WO2013018723A1 - 成形性に優れた高強度鋼板、高強度亜鉛めっき鋼板及びそれらの製造方法 - Google Patents
成形性に優れた高強度鋼板、高強度亜鉛めっき鋼板及びそれらの製造方法 Download PDFInfo
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- WO2013018723A1 WO2013018723A1 PCT/JP2012/069226 JP2012069226W WO2013018723A1 WO 2013018723 A1 WO2013018723 A1 WO 2013018723A1 JP 2012069226 W JP2012069226 W JP 2012069226W WO 2013018723 A1 WO2013018723 A1 WO 2013018723A1
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- Prior art keywords
- steel sheet
- strength
- less
- phase
- formability
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 174
- 239000010959 steel Substances 0.000 title claims abstract description 174
- 238000004519 manufacturing process Methods 0.000 title claims description 33
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 74
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 54
- 229910052742 iron Inorganic materials 0.000 claims abstract description 37
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 20
- 239000002245 particle Substances 0.000 claims description 78
- 238000001816 cooling Methods 0.000 claims description 39
- 238000010438 heat treatment Methods 0.000 claims description 39
- 238000005096 rolling process Methods 0.000 claims description 31
- 229910000734 martensite Inorganic materials 0.000 claims description 28
- 238000000034 method Methods 0.000 claims description 23
- 238000000137 annealing Methods 0.000 claims description 19
- 229910001335 Galvanized steel Inorganic materials 0.000 claims description 17
- 229910001563 bainite Inorganic materials 0.000 claims description 17
- 239000008397 galvanized steel Substances 0.000 claims description 17
- 238000005098 hot rolling Methods 0.000 claims description 15
- 238000005097 cold rolling Methods 0.000 claims description 14
- 230000008569 process Effects 0.000 claims description 14
- 238000005452 bending Methods 0.000 claims description 12
- 229910052684 Cerium Inorganic materials 0.000 claims description 10
- 238000005246 galvanizing Methods 0.000 claims description 10
- 229910052761 rare earth metal Inorganic materials 0.000 claims description 10
- 239000012535 impurity Substances 0.000 claims description 9
- 229910052791 calcium Inorganic materials 0.000 claims description 8
- 229910052749 magnesium Inorganic materials 0.000 claims description 8
- 230000009467 reduction Effects 0.000 claims description 8
- 230000009466 transformation Effects 0.000 claims description 8
- 238000005275 alloying Methods 0.000 claims description 5
- 238000004804 winding Methods 0.000 claims description 4
- 238000009713 electroplating Methods 0.000 claims description 3
- 238000003825 pressing Methods 0.000 claims description 3
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 2
- 229910052725 zinc Inorganic materials 0.000 claims description 2
- 239000011701 zinc Substances 0.000 claims description 2
- 239000000203 mixture Substances 0.000 abstract description 9
- 230000000694 effects Effects 0.000 description 18
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- 238000001556 precipitation Methods 0.000 description 10
- 238000005728 strengthening Methods 0.000 description 10
- 229910052802 copper Inorganic materials 0.000 description 9
- 238000005554 pickling Methods 0.000 description 9
- 229910052710 silicon Inorganic materials 0.000 description 9
- 229910052782 aluminium Inorganic materials 0.000 description 7
- 239000010960 cold rolled steel Substances 0.000 description 7
- 230000001771 impaired effect Effects 0.000 description 7
- 229910052748 manganese Inorganic materials 0.000 description 7
- 150000001247 metal acetylides Chemical class 0.000 description 7
- 229910052759 nickel Inorganic materials 0.000 description 7
- 229910052804 chromium Inorganic materials 0.000 description 6
- 239000013078 crystal Substances 0.000 description 6
- 239000000463 material Substances 0.000 description 6
- 229910052796 boron Inorganic materials 0.000 description 5
- 229910052799 carbon Inorganic materials 0.000 description 5
- 229910052698 phosphorus Inorganic materials 0.000 description 5
- 239000000523 sample Substances 0.000 description 5
- 230000005540 biological transmission Effects 0.000 description 4
- 239000002131 composite material Substances 0.000 description 4
- 238000005260 corrosion Methods 0.000 description 4
- 230000007797 corrosion Effects 0.000 description 4
- 238000005259 measurement Methods 0.000 description 4
- 229910052750 molybdenum Inorganic materials 0.000 description 4
- 229910052757 nitrogen Inorganic materials 0.000 description 4
- 229910001562 pearlite Inorganic materials 0.000 description 4
- 238000012360 testing method Methods 0.000 description 4
- 238000005266 casting Methods 0.000 description 3
- 229910001567 cementite Inorganic materials 0.000 description 3
- 238000005430 electron energy loss spectroscopy Methods 0.000 description 3
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 3
- 229910052747 lanthanoid Inorganic materials 0.000 description 3
- 150000002602 lanthanoids Chemical class 0.000 description 3
- 229910052746 lanthanum Inorganic materials 0.000 description 3
- 230000014759 maintenance of location Effects 0.000 description 3
- 229910052758 niobium Inorganic materials 0.000 description 3
- 238000012545 processing Methods 0.000 description 3
- 238000001953 recrystallisation Methods 0.000 description 3
- 229910052717 sulfur Inorganic materials 0.000 description 3
- 229910052719 titanium Inorganic materials 0.000 description 3
- 229910052720 vanadium Inorganic materials 0.000 description 3
- 229910000797 Ultra-high-strength steel Inorganic materials 0.000 description 2
- 238000002441 X-ray diffraction Methods 0.000 description 2
- 239000000654 additive Substances 0.000 description 2
- 230000000996 additive effect Effects 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
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- 238000002003 electron diffraction Methods 0.000 description 2
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- 239000012467 final product Substances 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 238000010899 nucleation Methods 0.000 description 2
- 230000006911 nucleation Effects 0.000 description 2
- 229910052760 oxygen Inorganic materials 0.000 description 2
- 238000007747 plating Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- 210000001519 tissue Anatomy 0.000 description 2
- 229910052721 tungsten Inorganic materials 0.000 description 2
- 230000000007 visual effect Effects 0.000 description 2
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 1
- 229910001122 Mischmetal Inorganic materials 0.000 description 1
- 229910001035 Soft ferrite Inorganic materials 0.000 description 1
- 238000009825 accumulation Methods 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000004719 convergent beam electron diffraction Methods 0.000 description 1
- 238000012937 correction Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000002950 deficient Effects 0.000 description 1
- 230000003111 delayed effect Effects 0.000 description 1
- 238000000151 deposition Methods 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 238000000445 field-emission scanning electron microscopy Methods 0.000 description 1
- 239000010419 fine particle Substances 0.000 description 1
- 229910052735 hafnium Inorganic materials 0.000 description 1
- 238000002173 high-resolution transmission electron microscopy Methods 0.000 description 1
- 238000009434 installation Methods 0.000 description 1
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- 238000012423 maintenance Methods 0.000 description 1
- 239000012528 membrane Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 239000003973 paint Substances 0.000 description 1
- 238000004881 precipitation hardening Methods 0.000 description 1
- 150000002910 rare earth metals Chemical class 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 210000004872 soft tissue Anatomy 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Classifications
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
- B32B15/013—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of a metal other than iron or aluminium
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
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- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
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- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
- C23C2/36—Elongated material
- C23C2/40—Plates; Strips
-
- C—CHEMISTRY; METALLURGY
- C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
- C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
- C25D5/00—Electroplating characterised by the process; Pretreatment or after-treatment of workpieces
- C25D5/34—Pretreatment of metallic surfaces to be electroplated
- C25D5/36—Pretreatment of metallic surfaces to be electroplated of iron or steel
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- C—CHEMISTRY; METALLURGY
- C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
- C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
- C25D7/00—Electroplating characterised by the article coated
- C25D7/06—Wires; Strips; Foils
- C25D7/0614—Strips or foils
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/004—Dispersions; Precipitations
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
- Y10T428/12771—Transition metal-base component
- Y10T428/12785—Group IIB metal-base component
- Y10T428/12792—Zn-base component
- Y10T428/12799—Next to Fe-base component [e.g., galvanized]
Definitions
- the present invention relates to a high-strength steel sheet having high formability, a high-strength galvanized steel sheet, and methods for producing them.
- Patent Document 1 contains C, Si, P, S, Al, N, and Cu in a predetermined mass% range, Mn: 0.1 to 3.0%, Cr: 0.1 to 3.0% 1 or 2 of them, (Mn + Cr) / Cu is 0.2 or more, the balance is composed of iron and inevitable impurities, the average ferrite crystal grain size is 3 ⁇ m or more, and the ferrite area ratio is 60% or more.
- Mn 0.1 to 3.0%
- Cr 0.1 to 3.0% 1 or 2 of them
- (Mn + Cr) / Cu is 0.2 or more
- the balance is composed of iron and inevitable impurities
- the average ferrite crystal grain size is 3 ⁇ m or more
- the ferrite area ratio is 60% or more
- a Cu precipitation hardening type high strength steel is disclosed.
- Patent Document 2 contains a predetermined mass% of C, Si, Cu, and Mn, and further appropriately includes Al, Ni, Mo, It contains at least one of Cr, V, B, Ti, Nb, Ca, and Mg, and the hardness of the ferrite phase is 150 to 240 in Hv, and the volume fraction of retained austenite in the steel structure Is a high-strength steel sheet excellent in formability and hole expansibility with a tensile strength of 600-800 MPa.
- Patent Document 3 as an example of a high-strength cold-rolled steel sheet having excellent fatigue characteristics, C: 0.05 to 0.30%, Cu: 0.2 to 2.0%, and B: 2 to 20 ppm.
- the microstructure included is a steel plate composed of retained austenite having a volume ratio of 5% or more and 25% or less, and ferrite and bainite, and the presence state of Cu in the ferrite phase is the size of particles composed of Cu alone.
- a high-strength cold-rolled steel sheet for processing excellent in fatigue properties in a solid solution state and / or a precipitation state with a thickness of 2 nm or less is disclosed.
- Patent Document 4 describes C: 0.03 to 0.20%, Cu: 0.2 to 2.0%, and B: 2 to 20 ppm as an example of a composite structure high-strength cold-rolled steel sheet having excellent fatigue characteristics.
- the ferrite-martensite composite structure steel sheet is characterized in that the presence state of Cu in the ferrite phase is a solid solution state and / or a precipitation state in which the size of particles composed of Cu alone is 2 nm or less.
- a composite structure high-strength cold-rolled steel sheet having excellent fatigue properties is disclosed.
- Patent Document 5 as an example of an ultra-high strength steel sheet having excellent delayed fracture resistance, C: 0.08 to 0.30, Si: less than 1.0, Mn: 1.5 to 3. 0, S: 0.010 or less, P: 0.03 to 0.15, Cu: 0.10 to 1.00, and Ni: 0.10 to 4.00, from the balance iron and inevitable impurities Therefore, an ultra-high strength steel sheet containing at least one of martensite, tempered martensite, and bainite structure in a volume ratio of 40% or more and having a strength of 1180 MPa or more is disclosed.
- Patent Document 6 as an example of a high-strength steel plate excellent in press formability and corrosion resistance, C: 0.08 to 0.20%, Si: 0.8 to 2.0%, Mn: 0.7 to 2 0.5%, P: 0.02 to 0.15%, S: 0.010% or less, Al: 0.01 to 0.10%, Cu: 0.05 to 1.0%, Ni: 1.0 %, The balance being iron and inevitable impurities, and the following formula “0.4 ⁇ (10P + Si) / (10C + Mn + Cu + 0.5Ni) ⁇ 1.6” [the element symbol in the formula is the respective content ( A high-strength steel sheet excellent in press formability and corrosion resistance, having a retained austenite of 3 to 10% and a tensile strength of 610 to 760 MPa. .
- Patent Document 7 as an example of a high-tensile steel sheet, a thin steel sheet is made of C: 0.05 to 0.3%, Si: 2% or less, Mn: 0.05 to 4.0%, P: 0.00. 1% or less, S: 0.1% or less, Cu: 0.1-2% and Si (%) / 5 or more, Al: 0.1-2%, N: 0.01% or less, Ni: Cu (%) / 3 or more (may not be included when Cu is 0.5% or less) and “Si (%) + Al (%) ⁇ 0.5”, “Mn (%) + Ni (% )> 0.5 ”, a high-strength steel sheet having a structure containing a retained austenite of 5% or more by volume and exhibiting a tensile strength of 650 to 800 MPa is disclosed.
- the present invention has been made in consideration of such circumstances.
- a high-strength steel sheet having a tensile strength of 900 MPa or more the stretch flangeability is improved to improve local deformability, and high-speed tension is applied. It is an object of the present invention to provide a high-strength steel sheet that can improve tensile strength and a method for producing the same.
- the present inventors diligently studied a steel sheet structure and a manufacturing method for achieving both improvement in stretch flangeability and improvement in tensile force when high-speed tension is applied in a high-strength steel sheet. As a result, it was found that by efficiently depositing Cu in the steel sheet, it is possible to improve both stretch flangeability and tensile force when high-speed tension is applied. And in order to form such a structure
- the present invention has been made as a result of further investigation based on the above findings, and the gist thereof is as follows.
- the steel sheet structure includes a ferrite phase and a martensite phase, and the proportion of Cu particles inconsistent with bcc iron is 15% or more with respect to the entire Cu particles, and the Cu particle density in the ferrite phase Is 1.0 ⁇ 10 18 particles / m 3 or more, and the average particle size of Cu particles in the ferrite phase is 2.0 nm or more.
- the structure in the range of 1/8 thickness to 3/8 thickness of the high-strength steel sheet has a volume fraction of ferrite phase: 10 to 75%, bainitic ferrite phase and / or bainite phase: 50% or less
- the high-strength steel sheet having excellent formability as described in (1) above, having a tempered martensite phase: 50% or less, a fresh martensite phase: 15% or less, and a retained austenite phase: 20% or less.
- a slab consisting of: directly or partially cooled and then heated to 1050 ° C. or higher, subjected to rolling at a higher temperature of 800 ° C. and Ar 3 transformation point, and wound at 500 to 700 ° C., The wound steel sheet was heated to a maximum heating temperature of 740 to 1000 ° C. at an average heating rate of 550 to 700 ° C.
- a method for producing a high-strength steel sheet having excellent formability characterized by having an annealing step of cooling at 0.0 to 200.0 ° C./second.
- the steel plate that has been wound is pickled, and thereafter, it has a cold rolling step in which rolling is performed at a rolling reduction of 35 to 75%.
- a method for producing a high-strength steel sheet having excellent formability is a method for producing a high-strength steel sheet having excellent formability.
- a high-strength galvanized steel sheet having excellent formability characterized in that a high-strength steel sheet is produced by the method for producing a high-strength steel sheet according to any one of (4) to (7) and then zinc electroplating is performed. Manufacturing method.
- a high-strength steel sheet that is excellent in formability such as stretch flangeability and excellent in high-speed tensile properties while ensuring a high strength of a tensile maximum strength of 900 MPa or more. Further, it is possible to provide a high-strength galvanized steel sheet having excellent formability such as stretch flangeability and excellent high-speed tensile properties while ensuring high strength of a tensile maximum strength of 900 MPa or more.
- the structure of the high-strength steel sheet of the present invention is not particularly limited as long as it can secure a tensile maximum strength of 900 MPa or more.
- ferrite, bainite, martensite represented by martensite single phase structure, multiphase structure composed of martensite and bainite, double phase structure composed of ferrite and martensite, and multiphase structure composed of ferrite, bainite and retained austenite.
- Any of the structures containing residual austenite alone or in combination may be used.
- these tissues may contain a pearlite structure.
- the ferrite phase contained in the structure of the high-strength steel sheet may be either precipitation strengthened ferrite, as-processed non-recrystallized ferrite, or ferrite in which dislocations are partially recovered.
- the steel structure of the high-strength steel sheet of the present invention is in the range of 1/8 to 3/8 thickness centered on 1/4 of the plate thickness, in volume fraction, ferrite phase: 10 to 75%, bainitic ferrite It is preferable to have a phase and / or bainite phase: 50% or less, a tempered martensite phase: 50% or less, a fresh martensite phase: 15% or less, and a retained austenite phase: 20% or less.
- the high strength steel sheet has such a steel sheet structure, the high strength steel sheet has a better formability.
- the structure in the range of 1/8 to 3/8 thickness is considered to be representative of the entire structure of the steel sheet, and in the range of 1/8 to 3/8 thickness. This is because if the steel sheet structure is as described above, the entire steel sheet can be determined to have the above structure.
- the ferrite phase is a structure effective for improving ductility, and is preferably contained in the steel sheet structure in a volume fraction of 10 to 75%.
- the volume fraction of the ferrite phase is more preferably 15% or more, and further preferably 20% or more, from the viewpoint of ductility. Since the ferrite phase is a soft structure, in order to sufficiently increase the tensile strength of the steel sheet, the volume fraction of the ferrite phase contained in the steel sheet structure is more preferably 65% or less, and further preferably 50% or less. preferable.
- the bainitic ferrite phase and / or bainite phase is a structure having an excellent balance between strength and ductility, and is preferably contained in the steel sheet structure at a volume fraction of 10 to 50%.
- the bainitic ferrite phase and / or bainite phase is a microstructure having an intermediate strength between soft ferrite and hard martensite phase, tempered martensite phase and retained austenite phase, and is 15% from the viewpoint of stretch flangeability. More preferably, it is contained, and more preferably 20% or more.
- the volume fraction of the bainitic ferrite phase and / or bainite phase is 50% or less from the viewpoint of shape freezeability. Is preferred.
- the tempered martensite phase is a structure that greatly improves the tensile strength. From the viewpoint of tensile strength, the volume fraction of the tempered martensite phase is preferably 10% or more. Since the yield stress increases as the volume fraction of the tempered martensite phase contained in the steel sheet structure increases, the volume fraction of the tempered martensite phase is preferably 50% or less from the viewpoint of shape freezeability.
- the fresh martensite phase greatly improves the tensile strength.
- the volume fraction is preferably 15% or less.
- the volume fraction of the fresh martensite phase is more preferably 10% or less, and further preferably 5% or less.
- the residual austenite phase greatly improves strength and ductility.
- the volume fraction is preferably 20% or less.
- the volume fraction of the retained austenite phase is more preferably 15% or less.
- the volume fraction of the retained austenite phase is preferably 3% or more, and more preferably 5% or more.
- the steel sheet structure of the high-strength steel sheet of the present invention may contain other structures such as pearlite and / or coarse cementite.
- the total volume fraction of pearlite and / or coarse cementite contained in the steel sheet structure is preferably 10% or less, and more preferably 5% or less.
- the volume fraction of each structure included in the steel sheet structure of the high-strength steel sheet of the present invention can be measured by, for example, the following method.
- the volume fraction of the retained austenite phase is obtained by performing an X-ray analysis using a plane parallel to the plate surface of the steel sheet and a thickness of 1/4 as an observation surface, calculating an area fraction, and regarding the value as the volume fraction.
- the volume fraction of the ferrite phase, bainitic ferrite phase, bainite phase, tempered martensite phase and fresh martensite phase contained in the steel structure of the high-strength steel plate of the present invention is a thickness cross section parallel to the rolling direction of the steel plate.
- a sample is taken as an observation surface, the observation surface is polished, nital-etched, and a field emission scanning electron microscope (FE-) is used in the range of 1/8 to 3/8 thickness centered on 1/4 of the plate thickness.
- the area fraction is measured by SEM: Field Emission Scanning Electron Microscope), and the value is regarded as the volume fraction.
- the microstructure of the high-strength steel sheet of the present invention is such that the density of Cu particles ⁇ 1.0 ⁇ 10 18 particles / m 3 , the average particle diameter of Cu particles is 2.0 nm or more, and there is no gap between the Cu particles and the surrounding bcc iron. It is necessary that the matching Cu particles be 15% or more of the total Cu particles.
- Bcc iron is a general term for ferrite, bainite and bainitic ferrite whose crystal structure is a body-centered cubic lattice. If the Cu particles are consistent with bcc iron, the strength is greatly improved. Cu particles that are not matched with bcc iron inhibit the development of dislocation substructure in bcc iron, and accordingly, the accumulation of dislocations during large strain deformation is less likely to occur, and the generation of vacancies is suppressed, resulting in stretch flanges. Formability is improved.
- the density of Cu particles is preferably 5.0 ⁇ 10 18 particles / m 3 or more, and more preferably 1.0 ⁇ 10 19 particles / m 3 or more.
- the lower limit of the average particle size of Cu particles is 2.0 nm or more.
- the average particle size of the Cu particles is more preferably 4.0 nm or more, and still more preferably 6.0 nm or more.
- the number of Cu particles inconsistent with bcc iron is less than 15%, the stretch flangeability is not sufficiently improved. Therefore, the number of Cu particles needs to be 15% or more, preferably 25% or more, more preferably 35% or more.
- Cu particle average particle diameter, consistency and density can be performed as follows.
- a sample is cut out from a 1/4 thickness of a steel plate and observed using a high-resolution transmission electron microscope (HRTEM: High Resolution Transmission Electron Microscopy).
- HRTEM High Resolution Transmission Electron Microscopy
- the Cu particles whose composition was confirmed by electron energy loss spectroscopy (EELS: Electron Energy-Loss Spectroscopy) are examined for particle size and consistency with bcc iron.
- the size of the particles is the average of the particle sizes of 20 or more particles. Further, the ratio of precipitates inconsistent with bcc iron in the number of observed particles is obtained.
- the Cu particle density is measured by two methods depending on the average particle diameter.
- the average particle diameter is less than 3 nm, a sample is cut out from a 1/4 thickness of the steel plate and tested using a three-dimensional atom probe (3D-AP). The test is performed until 20 or more Cu particles are obtained or until the measurement volume exceeds 50000 nm 3, and the number of particles is divided by the measurement volume.
- the average particle diameter is 3 nm or more, the number of Cu particles is measured in a visual field of 10,000 nm 2 to 1 ⁇ m 2 and the film thickness of the observation part of the specimen is measured by convergent electron diffraction (CBED: Convergent-Beam Electron Diffraction). Then, the observation volume is obtained by multiplying by the observation area, and the Cu particle density is obtained by dividing the number of Cu particles by the observation volume.
- CBED Convergent-Beam Electron Diffraction
- the means for measuring the composition, particle size, and consistency of the Cu particles are not limited to the above methods.
- observation may be performed using an electrolytic emission transmission electron microscope (FE-TEM: Field-Emission Transmission Elictron Microscope).
- C 0.075 to 0.300% C is contained to increase the strength of the high-strength steel plate. If the C content exceeds 0.300%, the weldability becomes insufficient. From the viewpoint of weldability, the C content is preferably 0.250% or less, and more preferably 0.220% or less. If the C content is less than 0.075%, the strength decreases, and a maximum tensile strength of 900 MPa or more cannot be ensured. In order to increase the strength, the C content is preferably 0.090% or more, and more preferably 0.100% or more.
- Si 0.30 to 2.50% Si is an element necessary for suppressing the formation of iron-based carbides in the steel sheet and enhancing strength and formability. If the Si content exceeds 2.50%, the steel sheet becomes brittle and the ductility deteriorates. From the viewpoint of ductility, the Si content is preferably 2.20% or less, and more preferably 2.00% or less. On the other hand, when the Si content is less than 0.30%, a large amount of coarse iron-based carbide is generated in the annealing process, and the strength and formability deteriorate. In this respect, the lower limit value of Si is preferably 0.50% or more, and more preferably 0.70% or more.
- Mn 1.30 to 3.50% Mn is added to increase the strength of the steel sheet.
- Mn 1.30 to 3.50% Mn is added to increase the strength of the steel sheet.
- the Mn content exceeds 3.50%, a coarse Mn-concentrated portion is generated at the central portion of the plate thickness of the steel sheet, and embrittlement is likely to occur, and troubles such as cracking of the cast slab are likely to occur.
- the Mn content exceeds 3.50%, the weldability is also deteriorated. Therefore, the Mn content needs to be 3.50% or less.
- the Mn content is preferably 3.20% or less, and more preferably 3.00% or less.
- the content of Mn is less than 1.30%, a large amount of soft structure is formed during cooling after annealing, so it becomes difficult to ensure a maximum tensile strength of 900 MPa or more.
- the content needs to be 1.30% or more.
- the Mn content is preferably 1.50% or more, more preferably 1.70% or more.
- P 0.001 to 0.030% P tends to segregate in the central part of the plate thickness of the steel sheet, causing the weld to become brittle. If the P content exceeds 0.030%, the welded portion is significantly embrittled, so the P content is limited to 0.030% or less.
- the lower limit of the P content is not particularly defined, and the effects of the present invention are exhibited. However, if the P content is less than 0.001%, the manufacturing cost increases significantly, so 0.001% is made the lower limit.
- the upper limit of the S content is set to 0.0100% or less. Since S combines with Mn to form coarse MnS and lowers ductility and stretch flangeability, it is preferably 0.0050% or less, and more preferably 0.0025% or less.
- the lower limit of the content of S is not particularly defined, and the effect of the present invention is exhibited. However, if the S content is less than 0.0001%, the manufacturing cost increases significantly, so 0.0001% is set as the lower limit.
- Al 0.005-1.500%
- Al suppresses the production of iron-based carbides and increases the strength and formability of the steel sheet. If the Al content exceeds 1.500%, weldability deteriorates, so the upper limit of the Al content is 1.500%. From the viewpoint of weldability, the Al content is preferably 1.200% or less, and more preferably 0.900% or less.
- Al is an element that is also effective as a deoxidizing material, but if the Al content is less than 0.005%, the effect as a deoxidizing material cannot be sufficiently obtained, so the lower limit of the Al content is 0.005%. That's it. In order to obtain a sufficient deoxidation effect, the Al content is preferably 0.010% or more.
- N 0.0001 to 0.0100% N forms coarse nitrides and deteriorates ductility and stretch flangeability, so the content needs to be suppressed. If the N content exceeds 0.0100%, this tendency becomes significant, so the N content is set to 0.0100% or less. Moreover, since N causes the generation
- the lower limit of the N content is not particularly defined, and the effects of the present invention are exhibited. However, if the N content is less than 0.0001%, the manufacturing cost increases significantly, so 0.0001% is set as the lower limit.
- O 0.0001 to 0.0100% Since O forms an oxide and deteriorates ductility and stretch flangeability, it is necessary to suppress the content. When the content of O exceeds 0.0100%, the stretch flangeability is significantly deteriorated, so the O content is set to 0.0100% or less.
- the O content is preferably 0.0080% or less, and more preferably 0.0060% or less.
- the lower limit of the content of O is not particularly defined, and the effect of the present invention is exhibited. However, if the O content is less than 0.0001%, the manufacturing cost increases significantly, so 0.0001% is made the lower limit.
- Cu 0.15-2.00%
- Cu is an important element in the present invention.
- Cu exists in steel as fine particles.
- Cu particles that are matched or semi-matched to the surrounding bcc phase particularly increase the strength of the steel sheet.
- Cu particles that are inconsistent with the surrounding bcc iron improve formability, particularly by suppressing the development of dislocation substructures inside the steel sheet.
- the Cu content needs to be 0.15% or more.
- the Cu content is preferably 0.30% or more, and more preferably 0.40% or more.
- the Cu content exceeds 2.00%, weldability is impaired, so the Cu content is 2.00% or less.
- the Cu content is preferably 1.80% or less, and more preferably 1.50% or less.
- the high-strength steel plate of the present invention may further contain the following elements as necessary.
- Ni 0.01-2.00% Ni may be positively added for the purpose of improving productivity in order to suppress embrittlement caused by addition of Cu in a high temperature range.
- the Ni content needs to be 0.01% or more, preferably 0.05% or more, and more preferably 0.10% or more. If it exceeds 2.00%, weldability is impaired, so the Ni content is 2.00% or less.
- Ti is an element that contributes to increasing the strength of the steel sheet by strengthening precipitates, strengthening fine grains by suppressing the growth of ferrite crystal grains, and dislocation strengthening by suppressing recrystallization. If the Ti content exceeds 0.150%, precipitation of carbonitride increases and formability deteriorates, so the Ti content is set to 0.150% or less. From the viewpoint of moldability, the Ti content is more preferably 0.100% or less, and further preferably 0.070% or less. In order to sufficiently obtain the effect of increasing the strength due to Ti, the Ti content needs to be 0.005% or more. In order to increase the strength of the steel sheet, the Ti content is more preferably 0.010% or more, and further preferably 0.015% or more.
- Nb is an element that contributes to increasing the strength of the steel sheet by strengthening precipitates, strengthening fine grains by suppressing the growth of ferrite crystal grains, and dislocation strengthening by suppressing recrystallization. If the Nb content exceeds 0.150%, carbonitride precipitation increases and the formability deteriorates, so the Nb content is set to 0.150% or less. From the viewpoint of moldability, the Nb content is more preferably 0.100% or less, and further preferably 0.060% or less. In order to sufficiently obtain the effect of increasing the strength by Nb, the Nb content needs to be 0.005% or more. In order to increase the strength of the steel sheet, the Nb content is more preferably 0.010% or more, and further preferably 0.015% or more.
- V 0.005 to 0.150%
- V is an element that contributes to increasing the strength of the steel sheet by strengthening precipitates, strengthening fine grains by suppressing the growth of ferrite crystal grains, and dislocation strengthening by suppressing recrystallization. If the V content exceeds 0.150%, carbonitride precipitation increases and the formability deteriorates. Therefore, the V content is 0.150% or less. In order to sufficiently obtain the effect of increasing the strength due to V, the content of V needs to be 0.005% or more.
- B 0.0001 to 0.0100%
- B is an element that suppresses phase transformation at a high temperature and is effective for increasing the strength, and may be added instead of a part of C and / or Mn. If the B content exceeds 0.0100%, the hot workability is impaired and the productivity decreases, so the B content is set to 0.0100% or less. From the viewpoint of productivity, the B content is more preferably 0.0050% or less, and further preferably 0.0030% or less. In order to sufficiently obtain a high strength by B, the B content needs to be 0.0001% or more. For increasing the strength, the B content is more preferably 0.0003% or more, and more preferably 0.0005% or more.
- Mo 0.01 to 1.00%
- Mo is an element that suppresses phase transformation at high temperature and is effective for increasing the strength, and may be added instead of a part of C and / or Mn. If the Mo content exceeds 1.00%, hot workability is impaired and productivity is lowered, so the Mo content is set to 1.00% or less. In order to sufficiently obtain high strength by Mo, the Mo content needs to be 0.01% or more.
- W 0.01-1.00%
- W is an element that suppresses phase transformation at high temperatures and is effective for increasing the strength, and may be added instead of a part of C and / or Mn. If the W content exceeds 1.00%, the hot workability is impaired and the productivity is lowered, so the W content is 1.00% or less. In order to sufficiently increase the strength by W, the W content needs to be 0.01% or more.
- Cr 0.01 to 2.00% Cr is an element that suppresses phase transformation at high temperature and is effective for increasing the strength, and may be added instead of a part of C and / or Mn. If the Cr content exceeds 2.00%, the hot workability is impaired and the productivity is lowered, so the Cr content is 2.00% or less. In order to sufficiently obtain high strength by Cr, the Cr content needs to be 0.01% or more.
- Ca, Ce, Mg, Zr, Hf, and REM in total 0.0001 to 0.5000% are effective elements for improving moldability, and one or more of them can be added. If the total content of one or more selected from Ca, Ce, Mg and REM exceeds 0.5000%, the ductility may be impaired, so the total content of each element is 0.5000%.
- the total content of each element needs to be 0.0001% or more. From the viewpoint of moldability, the total content of each element is more preferably 0.0005% or more, and further preferably 0.0010% or more.
- REM is an abbreviation for Rare Earth Metal and refers to an element belonging to the lanthanoid series.
- REM and Ce are often added by misch metal and may contain a lanthanoid series element in combination with La and Ce. Even if these lanthanoid series elements other than La and Ce are included as inevitable impurities, the effect of the present invention is exhibited. Even if the metal La or Ce is added, the effect of the present invention is exhibited.
- the component composition of this invention was demonstrated, as long as it is a range which does not impair the characteristic of the steel plate of this invention, you may contain elements other than an essential additive element as an impurity resulting from a raw material, for example.
- the high-strength steel sheet of the present invention can be a high-strength galvanized steel sheet having a galvanized layer or an alloyed galvanized layer formed on the surface.
- a galvanized layer on the surface of a high-strength steel plate, a steel plate having excellent corrosion resistance is obtained.
- the alloyed galvanized layer on the surface of the high-strength steel plate, the steel plate has excellent corrosion resistance and excellent paint adhesion.
- a slab having the above-described component composition is cast.
- a slab produced by a continuous casting slab, a thin slab caster or the like can be used.
- CC-DR continuous casting-direct rolling
- the slab heating temperature in the hot rolling process needs to be 1050 ° C. or higher. If the slab heating temperature is low, the finish rolling temperature is below the Ar 3 point. As a result, since it becomes a two-phase rolling of ferrite and austenite, the hot-rolled sheet structure becomes a heterogeneous mixed grain structure, and even if it undergoes cold rolling and annealing processes, the heterogeneous structure is not eliminated, ductility and bendability Deteriorates. Moreover, when finish rolling temperature falls, there exists a possibility that rolling load will increase, rolling may become difficult, or the shape defect of the steel plate after rolling may be caused.
- the upper limit of the slab heating temperature is not particularly defined, and the effect of the present invention is exhibited. However, since it is not economically preferable to make the heating temperature excessively high, the upper limit of the slab heating temperature is 1350 ° C. or less. Is preferred.
- Ar 3 points can be calculated by the following equation.
- Ar 3 (° C.) 901-325 ⁇ C + 33 ⁇ Si-92 ⁇ (Mn + Ni / 2 + Cr / 2) + Cu / 2 + Mo / 2) + 52 ⁇ Al
- C, Si, Mn, Ni, Cr, Cu, Mo, and Al are the contents (mass%) of each element.
- the hot rolling finish rolling temperature has a lower limit of 800 ° C. or a higher Ar 3 point, and an upper limit of 1000 ° C.
- the finish rolling temperature is less than 800 ° C.
- the finish rolling temperature is less than Ar 3 points, the hot rolling becomes a two-phase rolling of a ferrite phase and an austenite phase, and the structure of the hot-rolled steel sheet may be a heterogeneous mixed grain structure.
- the upper limit of the finish rolling temperature is not particularly defined, and the effect of the present invention is exhibited. However, if the finish rolling temperature is excessively high, the slab heating temperature must be excessively high in order to secure the temperature. . Therefore, the upper limit temperature of the finish rolling temperature is preferably 1000 ° C. or less.
- the rolled steel sheet is wound up at 500 to 700 ° C.
- the coiling temperature is preferably 680 ° C. or lower, and more preferably 660 ° C. or lower.
- the coiling temperature is preferably 550 ° C. or higher, and more preferably 600 ° C. or higher.
- the steel sheet after winding is preferably cooled at a cooling rate of 25 ° C./hour or less. This is to advance the precipitation of Cu.
- the hot-rolled steel sheet manufactured in this way is subjected to pickling treatment.
- pickling it is possible to remove oxides on the surface of the steel sheet, and the chemical conversion of the cold-rolled high-strength steel sheet of the final product and the hot-plating of the cold-rolled steel sheet for hot-dip galvanized or alloyed hot-dip galvanized steel sheets It is important from the point of improving. Pickling may be performed only once or may be performed in multiple steps.
- the steel plate after pickling may be subjected to an annealing process as it is, but by performing cold rolling at a rolling reduction of 35 to 75%, a steel plate having an excellent shape with high thickness accuracy can be obtained. If the rolling reduction is less than 35%, it is difficult to keep the shape flat, and the ductility of the final product becomes poor, so the rolling reduction is set to 35% or more. When the rolling reduction exceeds 75%, the cold rolling load becomes excessively large and cold rolling becomes difficult. For this reason, the upper limit of the rolling reduction is set to 75%.
- the effect of the present invention is exhibited without particular limitation on the number of rolling passes and the rolling reduction for each pass.
- the obtained hot-rolled steel sheet or cold-rolled steel sheet is annealed.
- the average heating rate at 550 to 700 ° C. is set to 1.0 to 10.0 ° C./second, preferably 2.0 to 5.0 ° C./second, and heating is performed up to the maximum heating temperature.
- the maximum heating temperature is 740 to 1000 ° C.
- the crystal structure of the Cu precipitate generated in the previous hot rolling process is set to fcc (face-centered cubic lattice).
- fcc face-centered cubic lattice
- the maximum heating temperature is less than 740 ° C.
- coarse iron-based carbides remain undissolved in the steel sheet and serve as a starting point for fracture, so that formability is significantly deteriorated.
- the maximum heating temperature is preferably 760 ° C. or higher.
- the maximum heating temperature exceeds 1000 ° C., Cu particles are dissolved during heating, and Cu particles inconsistent with bcc iron are reduced, so that stretch flangeability is deteriorated.
- the maximum heating temperature is preferably 970 ° C. or less, and more preferably 950 ° C. or less.
- the steel sheet is cooled at an average cooling rate between the maximum heating temperature and 700 ° C. of 1.0 to 10.0 ° C./second, and further, distortion is applied to the steel sheet in the temperature range of the maximum heating temperature to 700 ° C.
- a method for imparting strain for example, a method in which bending is performed once or more in a range where the tensile strain amount on the outermost periphery is 0.0007 or more and 0.0910 or less while applying a tension of 5 to 50 MPa is used. be able to. As a result, nucleation of Cu precipitates that are matched or semi-matched with the surrounding bcc phase can be newly promoted.
- the bent steel plate may be bent back.
- the tension applied to the steel sheet is less than 5 MPa, the precipitation of Cu particles may not be sufficiently promoted.
- the tension is more preferably 10 MPa or more, and further preferably 15 MPa or more. If the tension exceeds 50 MPa, the steel sheet may be plastically deformed and the shape may not be maintained.
- the amount of strain is preferably 0.0010 or more. Since the shape cannot be maintained when the strain amount exceeds 0.0910, the strain amount is preferably 0.0910 or less. In order to maintain the shape of the steel sheet, the strain amount is more preferably 0.0500 or less, and further preferably 0.0250 or less.
- the thickness of the steel plate is preferably 0.6 mm or more and 10.0 mm or less. If the thickness is less than 0.6 mm, the shape of the steel sheet may not be maintained. When the thickness exceeds 10.0 mm, it becomes difficult to control the temperature inside the steel sheet.
- Bending can be performed, for example, by pressing against a roll while applying tension.
- the roll diameter is preferably 800 mm or less in order to obtain a sufficient amount of strain.
- the diameter of a roll shall be 50 mm or more.
- Bs point bainite transformation start temperature
- 500 ° C. at a cooling rate of 5.0 to 200.0 ° C./second. Since the formation of bainite or bainitic ferrite starts at a temperature below the Bs point, the cooling rate may be lowered. Even if the temperature is higher than the Bs point, ferrite hardly grows below 500 ° C., so the cooling rate may be slowed.
- the Bs point can be calculated by the following formula.
- VF the volume fraction of ferrite
- C, Mn, Cr, Ni, Al, and Si addition amounts (mass%) of the respective elements.
- the present invention since it is difficult to directly measure the volume fraction of the ferrite phase during the production of the high-strength steel plate, in the present invention, a small piece of cold-rolled steel plate before passing through the continuous annealing line is cut out, and the small piece Is annealed with the same temperature history as when passing through a continuous annealing line, the change in the volume of ferrite in small pieces is measured, and the numerical value calculated using the result is defined as the volume fraction of ferrite VF.
- the result of the first measurement may be used, and it is not necessary to measure each time. If the manufacturing conditions are to be changed significantly, measure again. Of course, the microstructure of the steel sheet actually manufactured may be observed and fed back to subsequent manufacturing.
- the annealed steel sheet is retained at 250 to 500 ° C. for 60 to 1000 seconds to form a hard structure and then cooled to room temperature. After cooling to room temperature, 0.05 to 3.00% cold rolling may be performed for the purpose of shape correction.
- the annealed steel sheet may be electroplated to form a plated steel sheet. Further, during cooling from the maximum heating temperature to room temperature, for example, after cooling to 500 ° C. or after a retention treatment, it may be immersed in a galvanizing bath to obtain a hot dip galvanized steel sheet. After the steel sheet is immersed in the galvanizing bath, an alloying treatment may be performed in the range of 470 to 650 ° C. Furthermore, you may form the membrane
- heating was performed between 550 and 700 ° C. at the average heating rate described in Table 7 to Table 10 up to the maximum heating temperature described in Table 7 to Table 10.
- cooling is performed at the average cooling rate described in Table 7 to Table 10, and then further cooled to the range of 250 to 500 ° C., and described in Table 7 to Table 10. After stopping for a period of time, it was cooled to room temperature.
- Experimental examples 29, 33, 43, 60, and 69 are examples in which an electroplating process was performed after the annealing step to obtain a galvanized steel sheet (EG).
- Experimental Examples 18, 21, 81, and 84 are examples in which a hot-dip galvanized steel sheet (GI) was obtained by immersing in a galvanizing bath after stopping at a temperature of 250 to 500 ° C. and then cooling to room temperature.
- GI hot-dip galvanized steel sheet
- Experimental Examples 38, 48, 51, 66, 72, 87 and 90 were immersed in a galvanizing bath after stopping in the range of 250 to 500 ° C., further subjected to alloying treatment at the described temperature, and galvannealed steel sheets. This is an example of (GA).
- Experimental examples 38 and 72 are examples in which a film made of a P-based composite oxide was further applied to the surface of the plating layer.
- Tables 11 to 14 show the results of measuring the fraction of the microstructure in the range of 1/8 to 3/8 thickness of the steel sheets of Experimental Examples 1 to 114.
- the amount of retained austenite was measured by X-ray diffraction, and the others were cut out of a plate thickness section parallel to the rolling direction, and the mirror-polished section was nital-etched to produce a field emission type. This was determined by observation using a scanning electron microscope (FE-SEM: field : emission scanning electron microscope).
- Tables 15 to 18 show the observation results of Cu precipitates.
- the Cu deposit was observed using the high-resolution transmission electron microscope (HRTEM).
- HRTEM high-resolution transmission electron microscope
- EELS electron energy loss spectroscopy
- the particle size was the average of the particle size of 25 particles. Further, the ratio of precipitates inconsistent with bcc iron in the number of observed particles was determined.
- Tables 19 to 22 show the characteristic evaluation results of the steel plates of Experimental Examples 1 to 114.
- Tensile test pieces in accordance with JIS Z 2201 were collected from the steel sheets of Experimental Examples 1-114, and the tensile test was conducted in accordance with JIS Z 2241. Yield strength (YS), tensile strength (TS), total elongation (EL) The hole expansion rate ( ⁇ ) was measured.
- Experimental Example 5 is an example in which the completion temperature of hot rolling is low, and the microstructure becomes inhomogeneous in one direction, so that ductility and stretch flangeability are inferior.
- Experimental Example 15 has a high heating rate, insufficient growth of Cu particles, a small proportion of Cu particles inconsistent with bcc iron, and poor stretch flangeability.
- Experimental Example 20 is an example in which the maximum heating temperature in the annealing process is low, and includes a large number of coarse iron-based carbides that are the starting points of fracture, so that ductility and stretch flangeability are inferior.
- Experimental Example 23 is an example in which the maximum heating temperature in the annealing process is high, and Cu particles are once dissolved during heating, and there are few Cu particles inconsistent with bcc iron, so that stretch flangeability is inferior.
- Experimental Example 30 is an example in which the average cooling rate in the first cooling step is high, Cu particles are not sufficiently precipitated, and the soft tissue is insufficiently grown, so the ductility and stretch flangeability are inferior. is there.
- Experimental Example 34 is an example in which the average cooling rate in the first cooling step is low, coarse iron-based carbides are generated, and stretch flangeability is inferior.
- Experimental Example 35 is an example in which there is no tension in the first cooling step, Cu is insufficiently precipitated, and stretch flangeability is inferior.
- Experimental Example 40 is an example in which the bending process in the first cooling step is not performed, Cu is insufficiently precipitated, and the stretch flangeability is inferior.
- Experimental Examples 97 to 100 are examples in which the component composition deviates from the predetermined range, and none of the characteristics has been obtained.
- Experimental example 101 is an example where the lower limit of the amount of Cu is not reached, the Cu particle density is low, and the stretch flangeability is inferior.
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Abstract
Description
鋼板に5~50MPaの張力をかけつつ、最外周の引張ひずみ量が0.0007~0.0910となる範囲で、1回以上の曲げ加工を施すことにより行われる
ことを特徴とする前記(4)又は(5)の成形性に優れた高強度鋼板の製造方法。
フェライト相は、延性の向上に有効な組織であり、鋼板組織に体積分率で10~75%含まれていることが好ましい。フェライト相の体積分率は、延性の観点からは15%以上含まれることがより好ましく、20%以上含まれることがさらに好ましい。フェライト相は軟質な組織であるため、鋼板の引張強度を十分高めるには、鋼板組織に含まれるフェライト相の体積分率を65%以下とすることがより好ましく、50%以下とすることがさらに好ましい。
ベイニティックフェライト相及び/又はベイナイト相は、強度と延性のバランスに優れた組織であり、鋼板組織に体積分率で10~50%含まれていることが好ましい。また、ベイニティックフェライト相及び/又はベイナイト相は軟質なフェライトと硬質なマルテンサイト相、焼戻しマルテンサイト相及び残留オーステナイト相の中間の強度を有するミクロ組織であり、伸びフランジ性の観点から15%以上含まれることがより好ましく、20%以上含まれることがさらに好ましい。ベイニティックフェライト相及び/又はベイナイト相の体積分率が高くなると降伏応力が高くなるので、形状凍結性の観点からは、ベイニティックフェライト相及び/又はベイナイト相の体積分率は50%以下が好ましい。
焼戻しマルテンサイト相は、引張強度を大きく向上させる組織である。引張強度の観点から、焼戻しマルテンサイト相の体積分率は10%以上とすることが好ましい。鋼板組織に含まれる焼戻しマルテンサイト相の体積分率が高くなると降伏応力が高くなるので、形状凍結性の観点からは、焼戻しマルテンサイト相の体積分率は50%以下が好ましい。
フレッシュマルテンサイト相は、引張強度を大きく向上させる。一方、破壊の起点となって伸びフランジ性を劣化させることがあるので、体積分率で15%以下とすることが好ましい。伸びフランジ性を高めるには、フレッシュマルテンサイト相の体積分率を10%以下とすることがより好ましく、5%以下とすることがさらに好ましい。
残留オーステナイト相は、強度及び延性を大きく向上させる。一方、破壊の起点となって伸びフランジ性を劣化させることがあるので、体積分率で20%以下とすることが好ましい。伸びフランジ性を高めるには、残留オーステナイト相の体積分率を15%以下とすることがより好ましい。強度及び延性を向上させる効果を得るには、残留オーステナイト相の体積分率が3%以上あることが好ましく、さらに好ましくは5%以上である。
本発明の高強度鋼板の鋼板組織には、パーライト及び/又は粗大なセメンタイトなど上記以外の組織が含まれていてもよい。しかし、高強度鋼板の鋼板組織中にパーライト及び/又は粗大なセメンタイトが多くなると、曲げ性が劣化する。したがって、鋼板組織に含まれるパーライト及び/又は粗大なセメンタイトの体積分率は、合計で10%以下であることが好ましく、5%以下であることがより好ましい。
Cは、高強度鋼板の強度を高めるために含有される。Cの含有量が0.300%を超えると溶接性が不十分となる。溶接性の観点から、Cの含有量は0.250%以下であることが好ましく、0.220%以下であることがより好ましい。Cの含有量が0.075%未満であると強度が低下し、900MPa以上の引張最大強度を確保することができない。強度を高めるため、Cの含有量は0.090%以上であることが好ましく、0.100%以上であることがより好ましい。
Siは、鋼板における鉄系炭化物の生成を抑制し、強度と成形性を高めるために必要な元素である。Siの含有量が2.50%を超えると鋼板が脆化し、延性が劣化する。延性の観点から、Siの含有量は2.20%以下であることが好ましく、2.00%以下であることがより好ましい。一方、Siの含有量が0.30%未満では、焼鈍工程において粗大な鉄系炭化物が多量に生成し、強度及び成形性が劣化する。この観点から、Siの下限値は0.50%以上であることが好ましく、0.70%以上がより好ましい。
Mnは、鋼板の強度を高めるために添加される。Mnの含有量が3.50%を超えると、鋼板の板厚中央部に粗大なMn濃化部が生じ、脆化が起こりやすくなり、鋳造したスラブが割れるなどのトラブルが起こりやすい。また、Mnの含有量が3.50%を超えると溶接性も劣化する。したがって、Mnの含有量は、3.50%以下とする必要がある。溶接性の観点から、Mnの含有量は3.20%以下であることが好ましく、3.00%以下であることがより好ましい。一方、Mnの含有量が1.30%未満であると、焼鈍後の冷却中に軟質な組織が多量に形成されるため、900MPa以上の引張最大強度を確保することが難しくなるので、Mnの含有量を1.30%以上とする必要がある。強度を高めるため、Mnの含有量は1.50%以上であることが好ましく、1.70%以上であることがより好ましい。
Pは鋼板の板厚中央部に偏析する傾向があり、溶接部を脆化させる。Pの含有量が0.030%を超えると溶接部が大幅に脆化するので、Pの含有量は0.030%以下に制限する。Pの含有量の下限は、特に定めることなく本発明の効果は発揮される。しかし、Pの含有量を0.001%未満とすると製造コストが大幅に増加するので、0.001%を下限値とする。
Sは、溶接性、並びに鋳造時及び熱延時の製造性に悪影響を及ぼす。よって、Sの含有量の上限値を0.0100%以下とする。SはMnと結びついて粗大なMnSを形成して延性や伸びフランジ性を低下させるので、0.0050%以下とすることが好ましく、0.0025%以下とすることがより好ましい。Sの含有量の下限は、特に定めることなく本発明の効果は発揮される。しかし、Sの含有量を0.0001%未満とすると製造コストが大幅に増加するので、0.0001%を下限値とする。
Alは鉄系炭化物の生成を抑えて鋼板の強度及び成形性を高める。Alの含有量が1.500%を超えると溶接性が悪化するので、Alの含有量の上限は1.500%とする。溶接性の観点からは、Alの含有量は1.200%以下とすることが好ましく、0.900%以下とすることがより好ましい。Alは脱酸材としても有効な元素であるが、Alの含有量が0.005%未満では脱酸材としての効果が十分に得られないので、Alの含有量の下限は0.005%以上とする。脱酸の効果を十分に得るためには、Al量は0.010%以上とすることが好ましい。
Nは、粗大な窒化物を形成し、延性及び伸びフランジ性を劣化させるので、含有量を抑える必要がある。Nの含有量が0.0100%を超えると、この傾向が顕著となるので、N含有量は0.0100%以下とする。また、Nは、溶接時のブローホール発生の原因になるので、含有量は少ない方がよい。Nの含有量の下限は、特に定めることなく本発明の効果は発揮される。しかし、Nの含有量を0.0001%未満にすると、製造コストが大幅に増加するので、0.0001%を下限値とする。
Oは、酸化物を形成し、延性及び伸びフランジ性を劣化させるので、含有量を抑える必要がある。Oの含有量が0.0100%を超えると、伸びフランジ性の劣化が顕著となるので、O含有量は0.0100%以下とする。Oの含有量は0.0080%以下であることが好ましく、0.0060%以下であることがさらに好ましい。Oの含有量の下限は、特に定めることなく本発明の効果は発揮される。しかし、Oの含有量を0.0001%未満と製造コストが大幅に増加するので、0.0001%を下限とする。
Cuは、本発明における重要な元素である。Cuは微細な粒子として鋼中に存在する。周辺のbcc相に対して整合あるいは半整合であるCu粒子は、特に鋼板の強度を高める。周辺のbcc鉄に対して非整合であるCu粒子は、特に鋼板内部における転位下部組織の発達を抑制することによって、成形性を高める。本発明においては、Cu粒子の効果を十分に得るため、Cuの含有量を0.15%以上とする必要がある。Cuの含有量は0.30%以上であることが好ましく、0.40%以上であることがさらに好ましい。一方、Cuの含有量が2.00%を超えると、溶接性が損なわれるので、Cuの含有量は2.00%以下とする。溶接性の観点からは、Cuの含有量は1.80%以下であることが好ましく、1.50%以下であることがさらに好ましい。
Niは、高温域においてCu添加に起因して生じる脆化を抑制するため、生産性向上を目的として積極的に添加しても構わない。この効果を得るには、Niの含有量を0.01%以上とする必要があり、0.05%以上とすることが好ましく、0.10%以上とすることがさらに好ましいNiの含有量が2.00%を超えると、溶接性が損なわれるので、Niの含有量は2.00%以下とする。
Tiは、析出物強化、フェライト結晶粒の成長抑制による細粒強化及び再結晶の抑制を通じた転位強化によって、鋼板の強度上昇に寄与する元素である。Tiの含有量が0.150%を超えると、炭窒化物の析出が多くなり成形性が劣化するので、Tiの含有量は0.150%以下とする。成形性の観点からは、Tiの含有量は0.100%以下であることがより好ましく、0.070%以下であることがさらに好ましい。Tiによる強度上昇効果を十分に得るにはTiの含有量を0.005%以上とする必要がある。鋼板の高強度化には、Tiの含有量は0.010%以上であることがより好ましく、0.015%以上であることがさらに好ましい。
Nbは、析出物強化、フェライト結晶粒の成長抑制による細粒強化及び再結晶の抑制を通じた転位強化によって、鋼板の強度上昇に寄与する元素である。Nbの含有量が0.150%を超えると、炭窒化物の析出が多くなり成形性が劣化するので、Nbの含有量は0.150%以下とする。成形性の観点からは、Nbの含有量を0.100%以下であることがより好ましく、0.060%以下であることがさらに好ましい。Nbによる強度上昇効果を十分に得るにはNbの含有量を0.005%以上とする必要がある。鋼板の高強度化には、Nbの含有量は0.010%以上であることがより好ましく、0.015%以上であることがさらに好ましい。
Vは、析出物強化、フェライト結晶粒の成長抑制による細粒強化及び再結晶の抑制を通じた転位強化によって、鋼板の強度上昇に寄与する元素である。Vの含有量が0.150%を超えると、炭窒化物の析出が多くなり成形性が劣化するので、Vの含有量は0.150%以下でとする。Vによる強度上昇効果を十分に得るにはVの含有量を0.005%以上とする必要がある。
Bは高温での相変態を抑制し、高強度化に有効な元素であり、C及び/又はMnの一部に代えて添加してもよい。Bの含有量が0.0100%を超えると、熱間での加工性が損なわれ生産性が低下するので、Bの含有量は0.0100%以下とする。生産性の観点からは、Bの含有量は0.0050%以下であることがより好ましく、0.0030%以下であることがさらに好ましい。Bによる高強度化を十分に得るには、Bの含有量を0.0001%以上とする必要がある。高強度化には、Bの含有量が0.0003%以上であることがより好ましく、0.0005%以上であることがより好ましい。
Moは高温での相変態を抑制し、高強度化に有効な元素であり、C及び/又はMnの一部に代えて添加してもよい。Moの含有量が1.00%を超えると、熱間での加工性が損なわれ生産性が低下するので、Moの含有量は1.00%以下とする。Moによる高強度化を十分に得るには、Moの含有量は0.01%以上とする必要がある。
Wは高温での相変態を抑制し、高強度化に有効な元素であり、C及び/又はMnの一部に代えて添加してもよい。Wの含有量が1.00%を超えると、熱間での加工性が損なわれ生産性が低下するので、Wの含有量は1.00%以下とする。Wによる高強度化を十分に得るには、Wの含有量は0.01%以上とする必要がある。
Crは高温での相変態を抑制し、高強度化に有効な元素であり、C及び/又はMnの一部に代えて添加してもよい。Crの含有量が2.00%を超えると、熱間での加工性が損なわれ生産性が低下するので、Crの含有量は2.00%以下とする。Crによる高強度化を十分に得るには、Crの含有量は0.01%以上とする必要がある。
Ca、Ce、Mg、REMは、成形性の改善に有効な元素であり、1種又は2種以上を添加できる。Ca、Ce、Mg及びREMから選択した1種又は2種以上の含有量の合計が0.5000%を超えると、延性を損なうおそれがあるので、各元素の含有量の合計が0.5000%以下とする。鋼板の成形性を改善する効果を十分に得るには、各元素の含有量の合計が0.0001%以上とする必要がある。成形性の観点からは、各元素の含有量の合計は0.0005%以上であることがより好ましく、0.0010%以上であることがさらに好ましい。
+Cu/2+Mo/2)+52×Al
-50Ni+70Al
上式において、VFはフェライトの体積分率であり、C、Mn、Cr、Ni、Al、Siは、それぞれの元素の添加量(質量%)である。
Claims (10)
- 質量%で、
C :0.075~0.300%、
Si:0.30~2.50%、
Mn:1.30~3.50%、
P :0.001~0.030%、
S :0.0001~0.0100%、
Al:0.005~1.500%、
Cu:0.15~2.00%、
N :0.0001~0.0100%、
O :0.0001~0.0100%
を含有し、選択元素として、
Ti:0.005~0.150%、
Nb:0.005~0.150%、
B :0.0001~0.0100%、
Cr:0.01~2.00%、
Ni:0.01~2.00%、
Mo:0.01~1.00%、
W :0.01~1.00%、
V :0.005~0.150%、
Ca、Ce、Mg、REMの1種又は2種以上:合計で0.0001~0.50%
を含有し、残部が鉄及び不可避的不純物からなる鋼板であり、
前記鋼板組織が、フェライト相とマルテンサイト相を含み、
bcc鉄と非整合なCu粒子の割合が、Cu粒子全体に対し15%以上であり、
フェライト相中のCu粒子密度が、1.0×1018個/m3以上であり、
フェライト相中のCu粒子の平均粒径が、2.0nm以上である
ことを特徴とする成形性に優れた高強度鋼板。 - 前記高強度鋼板の1/8厚~3/8厚の範囲の組織が、体積分率で、
フェライト相:10~75%、
ベイニティックフェライト相及び/又はベイナイト相:50%以下、
焼戻しマルテンサイト相:50%以下、
フレッシュマルテンサイト相:15%以下、
残留オーステナイト相:20%以下
を有することを特徴とする請求項1に記載の成形性に優れた高強度鋼板。 - 請求項1又は2のいずれか1項に記載の高強度鋼板の表面に亜鉛めっき層が形成されてなることを特徴とする成形性に優れた高強度亜鉛めっき鋼板。
- 質量%で、
C :0.075~0.300%、
Si:0.30~2.50%、
Mn:1.30~3.50%、
P :0.001~0.030%、
S :0.0001~0.0100%、
Al:0.005~1.500%、
Cu:0.15~2.00%、
N :0.0001~0.0100%、
O :0.0001~0.0100%
を含有し、選択元素として、
Ti:0.005~0.150%、
Nb:0.005~0.150%、
B :0.0001~0.0100%、
Cr:0.01~2.00%、
Ni:0.01~2.00%、
Mo:0.01~1.00%、
W :0.01~1.00%、
V :0.005~0.150%、
Ca、Ce、Mg、REMの1種又は2種以上:合計で0.0001~0.50%
を含有し、残部が鉄及び不可避的不純物からなるスラブを、直接又は一端冷却した後1050℃以上に加熱し、800℃とAr3変態点のうち高い方の温度を下限として圧延を施し、500~700℃で巻取る熱間圧延工程と、
巻取られた鋼板を550~700℃での平均加熱速度を1.0~10.0℃/秒として、最高加熱温度740~1000℃まで加熱し、その後、最高加熱温度~700℃間の平均冷却速度を1.0~10.0℃/秒として冷却し、かつ、最高加熱温度~700℃の間に、鋼板に歪を付与し、700℃~Bs点又は500℃までの冷却速度を5.0~200.0℃/秒として冷却する焼鈍工程
を有することを特徴とする成形性に優れた高強度鋼板の製造方法。 - 前記熱間圧延工程の後、前記焼鈍工程の前に、
巻き取られた鋼板を酸洗し、その後、圧下率35~75%の圧下率で圧延を施す冷間圧延工程
を有することを特徴とする請求項4に記載の成形性に優れた高強度鋼板の製造方法。 - 前記焼鈍工程中の鋼板への歪の付与は、
鋼板に5~50MPaの張力をかけつつ、最外周の引張ひずみ量が0.0007~0.0910となる範囲で、1回以上の曲げ加工を施すことにより行われる
ことを特徴とする請求項4又は5に記載の成形性に優れた高強度鋼板の製造方法。 - 前記曲げ加工は、ロール径800mm以下のロールに鋼板を押しつけることにより施すことを特徴とする請求項6に記載の成形性に優れた高強度鋼板の製造方法。
- 請求項4又は5に記載の高強度鋼板の製造方法で高強度鋼板を製造した後、亜鉛電気めっきを施すことを特徴とする成形性に優れた高強度亜鉛めっき鋼板の製造方法。
- 請求項4又は5に記載の高強度鋼板の製造方法において、Bs点又は500℃までの冷却の後、溶融亜鉛めっきを施すことを特徴とする成形性に優れた高強度亜鉛めっき鋼板の製造方法。
- 前記溶融亜鉛めっきを施した後に、470~650℃の温度で合金化処理を施すことを特徴とする請求項9に記載の成形性に優れた高強度亜鉛めっき鋼板の製造方法。
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- 2012-07-27 KR KR1020147001742A patent/KR101601566B1/ko active IP Right Grant
- 2012-07-27 CN CN201280036158.3A patent/CN103703156B/zh active Active
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JP2016514211A (ja) * | 2013-03-13 | 2016-05-19 | シティー、ユニバーシティー、オブ、ホンコンCity University Of Hong Kong | 銅リッチナノクラスター強化超高強度フェライト鋼およびその製造方法 |
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JP2016156033A (ja) * | 2015-02-23 | 2016-09-01 | 新日鐵住金株式会社 | 伸びフランジ性に優れる析出強化型複合組織冷延鋼板およびその製造方法 |
EP3290539A4 (en) * | 2015-04-27 | 2018-09-19 | Nippon Steel & Sumitomo Metal Corporation | Non-oriented magnetic steel sheet |
US11572610B2 (en) * | 2017-01-25 | 2023-02-07 | Nippon Steel Corporation | Steel sheet |
JP2021139012A (ja) * | 2020-03-06 | 2021-09-16 | Jfeスチール株式会社 | プレス用鋼板の製造方法、プレス部品の製造方法、鋼板、伸びフランジ成形性の評価方法 |
JP7264090B2 (ja) | 2020-03-06 | 2023-04-25 | Jfeスチール株式会社 | プレス用鋼板の製造方法、プレス部品の製造方法、及び伸びフランジ成形性の評価方法 |
WO2023153096A1 (ja) * | 2022-02-09 | 2023-08-17 | 日本製鉄株式会社 | 冷延鋼板 |
WO2023153097A1 (ja) * | 2022-02-09 | 2023-08-17 | 日本製鉄株式会社 | 冷延鋼板およびその製造方法 |
Also Published As
Publication number | Publication date |
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MX2014001115A (es) | 2014-02-27 |
BR112014001589A2 (pt) | 2017-02-21 |
CA2843180A1 (en) | 2013-02-07 |
CA2843180C (en) | 2017-08-22 |
KR20140026625A (ko) | 2014-03-05 |
MX352397B (es) | 2017-11-23 |
US20140170440A1 (en) | 2014-06-19 |
CN103703156B (zh) | 2016-02-10 |
TW201309814A (zh) | 2013-03-01 |
EP2738275B1 (en) | 2020-05-27 |
JPWO2013018723A1 (ja) | 2015-03-05 |
CN103703156A (zh) | 2014-04-02 |
EP2738275A4 (en) | 2015-10-28 |
EP2738275A1 (en) | 2014-06-04 |
JP5310963B2 (ja) | 2013-10-09 |
KR101601566B1 (ko) | 2016-03-08 |
US9694561B2 (en) | 2017-07-04 |
RU2556253C1 (ru) | 2015-07-10 |
BR112014001589B1 (pt) | 2019-01-08 |
TWI494448B (zh) | 2015-08-01 |
ZA201401304B (en) | 2015-09-30 |
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