) - heating start temperature (°C))/heating time (s).
  • One embodiment of the present invention includes an annealing step after the temperature raising step, in which annealing is performed at an annealing temperature of 750° C. or more and 900° C. or less and an annealing time of 20 seconds or more.
  • Annealing temperature 750°C or more and 900°C or less
  • the annealing temperature is set to 750°C or more and 900°C or less.
  • the annealing temperature is preferably 880°C or lower. Note that the annealing temperature is the highest temperature reached in the annealing step.
  • Annealing time 20 seconds or more
  • the annealing time is set to 20 seconds or more.
  • the annealing time is preferably 30 seconds or more, more preferably 50 seconds or more.
  • the upper limit of the annealing time is not particularly limited, the annealing time is preferably 900 seconds or less, more preferably 800 seconds or less.
  • the annealing time is the holding time in a temperature range of (annealing temperature -40° C.) or higher and lower than the annealing temperature. That is, in addition to the holding time at the annealing temperature, the annealing time also includes the residence time in the temperature range from (annealing temperature -40°C) to below the annealing temperature during heating and cooling before and after reaching the annealing temperature.
  • the number of times of annealing may be two or more times, but from the viewpoint of energy efficiency, one time is preferable.
  • Dew point of annealing process atmosphere ⁇ 30° C. or higher
  • the dew point of the annealing step atmosphere is ⁇ 30° C. or higher.
  • the dew point of the annealing atmosphere in the annealing step is more preferably -25°C or higher, even more preferably -15°C or higher, and most preferably -5°C or higher.
  • the annealing atmosphere in the annealing process should be set.
  • the dew point is preferably 30°C or lower.
  • the average cooling rate from (annealing temperature -30°C) to 650°C is 7°C/second or more, and the average cooling rate from 650°C to 500°C is 14°C/second or less. It includes a first cooling step of cooling.
  • Average cooling rate from (annealing temperature -30°C) to 650°C: 7°C/sec or more when cooling quickly in a high temperature range of 650°C or higher, fine austenite is left behind at the ferrite grain boundaries, resulting in the final The ratio of isolated fine island-like hard second phases (martensite + retained austenite) within ferrite grains increases. Therefore, the average cooling rate from (annealing temperature -30°C) to 650°C is 7°C/sec or more.
  • the average cooling rate from (annealing temperature -30°C) to 650°C is preferably 9°C/sec or more.
  • the average cooling rate from (annealing temperature -30°C) to 650°C is preferably 80°C/second or less, more preferably 60°C/second or less.
  • the average cooling rate (°C/s) is calculated from (annealing temperature (°C) - 30 (°C) - 650 (°C))/cooling time (s).
  • Average cooling rate from 650°C to 500°C 14°C/sec or less
  • fine austenite at the ferrite grain boundaries coalesce between adjacent ferrites with similar orientations. After that, it becomes one ferrite grain, and is left behind as a fine island-like austenite isolated within the ferrite grain, and finally the ratio of isolated fine island-like hard second phase (martensite + retained austenite) within the ferrite grain increases. Therefore, the average cooling rate from 650°C to 500°C is 14°C/second or less, preferably 12°C/second or less.
  • the average cooling rate from 650°C to 500°C is preferably 1°C/second or more, more preferably 2°C/second or more.
  • the average cooling rate (°C/s) is calculated from (650 (°C) - 500 (°C))/cooling time (s).
  • the steel sheet is galvanized to obtain a galvanized steel sheet.
  • the galvanizing treatment include hot-dip galvanizing and alloyed galvanizing.
  • hot-dip galvanizing it is preferable to immerse the steel sheet in a galvanizing bath at a temperature of 440° C. or higher and 500° C. or lower, and then adjust the coating amount by gas wiping or the like.
  • the hot-dip galvanizing bath is not particularly limited as long as it has the composition of the galvanized layer described above. It is preferable to use a plating bath having a composition comprising: and unavoidable impurities.
  • alloyed galvanizing treatment after hot-dip galvanizing treatment as described above, it is preferable to heat the hot-dip galvanized steel sheet to an alloying temperature of 450°C or more and 600°C or less to perform alloying treatment. . If the alloying temperature is less than 450° C., the Zn--Fe alloying speed will be slow and alloying may become difficult. On the other hand, when the alloying temperature exceeds 600°C, untransformed austenite transforms into pearlite, making it difficult to make the TS 780 MPa or higher. Note that the alloying temperature is more preferably 500°C or higher, and still more preferably 510°C or higher. Further, the alloying temperature is more preferably 570°C or lower.
  • the coating weight of the hot-dip galvanized steel sheet (GI) and the alloyed hot-dip galvanized steel sheet (GA) be 20 to 80 g/m 2 per side. Note that the amount of plating deposited can be adjusted by gas wiping or the like.
  • a tension of 2.0 kgf/mm2 or more is applied to the galvanized steel sheet in a temperature range of 300°C or higher and 450°C or lower, and the galvanized steel sheet is heated to a diameter of 500 mm or more per pass.
  • a second cooling step is included in which the material is passed through 5 passes or more while being brought into contact with a roll of 1500 mm or less for 1/4 rotation of the roll, and then cooled to a cooling stop temperature (second cooling stop temperature) of 250° C. or less.
  • a tension of 2.0 kgf/mm 2 or more is applied to the galvanized steel sheet at least once as described above.
  • most of the austenite becomes martensite through deformation (stress/strain)-induced transformation, and then undergoes tempering in the reheating process, which reduces the area ratio of fresh martensite in the final structure.
  • a suitable amount can be secured.
  • the amount of austenite immediately after the second cooling step can be reduced, and the volume fraction of retained austenite in the final structure can be reduced.
  • desired ⁇ , R/t, ST and SFmax are obtained.
  • the load cell must be placed parallel to the tension direction.
  • the load cell is preferably arranged at a position 200 mm from both ends of the roll.
  • the length of the roll used is preferably 1500 to 2500 mm.
  • this tension is preferably 2.2 kgf/mm 2 or more, more preferably 2.4 kgf/mm 2 or more.
  • the number of passes is preferably 15.0 kgf/mm 2 or less, more preferably 10.0 kgf/mm 2 or less.
  • the galvanized steel sheet is passed through a roll having a diameter of 500 mm or more and 1500 mm or less while being in contact with the roll for 1/4 rotation per pass: 5 passes or more
  • the galvanized steel sheet is passed through a roll having a diameter of 500 mm or more and 1500 mm or less.
  • Second cooling stop temperature 250°C or less
  • the cooling conditions for the second cooling step are not particularly limited, and may be according to a conventional method.
  • the cooling method for example, gas jet cooling, mist cooling, roll cooling, water cooling, air cooling, etc. can be applied.
  • an appropriate amount of austenite transforms into martensite and is then tempered in the reheating process, which reduces the area ratio of fresh martensite in the final structure.
  • an appropriate amount of tempered martensite can be secured.
  • the amount of austenite immediately after the second cooling step can be reduced, and the volume fraction of retained austenite in the final structure can be reduced. As a result, desired ⁇ , R/t, ST and SFmax are obtained.
  • the lower limit is not particularly limited, but it is preferably room temperature (-5°C or higher and 55°C or lower).
  • the average cooling rate is preferably, for example, 1° C./second or more and 50° C./second or less.
  • the galvanized steel sheet is reheated to a temperature range of above the cooling stop temperature (second cooling stop temperature) and below 440° C. and held for 20 seconds or more.
  • Reheating temperature Temperature range above the above cooling stop temperature (second cooling stop temperature) and below 440°C Reheating holding time: 20 seconds or more
  • reheating to above the cooling stop temperature (second cooling stop temperature) By holding the temperature for 20 seconds or more, diffusible hydrogen in the steel is released. Furthermore, the area ratio of fresh martensite in the final structure can be reduced, and an appropriate amount of tempered martensite can be secured. Further, the amount of austenite immediately after the second cooling step can be reduced, and the volume fraction of retained austenite in the final structure can be reduced. As a result, desired ⁇ , R/t, ST and SFmax are obtained.
  • the temperature is reheated to a temperature range from the second cooling stop temperature to 440° C. and held for 20 seconds or more.
  • the galvanized steel sheet obtained as described above may be further subjected to temper rolling. If the reduction ratio in temper rolling exceeds 2.00%, the yield stress will increase, and there is a risk that the dimensional accuracy when forming the galvanized steel sheet into a member will decrease. Therefore, the reduction ratio in temper rolling is preferably 2.00% or less.
  • the lower limit of the rolling reduction in skin pass rolling is not particularly limited, but from the viewpoint of productivity, it is preferably 0.05% or more.
  • skin pass rolling may be performed on a device that is continuous with the annealing device for performing each process mentioned above (online), or on a device that is discontinuous with the annealing device for performing each process (offline). You may go. Further, the number of times of temper rolling may be one, or two or more times. Note that rolling with a leveler or the like may be used as long as it can provide an elongation rate equivalent to that of temper rolling.
  • Conditions for other manufacturing methods are not particularly limited, but from the viewpoint of productivity, a series of treatments such as annealing, hot-dip galvanizing, and alloying treatment of galvanizing are performed on a CGL (Continuous Galvanizing Line), which is a hot-dip galvanizing line. It is preferable to carry out the process using Line). After hot-dip galvanizing, wiping can be performed to adjust the coating weight. Note that the conditions for plating and the like other than the above-mentioned conditions can be based on a conventional method for hot-dip galvanizing.
  • a member according to an embodiment of the present invention is a member made of (made of) the above-mentioned galvanized steel plate.
  • the material is a galvanized steel plate that is subjected to at least one of forming and joining processes to produce a member.
  • the above-mentioned galvanized steel sheet has a TS of 780 MPa or more, high YS and YR, excellent press formability (ductility, hole expandability, and bendability), and rupture resistance at the time of collision (bending fracture properties and axial crush properties). Therefore, the member according to one embodiment of the present invention has high strength and excellent impact resistance. Therefore, a member according to an embodiment of the present invention is particularly suitable for application as an impact energy absorbing member used in the automotive field.
  • a method for producing a member according to an embodiment of the present invention includes subjecting the above galvanized steel sheet (for example, a galvanized steel sheet produced by the above method for producing a galvanized steel sheet) to at least one of forming processing and joining processing. It has a process of making it into a member.
  • the molding method is not particularly limited, and for example, a general processing method such as press working can be used.
  • the joining method is not particularly limited, and for example, common welding such as spot welding, laser welding, arc welding, riveting joining, caulking joining, etc. can be used.
  • the molding conditions and bonding conditions are not particularly limited, and conventional methods may be followed.
  • a galvanized steel sheet comprising a base steel plate and a galvanized layer formed on the base steel plate, the base steel plate comprising: In mass%, C: 0.030% or more and 0.250% or less, Si: 0.01% or more and 0.75% or less, Mn: 2.00% or more and less than 3.50%, P: 0.001% or more and 0.100% or less, S: 0.0200% or less, Al: 0.010% or more and 2.000% or less, N: 0.0100% or less, , with the remainder consisting of Fe and unavoidable impurities;
  • Ferrite area ratio 20.0% or more and 80.0% or less
  • Fresh martensite area ratio 15.0% or less
  • Area ratio of retained austenite 3.0% or less
  • the component composition further includes, in mass%, Nb: 0.200% or less, Ti: 0.200% or less, V: 0.200% or less, B: 0.0100% or less, Cr: 1.000% or less, Ni: 1.000% or less, Mo: 1.000% or less, Sb: 0.200% or less, Sn: 0.200% or less, Cu: 1.000% or less, Ta: 0.100% or less, W: 0.500% or less, Mg: 0.0200% or less, Zn: 0.0200% or less, Co: 0.0200% or less, Zr: 0.1000% or less, Ca: 0.0200% or less, Se: 0.0200% or less, Te: 0.0200% or less, Ge: 0.0200% or less, As: 0.0500% or less, Sr: 0.0200% or less, Cs: 0.0200% or less, Hf: 0.0200% or less, Pb: 0.0200% or less,
  • the nanohardness of the plate surface at 1/4 of the depth in the thickness direction of the surface soft layer from the surface of the base steel sheet is 7.0 GPa or more is the total number of measurements at 1/4 of the depth in the thickness direction of the surface soft layer. 0.10 or less for the number
  • the standard deviation ⁇ of the nano-hardness of the plate surface at a position 1/4 of the thickness direction depth of the surface soft layer from the base steel plate surface is 1.8 GPa or less
  • any one of [1] to [3] above, wherein the standard deviation ⁇ of nano-hardness of the plate surface at a position 1/2 the thickness direction depth of the surface soft layer from the base steel plate surface is 2.2 GPa or less.
  • Galvanized steel sheet described in Crab [5] The galvanized steel sheet according to any one of [1] to [4] above, which has a metal plating layer formed between the base steel sheet and the galvanized layer on one or both sides of the galvanized steel sheet. . [6] The galvanized steel sheet according to any one of [1] to [5], wherein the galvanized layer is a hot-dip galvanized layer or an alloyed hot-dip galvanized layer. [7] A member using the galvanized steel sheet according to any one of [1] to [6] above.
  • a galvanizing step is performed on the steel sheet to obtain a galvanized steel sheet; Applying a tension of 2.0 kgf/mm 2 or more to the galvanized steel sheet in a temperature range of 300 ° C. or higher and 450 ° C. or lower, Thereafter, the galvanized steel sheet is passed through 5 passes or more while being in contact with a roll having a diameter of 500 mm or more and 1500 mm or less for 1/4 rotation of the roll per pass, Then, a second cooling step of cooling to a cooling stop temperature of 250° C. or less; a reheating step of reheating the galvanized steel sheet to a temperature range from the cooling stop temperature to 440° C.
  • a method for manufacturing a galvanized steel sheet comprising a cold rolling step of cold rolling a previous steel sheet at a rolling reduction of 20% or more and 80% or less to obtain a cold rolled steel sheet.
  • the galvanized steel sheet according to [8] or [9] which includes a metal plating step of applying metal plating to form a metal plating layer on one or both sides of the galvanized steel sheet before the annealing step. manufacturing method.
  • a method for producing a member comprising the step of subjecting the galvanized steel sheet according to any one of [1] to [6] to at least one of forming and bonding to produce a member.
  • a steel material having the component composition shown in Table 1 (the remainder being Fe and unavoidable impurities) was melted in a converter and made into a steel slab using a continuous casting method.
  • Table 1 indicates the content at the inevitable impurity level.
  • the obtained steel slab was heated to 1200°C, and after heating, the steel slab was subjected to rough rolling and hot rolling to obtain a hot rolled steel plate. Then, the obtained hot rolled steel sheet No. 1 ⁇ No. 57 and no. 60 ⁇ No. No. 83 was pickled and cold rolled to obtain a cold rolled steel sheet having the thickness shown in Table 3. Moreover, No. of the obtained hot-rolled steel sheet. 57 ⁇ No. 59 and no. 84 ⁇ No. No. 91 was pickled to obtain a hot rolled steel plate (white skin) having the thickness shown in Table 3.
  • the obtained cold-rolled steel sheet or hot-rolled steel sheet (white skin) is subjected to treatments in a temperature raising step, an annealing step, a first cooling step, a plating step, a second cooling step, and a reheating step under the conditions shown in Table 2. Also, under the conditions shown in Table 4, a temperature raising process, a first plating process (metal plating process), an annealing process, a first cooling process, a second plating process (zinc plating process), a second cooling process and a re- A galvanized steel sheet was obtained by processing in a heating process.
  • a temperature raising process a first plating process (metal plating process), an annealing process, a first cooling process, a second plating process (zinc plating process), a second cooling process and a re- A galvanized steel sheet was obtained by processing in a heating process.
  • hot-dip galvanizing treatment or alloyed galvanizing treatment was performed to obtain a hot-dip galvanized steel sheet (hereinafter also referred to as GI) or an alloyed hot-dip galvanized steel sheet (hereinafter also referred to as GA).
  • GI hot-dip galvanized steel sheet
  • GA alloyed hot-dip galvanized steel sheet
  • Table 2 the types of plating processes are also indicated as "GI” and "GA”.
  • the alloying temperature is indicated as - because no alloying treatment is performed in the case of GI steel sheets.
  • the zinc plating bath temperature was 470° C. in both GI and GA production.
  • the amount of zinc plating deposited was 45 to 72 g/m 2 per side when manufacturing GI, and 45 g/m 2 per side when manufacturing GA.
  • the composition of the galvanized layer of the finally obtained hot-dip galvanized steel sheet contains, in GI, Fe: 0.1 to 1.0 mass%, Al: 0.2 to 0.33 mass%, The remainder was Zn and unavoidable impurities.
  • GA contained Fe: 8.0 to 12.0% by mass, Al: 0.1 to 0.23% by mass, and the remainder was Zn and inevitable impurities. Further, all galvanized layers were formed on both sides of the base steel sheet.
  • the method for measuring the surface soft layer is as follows. After smoothing the thickness section (L section) parallel to the rolling direction of the steel plate by wet polishing, using a Vickers hardness tester, the thickness was measured 100 ⁇ m from a position 1 ⁇ m in the thickness direction from the steel plate surface under a load of 10 gf. Measurements were made at 1 ⁇ m intervals up to the position. Thereafter, measurements were taken at intervals of 20 ⁇ m up to the center of the plate thickness. The area where the hardness has decreased to 85% or less compared to the hardness at 1/4 of the plate thickness is defined as a soft layer (surface soft layer), and the thickness of this area in the plate thickness direction is defined as the thickness of the soft layer. .
  • yield stress (YS), yield ratio (YR), total elongation (El), critical hole expansion rate ( ⁇ ), R/t in V-bending test, critical spacer thickness in U-bending + close contact bending test ( ST), the stroke at maximum load (SFmax) measured in the V-bending + orthogonal VDA bending test, and the presence or absence of fracture (appearance cracking) in the axial crushing test were evaluated.
  • ⁇ YS ⁇ (Passed) (A) If 780MPa ⁇ TS ⁇ 980MPa, 500MPa ⁇ YS (B) If 980MPa ⁇ TS, 600MPa ⁇ YS ⁇ (fail): (A) If 780MPa ⁇ TS ⁇ 980MPa, 500MPa>YS (B) If 980MPa ⁇ TS, 600MPa>YS
  • ⁇ YR ⁇ (Passed) (A) When 780MPa ⁇ TS ⁇ 980MPa, 0.64 ⁇ YR (B) If 980MPa ⁇ TS, 0.61 ⁇ YR ⁇ (fail): (A) If 780MPa ⁇ TS ⁇ 980MPa, 0.64>YR (B) If 980MPa ⁇ TS, 0.61>YR
  • ⁇ R/t ⁇ (Passed) (A) When 780MPa ⁇ TS ⁇ 980MPa, 2.0 ⁇ R/t (B) If 980MPa ⁇ TS, 2.5 ⁇ R/t ⁇ (fail): (A) When 780MPa ⁇ TS ⁇ 980MPa, 2.0 ⁇ R/t (B) When 980MPa ⁇ TS, 2.5 ⁇ R/t
  • Tensile test The tensile test was conducted in accordance with JIS Z 2241. That is, a JIS No. 5 test piece was taken from the obtained galvanized steel sheet so that the longitudinal direction was perpendicular to the rolling direction of the base steel sheet. Using the sampled test piece, a tensile test was conducted at a crosshead speed of 10 mm/min, and TS, YS, YR, and El were measured. The results are shown in Tables 3 and 5.
  • ⁇ is an index for evaluating stretch flangeability.
  • the results are shown in Tables 3 and 5.
  • ⁇ (%) ⁇ (D f - D 0 )/D 0 ⁇ 100 here, D f : Diameter of hole in test piece at the time of crack occurrence (mm) D 0 : Diameter of hole in initial test piece (mm) It is.
  • V bending test The V (90°) bending test was conducted in accordance with JIS Z 2248. A 100 mm x 35 mm test piece was taken from the obtained galvanized steel plate by shearing and end face grinding. Here, the 100 mm side is parallel to the width (C) direction.
  • Bending radius R Changes at 0.5mm pitch
  • Test method Die support, punch press molding load: 10 tons
  • Test speed 30mm/min Holding time: 5s
  • Bending direction Evaluation was performed three times in the direction perpendicular to rolling (C), and R/t was calculated by dividing the minimum bending radius (limit bending radius) R at which no cracks appeared in each case by the plate thickness t.
  • U-bending + close-contact bending test was conducted as follows. A 60 mm x 30 mm test piece was taken from the obtained galvanized steel sheet by shearing and end face grinding. Here, the 60 mm side is parallel to the width (C) direction. A test piece was prepared by performing U bending (primary bending) in the width (C) direction with the rolling (L) direction as the axis at a radius of curvature/plate thickness of 4.2. In the U-bending process (primary bending process), as shown in FIG. 2(a), a punch B1 was pushed into a steel plate placed on a roll A1 to obtain a test piece T1. Next, as shown in FIG.
  • test piece T1 placed on the lower mold A2 was subjected to close bending (secondary bending) by crushing it with the upper mold B2.
  • D1 indicates the width (C) direction
  • D2 indicates the rolling (L) direction. Note that a spacer S, which will be described later, was inserted between the test pieces.
  • the U-bending conditions in the U-bending + close contact bending test are as follows.
  • Test method Roll support, punch pushing Punch tip R: 5.0mm Clearance between roll and punch: plate thickness + 0.1mm Stroke speed: 10mm/min Bending direction: rolling perpendicular (C) direction
  • the conditions for close bending in the U-bending + close bending test are as follows.
  • Spacer thickness Changes at 0.5mm pitch
  • Test method Die support, punch press molding load: 10 tons
  • V-bending + orthogonal VDA bending test is performed as follows.
  • a 60 mm x 65 mm test piece was taken from the obtained galvanized steel plate by shearing and end face grinding. Here, the 60 mm side is parallel to the rolling (L) direction.
  • a test piece was prepared by performing a 90° bending process (primary bending process) in the rolling (L) direction with the width (C) direction as the axis at a radius of curvature/plate thickness of 4.2. In the 90° bending process (primary bending process), as shown in FIG.
  • a punch B3 was pushed into a steel plate placed on a die A3 having a V-groove to obtain a test piece T1.
  • the punch B4 is pushed into the test piece T1 placed on the support roll A4 so that the bending direction is perpendicular to the rolling direction (secondary bending). bending process).
  • D1 indicates the width (C) direction
  • D2 indicates the rolling (L) direction.
  • V-bending conditions in the V-bending + orthogonal VDA bending test are as follows. Test method: die support, punch press molding load: 10 tons Test speed: 30mm/min Holding time: 5s Bending direction: rolling (L) direction
  • VDA bending conditions in the V-bending + orthogonal VDA bending test are as follows. Test method: Roll support, punch pushing Roll diameter: ⁇ 30mm Punch tip R: 0.4mm Distance between rolls: (plate thickness x 2) + 0.5mm Stroke speed: 20mm/min Test piece size: 60mm x 60mm Bending direction: rolling right angle (C) direction
  • SFmax is an index for evaluating the fracture resistance at the time of a collision (the fracture resistance of a bending ridgeline portion in an axial crush test). The results are shown in Tables 3 and 5.
  • Axial crush test A 150 mm x 100 mm test piece was taken from the obtained galvanized steel sheet by shearing. Here, the 150 mm side is parallel to the rolling (L) direction. Using a mold with a punch shoulder radius of 5.0 mm and a die shoulder radius of 5.0 mm, the molding process (bending process) was performed to a depth of 40 mm. A hat-shaped member 10 shown in b) was produced. Further, a steel plate used as a material for the hat-shaped member was separately cut into a size of 80 mm x 100 mm. Next, the cut steel plate 20 and the hat-shaped member 10 were spot welded to produce a test member 30 as shown in FIGS. 4(a) and 4(b). FIG.
  • FIG. 4A is a front view of a test member 30 produced by spot welding the hat-shaped member 10 and the steel plate 20.
  • FIG. 4(b) is a perspective view of the test member 30.
  • the spot welds 40 were positioned so that the distance between the end of the steel plate and the weld was 10 mm, and the distance between the welds was 20 mm.
  • the test member 30 was joined to the base plate 50 by TIG welding to prepare a sample for an axial crush test.
  • the impactor 60 was made to collide with the produced sample for the axial crush test at a constant velocity of 10 mm/min, and the sample for the axial crush test was crushed by 70 mm.
  • the crushing direction D3 was parallel to the longitudinal direction of the test member 30. The results are shown in Tables 3 and 5.
  • the ground surface is the inside of the bend (valley side)
  • the ground surface is was set as the outside of the bend (peak side)
  • the ground surface was set as the inside of the bend (valley side) during the subsequent VDA bending test.
  • the U-bending + close bending test V-bending + orthogonal VDA bending test, and axial crushing test of galvanized steel sheets with a thickness of less than 1.2, the effects of the sheet thickness were small, so the tests were conducted without grinding.
  • ⁇ Nano hardness measurement> In order to obtain excellent bendability during press forming and excellent bending rupture properties during collision, it is necessary to place the base material at a position of 1/4 of the depth in the thickness direction and 1/2 of the depth in the thickness direction of the surface soft layer from the surface layer of the substrate.
  • nanohardness was measured at 300 or more points in a 50 ⁇ m x 50 ⁇ m area of the plate surface at each position, the nanohardness of the plate surface at a position 1/4 of the thickness direction depth of the surface soft layer from the base steel plate surface was It is more preferable that the number of measurements of 7.0 GPa or more is 0.10 or less with respect to the total number of measurements at 1/4 position of the depth in the plate thickness direction.
  • the ratio of nanohardness of 7.0 GPa or more is 0.10 or less, it means that the ratio of hard structures (such as martensite) and inclusions is small. It becomes possible to further suppress the generation and connection of voids and the propagation of cracks during press molding and collisions, and excellent R/t and SFmax can be obtained.
  • the members obtained by forming or joining the steel sheets of the present invention example have tensile strength (TS), yield stress (YS), yield ratio (YR), Elongation (El), critical hole expansion rate ( ⁇ ), R/t in V-bending test, critical spacer thickness (ST) in U-bending + close bending test, and measured in V-bending + orthogonal VDA bending test
  • TS tensile strength
  • Yield stress Yield stress
  • YiR yield ratio
  • El Elongation
  • ⁇ critical hole expansion rate
  • ST critical spacer thickness
  • All of the strokes (SFmax) at the maximum load applied have the excellent characteristics characterized by the present invention, and there is no breakage (appearance cracking) in the axial crush test, and the excellent characteristics characterized by the present invention. I understand.
  • TS 780 MPa or more, high YS and YR, excellent press formability (ductility, hole expandability, and bendability), and rupture resistance properties at the time of collision (bending rupture properties and axial)
  • ductility, hole expandability, and bendability excellent press formability
  • rupture resistance properties at the time of collision bending rupture properties and axial

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PCT/JP2022/019991 2022-05-11 2022-05-11 亜鉛めっき鋼板、部材およびそれらの製造方法 WO2023218576A1 (ja)

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PCT/JP2022/019991 WO2023218576A1 (ja) 2022-05-11 2022-05-11 亜鉛めっき鋼板、部材およびそれらの製造方法
PCT/JP2023/006924 WO2023218730A1 (ja) 2022-05-11 2023-02-27 鋼板、部材およびそれらの製造方法
CN202380038649.XA CN119173645A (zh) 2022-05-11 2023-02-27 钢板、构件和它们的制造方法
EP23803217.1A EP4502217A4 (en) 2022-05-11 2023-02-27 STEEL SHEET, ELEMENT AND METHOD FOR THE PRODUCTION THEREOF
KR1020247036701A KR20240172211A (ko) 2022-05-11 2023-02-27 강판, 부재 및 그들의 제조 방법
JP2023565496A JP7601256B2 (ja) 2022-05-11 2023-02-27 鋼板、部材およびそれらの製造方法
MX2024013687A MX2024013687A (es) 2022-05-11 2024-11-05 Lamina de acero, miembro y metodos para producirlos

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WO2019189841A1 (ja) * 2018-03-30 2019-10-03 Ｊｆｅスチール株式会社 高強度亜鉛めっき鋼板、高強度部材およびそれらの製造方法
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EP4012055A4 (en) * 2019-08-06 2022-08-31 JFE Steel Corporation HIGH STRENGTH THIN STEEL SHEET AND METHOD OF PRODUCTION THEREOF

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
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