CN107923013A - High-strength steel sheet and its manufacture method - Google Patents
High-strength steel sheet and its manufacture method Download PDFInfo
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- CN107923013A CN107923013A CN201680047641.XA CN201680047641A CN107923013A CN 107923013 A CN107923013 A CN 107923013A CN 201680047641 A CN201680047641 A CN 201680047641A CN 107923013 A CN107923013 A CN 107923013A
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- carbide
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- steel sheet
- strength steel
- temperature
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 118
- 239000010959 steel Substances 0.000 title claims abstract description 118
- 238000000034 method Methods 0.000 title claims description 53
- 238000004519 manufacturing process Methods 0.000 title claims description 35
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 37
- 239000013078 crystal Substances 0.000 claims abstract description 33
- 239000002245 particle Substances 0.000 claims abstract description 33
- 238000001556 precipitation Methods 0.000 claims abstract description 22
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 17
- 229910001562 pearlite Inorganic materials 0.000 claims abstract description 12
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 9
- 229910001567 cementite Inorganic materials 0.000 claims abstract description 9
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 claims abstract description 9
- 238000005096 rolling process Methods 0.000 claims description 35
- 238000002791 soaking Methods 0.000 claims description 31
- 238000000137 annealing Methods 0.000 claims description 30
- 229910052719 titanium Inorganic materials 0.000 claims description 21
- 238000005098 hot rolling Methods 0.000 claims description 18
- 238000007747 plating Methods 0.000 claims description 17
- 229910052720 vanadium Inorganic materials 0.000 claims description 16
- 238000005097 cold rolling Methods 0.000 claims description 14
- 239000000203 mixture Substances 0.000 claims description 14
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical group [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 13
- 229910052725 zinc Inorganic materials 0.000 claims description 13
- 239000011701 zinc Substances 0.000 claims description 13
- 238000005275 alloying Methods 0.000 claims description 10
- 238000007598 dipping method Methods 0.000 claims description 8
- 238000005246 galvanizing Methods 0.000 claims description 7
- 239000012535 impurity Substances 0.000 claims description 6
- 229910052757 nitrogen Inorganic materials 0.000 claims description 6
- 229910052787 antimony Inorganic materials 0.000 claims description 5
- 229910052748 manganese Inorganic materials 0.000 claims description 4
- 238000012545 processing Methods 0.000 claims description 4
- 229910052802 copper Inorganic materials 0.000 claims description 3
- 229910052750 molybdenum Inorganic materials 0.000 claims description 3
- 229910052759 nickel Inorganic materials 0.000 claims description 3
- 229910052698 phosphorus Inorganic materials 0.000 claims description 3
- 230000002035 prolonged effect Effects 0.000 claims 2
- 230000000717 retained effect Effects 0.000 abstract description 6
- 238000001816 cooling Methods 0.000 description 24
- 229910052758 niobium Inorganic materials 0.000 description 20
- 238000012360 testing method Methods 0.000 description 15
- 238000010438 heat treatment Methods 0.000 description 14
- 238000001953 recrystallisation Methods 0.000 description 14
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 10
- 230000000694 effects Effects 0.000 description 10
- 150000001875 compounds Chemical class 0.000 description 9
- 210000001519 tissue Anatomy 0.000 description 6
- 239000011573 trace mineral Substances 0.000 description 6
- 235000013619 trace mineral Nutrition 0.000 description 6
- 229910052799 carbon Inorganic materials 0.000 description 5
- 238000005266 casting Methods 0.000 description 5
- 238000005516 engineering process Methods 0.000 description 5
- 238000010791 quenching Methods 0.000 description 5
- 230000000171 quenching effect Effects 0.000 description 5
- 239000010410 layer Substances 0.000 description 4
- 238000007792 addition Methods 0.000 description 3
- 230000014759 maintenance of location Effects 0.000 description 3
- 239000000243 solution Substances 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 230000006978 adaptation Effects 0.000 description 2
- 238000004458 analytical method Methods 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 239000010960 cold rolled steel Substances 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 238000004033 diameter control Methods 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 238000005554 pickling Methods 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- CKUAXEQHGKSLHN-UHFFFAOYSA-N [C].[N] Chemical compound [C].[N] CKUAXEQHGKSLHN-UHFFFAOYSA-N 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- LBDSXVIYZYSRII-IGMARMGPSA-N alpha-particle Chemical compound [4He+2] LBDSXVIYZYSRII-IGMARMGPSA-N 0.000 description 1
- 229910001563 bainite Inorganic materials 0.000 description 1
- 230000033228 biological regulation Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000009529 body temperature measurement Methods 0.000 description 1
- 238000003763 carbonization Methods 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 239000011247 coating layer Substances 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000010410 dusting Methods 0.000 description 1
- 210000000981 epithelium Anatomy 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000000879 optical micrograph Methods 0.000 description 1
- 238000007493 shaping process Methods 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 238000004381 surface treatment Methods 0.000 description 1
- 229910052718 tin Inorganic materials 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
- 230000000007 visual effect Effects 0.000 description 1
- 238000010792 warming Methods 0.000 description 1
Classifications
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
-
- 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
- C21D11/00—Process control or regulation for heat treatments
-
- 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
- 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
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- 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
- 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
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
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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
- 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
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
-
- 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
- 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
-
- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
- C21D9/54—Furnaces for treating strips or wire
- C21D9/56—Continuous furnaces for strip or wire
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
- C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
- C23C2/0224—Two or more thermal pretreatments
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
- C23C2/06—Zinc or cadmium or alloys based thereon
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/26—After-treatment
- C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- 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
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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
- C21D2211/005—Ferrite
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Crystallography & Structural Chemistry (AREA)
- Oil, Petroleum & Natural Gas (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
The present invention obtains the small high-strength steel sheet of anisotropy of high yield ratio and tensile properties.Above-mentioned high-strength steel sheet forms for specific component, and structure of steel is in terms of area occupation ratio by ferrite：More than 90%, pearlite and cementite is total:0~10%, martensite and retained austenite is total：0~2% is formed, above-mentioned ferritic average crystal particle diameter is less than 15.0 μm, average aspect ratio is less than 5.0, include Nb carbide, Ti carbide and/or V carbide, the Nb carbide and the average grain diameter of Ti carbide and/or V carbide are 5~50nm, and the total of the amount of precipitation of Nb carbide, Ti carbide and V carbide is calculated as 0.005~0.050% with volume fraction.
Description
Technical field
The present invention relates to the high-strength steel sheet and its manufacture method applied in automobile component etc..
Background technology
As the blanket of automobile component etc., the viewpoint such as the component lightweight brought from the thin-walled property based on blanket considers, excellent
Choosing uses high-strength steel sheet.For example, required in skeleton component, impact resistant component etc. in order to ensure the safety of passenger
It is unlikely to deform in collision, i.e. high yield ratio.On the other hand, in order to stably be suppressed in the case where not rupturing
Shaping, it is expected tensile properties in steel plate uniformly, i.e. the small high-strength steel sheet of the anisotropy of tensile properties.Wanted for such
Ask, disclose various steel plates and its manufacturing technology so far.
Patent Document 1 discloses Nb, Ti containing total more than 0.01 mass % and with recrystallization rate more than 80%
Ferrite for principal phase high-strength steel sheet and its manufacture method.
In addition, resistance to touch Patent Document 2 discloses non-recrystallization that structure of steel contains 20~50 area % is ferritic
Hit the high-strength steel sheet and its manufacture method of excellent.
Patent Document 3 discloses a kind of hot dipping plating high-strength steel sheet and its manufacture method, it is added with V, Ti, Nb
In it is one kind or two or more, principal phase for ferrite or bainite and by the amount of precipitation of the ferrous-carbide of grain boundaries be limited to necessarily with
It it is down and by the maximum particle diameter control of the ferrous-carbide 1 μm below.
Prior art literature
Patent document
Patent document 1：No. 4740099 publications of Japanese Patent No.
Patent document 2：No. 4995109 publications of Japanese Patent No.
Patent document 3：Japanese Unexamined Patent Publication 6-322479 publications
The content of the invention
However, in the technology of patent document 1, to after hot rolling~650 DEG C of holding temperature and continuous annealing furnace in it is equal
500~400 DEG C of the retention time in cooling after heat, it is not controlled, is unable to control Nb carbonizations important in the present invention
Thing and the average grain diameter of Ti carbide and/or V carbide, therefore, it is impossible to obtain each to different of high yield ratio and tensile properties
The small high-strength steel sheet of property.
In the technology of patent document 2, due to a large amount of addition Nb, Ti, more than 20% non-recrystallization is contained in terms of area occupation ratio
Ferrite not only deviates as structure of steel from the scope of required yield strength and tensile strength, but also non-recrystallization iron
Ferritic is unevenly disperseed in steel plate tissue, therefore in local easily surrender, can not obtain high yield ratio and tensile properties
The small high-strength steel sheet of anisotropy.
In the technology of patent document 3, to after hot rolling~650 DEG C of holding temperature and continuous annealing furnace in soaking after
500~400 DEG C of the retention time in cooling, be not controlled, be unable to control Nb carbide important in the present invention and
The average grain diameter of Ti carbide and/or V carbide, therefore, it is impossible to which the anisotropy for obtaining high yield ratio and tensile properties is small
High-strength steel sheet.
The present invention is given this situation to complete, its object is to obtain high yield ratio and tensile properties it is each to
The small high-strength steel sheet of the opposite sex.
The inventors of the present invention have made intensive studies in order to solve the above problems.Itself it turns out that, it is important that with iron element
Body turns to certain following in the structure of steel of main body, by ferritic average crystal particle diameter is fine, and average aspect ratio is made as one
Fixed following equiaxed structure, moreover, suitably controlling Nb carbide and the volume fraction and grain of Ti carbide and/or V carbide
Footpath.And it was found that in order to be adjusted to required tissue etc., defined component composition is adjusted to, and temperature will be batched after hot rolling
It is effective that the holdup time in set point of temperature region when degree, the heating annealed and soaking temperature, which are controlled in appropriate scope,.
The present invention is in view of finding and completing above, its purport is as described below.
[1] a kind of high-strength steel sheet, wherein, component composition contains C in terms of quality %：0.02% less than
0.10%th, Si：Less than 0.10%, Mn：Less than 1.0%, P：Less than 0.10%, S：Less than 0.020%, Al：0.01~0.10%,
N：Less than 0.010%, Nb：0.005~0.070%, Ti：Less than 0.100% (including 0%), V：Less than 0.100% (includes
0%) and Nb, Ti and V it is total：0.005~0.100%, remainder is made of Fe and inevitable impurity, steel group
Knit in terms of area occupation ratio by ferrite：More than 90%, pearlite and cementite is total:0~10%, martensite and retained austenite
It is total：0~3% is formed, and above-mentioned ferritic average crystal particle diameter is less than 15.0 μm, and average aspect ratio is less than 5.0, is contained
There are Nb carbide and Ti carbide and/or V carbide, the Nb carbide and the average grain of Ti carbide and/or V carbide
Footpath is 5~50nm, the amount of precipitation of Nb carbide, Ti carbide and V carbide it is total be calculated as 0.005 with volume fraction~
0.050%.
[2] high-strength steel sheet according to [1], wherein, mentioned component composition further contains Cr in terms of quality %：
Less than 0.3%, Mo：Less than 0.3%, B：Less than 0.005%, Cu：Less than 0.3%, Ni：Less than 0.3%, Sb：In less than 0.3%
Appoint it is one kind or two or more.
[3] high-strength steel sheet according to [1] or [2], wherein, there is zinc coat on surface.
[4] high-strength steel sheet according to [3], wherein, above-mentioned zinc coat is dip galvanized.
[5] high-strength steel sheet according to [4], wherein, above-mentioned dip galvanized is alloyed hot-dip zinc-coated layer.
[6] high-strength steel sheet according to [3], wherein, above-mentioned zinc coat is electro-galvanized layer.
[7] a kind of manufacture method of high-strength steel sheet, is the manufacture method of the high-strength steel sheet described in [1] or [2], has
Following process：Hot-rolled process, is 10 in the holdup time of the temperature province of final rolling temperature~650 DEG C after the hot rolling by steel hot rolling
Steel plate is cooled down under conditions of below second, is batched at 500~700 DEG C；Cold rolling process, by what is obtained in above-mentioned hot-rolled process
Hot rolled steel plate carries out cold rolling with less than 75% rolling rate；And annealing operation, cold prolong steel by what is obtained in above-mentioned cold rolling process
The holdup time of 650~750 DEG C of temperature province when plate is using continuous annealing furnace to heat up was detained as less than 60 seconds, at this
In soaking temperature after delay：760~880 DEG C, soaking time：Soaking is carried out under conditions of less than 120 seconds, at 400~500 DEG C
The holdup time of temperature province is to be cooled down under conditions of less than 100 seconds.
[8] according to the manufacture method of the high-strength steel sheet described in [7], it has prolongs steel plate by cold after above-mentioned annealing operation
Carry out the plating process of plating.
[9] manufacture method of the high-strength steel sheet according to [8], wherein, above-mentioned plating is galvanizing by dipping processing.
[10] according to the manufacture method of the high-strength steel sheet described in [9], it has prolongs steel by cold after above-mentioned plating process
Plate carries out the alloying step of Alloying Treatment.
[11] manufacture method of the high-strength steel sheet according to [8], wherein, above-mentioned plating is electrogalvanizing processing.
In the present invention, suitably control composition composition, the coiling condition after hot rolling, annealing heating when set point of temperature
The manufacturing condition such as the holdup time in region and soaking temperature.By the control, the structure of steel of the present invention as a purpose is obtained, its
As a result, it is possible to stably manufacture with the high yield ratio required by the purposes such as automobile component and the anisotropy of tensile properties it is small
High-strength steel sheet.Using the high-strength steel sheet of the present invention, the further lightweight of automobile can be carried out, the present invention automobile,
Utility value in steel industry is very big.
Embodiment
Hereinafter, embodiments of the present invention are illustrated.It should illustrate that the present invention is not limited to implementation below.
First, the summary of the high-strength steel sheet of the present invention is illustrated.
The high-strength steel sheet of the present invention is with tensile strengths of the 330MPa less than 500MPa, more than 0.70 surrender
Than, yield strength in the tension test that the draw direction direction parallel with rolling direction carries out with draw direction and rolling
The difference of yield strength in the tension test that the vertical direction in direction carries out is below 30MPa.Since yield ratio is more than 0.70,
Therefore the high-strength steel sheet of the present invention has high yield ratio.Further, since the difference of above-mentioned yield strength is below 30MPa, because
The anisotropy of the tensile properties of this high-strength steel sheet of the invention is small.
It is especially important to be formed into containing Nb in the present invention：0.005%~0.070%, Ti：Less than 0.100% (includes
0%), V：Less than 0.100% (including 0%) and Nb, Ti and V add up to less than 0.005%~0.100% component composition.
By adjusting component composition, manufacturing condition, so as to be adjusted to：With the structure such as required ferrite and arbitrary pearlite
Into structure of steel, which is less than 15.0 μm, and average aspect ratio is less than 5.0, contains Nb carbide
And Ti carbide and/or V carbide, the Nb carbide and the average grain diameter of Ti carbide and/or V carbide for 5~
The total of the amount of precipitation of 50nm, Nb carbide, Ti carbide and V carbide is calculated as 0.005~0.050% with volume fraction, thus,
It can obtain the small high-strength steel sheet of the anisotropy of high yield ratio and tensile properties.
In the present invention, Nb carbide, Ti carbide and V carbide further include Nb carbonitrides, Ti carbonitrides, V carbon nitrogen
The compound and compound carbonitride of Nb, Ti, the compound carbonitride of Nb, V and compound carbonitride of Nb, Ti, V.It should illustrate that on
The compound carbonitride of Nb, Ti, it considers average grain diameter, total volume fraction as the carbide of Nb or the carbide of Ti.Close
In the compound carbonitride of Nb, V and the compound carbonitride of Nb, Ti, V similarly.
As described above, in order to make ferritic average crystal particle diameter, average aspect ratio and carbide (Nb carbide and
Ti carbide and/or V carbide) average grain diameter and amount of precipitation meet needed for condition, not only component composition it is important, manufacture bar
Part is also important.Specifically, the holdup time of the temperature province of final rolling temperature~650 DEG C is set in cooling after hot rolling
Less than 10 seconds, coiling temperature is set to 500~700 DEG C.In addition, by 650~750 DEG C of temperature province in the heating of annealing
Holdup time is set to less than 60 seconds, next, under 760~880 DEG C of soaking temperature below soaking 120 seconds.After batching
Separate out with making Nb carbide, Ti carbide and/or V carbide fine uniform structures in cooling, after cold rolling, ferrite is existed in annealing
Compared with being recrystallized under low temperature, and will be controlled in the holdup time in recrystallization temperature region it is following in regulation, so as to obtain the present invention's
Target structure of steel.
Yield strength and tensile strength are that JIS5 tension tests are extracted in a manner of draw direction is vertical with rolling direction
Piece, is obtained by the tension test according to JIS Z 2241.The anisotropy of tensile properties is from draw direction and rolling direction
JIS5 tension test sheets are extracted in vertical perpendicular and parallel direction respectively, the tension test according to JIS Z 2241 are carried out, by surrendering
The difference of intensity is obtained.
It is required by the blanket of high-strength steel sheet of the invention with automobile component etc. for finding and completing based on more than, high
Yield ratio and the small feature of the anisotropy of tensile properties.
Then, the restriction of the restriction reason, the restriction reason of structure of steel and the manufacturing condition that are formed to the component of the present invention is managed
By illustrating.
(1) component forms
The high-strength steel sheet of the present invention contains C in terms of quality %：0.02% less than 0.10%, Si：It is less than
0.10%th, Mn：Less than 1.0%, P：Less than 0.10%, S：Less than 0.020%, Al：0.01~0.10%, N：Less than 0.010%,
Nb：0.005~0.070%, Ti：Less than 0.100% (including 0%) and V：Less than 0.100% (include 0%) and total
Less than 0.005~0.100% Nb, Ti and V.
In addition, the high-strength steel sheet of the present invention can also further contain Cr in terms of quality %：Less than 0.3%, Mo：
Less than 0.3%, B：Less than 0.005%, Cu：Less than 0.3%, Ni：Less than 0.3%, Sb：Wantonly a kind or 2 kinds in less than 0.3%
Any condition is used as above.
Remainder other than the above is Fe and inevitable impurity.
" % " expression " quality % " in the explanation of following component composition.
C：0.02% less than 0.10%
C becomes Nb carbide, Ti carbide, V carbide or makes pearlite, martensite increase, is strong to surrendering therefore
The effective element of increase of degree and tensile strength.When C content is less than 0.02%, total amount of precipitation of carbide does not become desired
Scope, therefore, cannot get the target tensile strength of the present invention.If C content is more than 0.10%, pearlite is exceedingly generated
Or martensite, therefore, yield ratio reduces, the anisotropy increase of tensile properties.Therefore, C content for 0.02% less than
0.10%.Preferably 0.02~0.06%.
Si：Less than 0.10%
Si is generally by ferritic solution strengthening and effective for increase yield strength and tensile strength.But if
Si is added, then significantly improving due to work hardening capacity, compared with yield strength, the incrementss bigger of tensile strength, yield ratio
Reduce, surface texture is deteriorated.Therefore, Si contents are less than 0.10%.It should illustrate that the lower limit of Si contents is not particularly limited,
But the composition beyond Si can also improve yield strength, tensile strength, therefore, in the present invention, Si contents are more few the more preferred.Cause
This, in the present invention, can not also add Si, but sometimes inevitably containing 0.005% Si in manufacture.
Mn：Less than 1.0%
Mn is by ferritic solution strengthening and effective for increase yield strength and tensile strength.But if Mn contains
Amount becomes more than 1.0%, then the martensite point rate in structure of steel increases, and therefore, tensile strength excessively increases, cannot the present invention
Target tensile strength, yield ratio reduce.Therefore, Mn contents are less than 1.0%.Mn can not also be added, but during addition Mn, as
The preferable Mn contents of lower limit are more than 0.2%.It is less than 0.8% as the preferable Mn contents of the upper limit.
P：Less than 0.10%
P is by ferritic solution strengthening and effective to increase yield strength and tensile strength.Therefore, in the present invention,
P can suitably be contained.But if P content more than 0.10%, due to casting aliquation, ferrite grain boundaries segregation and partly
The ferritic surrender of generation, therefore the anisotropy increase of tensile properties.Therefore, P content is less than 0.10%.It can not also add
It is more than 0.01% as the preferable P content of lower limit when adding P, but adding P.As the preferable P content of the upper limit for 0.04% with
Under.
S：Less than 0.020%
S is the element inevitably contained as impurity.Due to the field trashes such as MnS formation and bendability, part
The mouldabilities such as extensibility reduce, it is therefore preferable that reducing S contents as far as possible.In the present invention, S contents are less than 0.020%.It is preferred that
For less than 0.015%.It should illustrate that as described above, S contents are more low the more preferred, in the present invention, S can not also be added.But
It is the S in manufacture sometimes with 0.0003%.
Al：0.01~0.10%
Al is added for the deoxidation in refining procedure and in order to which solid solution N is fixed in the form of AlN.In order to obtain
Sufficient effect is, it is necessary to make Al content be more than 0.01%.In addition, if Al content is more than 0.10%, then AlN largely separate out and
Ferritic average aspect ratio increase, causes the anisotropic increase of tensile properties.Therefore, Al content for 0.01~
0.10%.Preferably 0.01~0.07%.In addition, more preferably 0.01~0.06%.
N：Less than 0.010%
N is the inevitably mixed element untill the refining procedure of molten iron.If N content more than 0.010%,
During casting after Nb carbide, Ti carbide, V Carbide Precipitations, when heating slab, Nb carbide, Ti carbide, V carbide
Do not melt and remained in the form of thick carbide, therefore, cause the coarsening of ferrite average crystallite grain.Therefore, N content
For less than 0.010%.It should illustrate that in the present invention, N can not also be added, but sometimes with 0.0005% in manufacture
N。
Nb：0.005~0.070%
Nb contribute to the miniaturization of ferrite average crystal grain, yield ratio caused by the precipitation of Nb carbide it is increased
Important element.When Nb contents are less than 0.005%, the amount of precipitation of carbide is insufficient etc. sometimes, so that this hair can not be obtained
Bright effect.In addition, if Nb contents are more than 0.070%, then Nb carbide excessively separates out and remains also to lack after annealing and prolong
The non-recrystallization ferrite of malleability, or ferritic average aspect ratio is more than 5.0, therefore the anisotropy of tensile properties increases
Greatly.Therefore, Nb contents are 0.005~0.070%.Preferably 0.005~0.040%.
Ti：Less than 0.100% (including 0%)
V：Less than 0.100% (including 0%)
Nb, Ti and V add up to 0.005~0.100%
For Ti and V by being used as Ti carbide and/or V Carbide Precipitations with the compound additions of Nb, contributing to will be ferritic
Average aspect ratio is controlled below 5.0.When Nb, Ti and V total is less than 0.005%, Nb carbide and Ti carbide and/or
The volume fraction of V carbide becomes inadequate, as a result, the amount of precipitation of carbide does not become required scope, can not obtain this hair
Bright effect.In addition, Nb, Ti and V it is total more than 0.100% when, Ti carbide and/or V carbide excessively separate out and residual
Stay the non-recrystallization ferrite for also lacking ductility after annealing, the anisotropy increase of tensile properties.Therefore, Ti and V are set to Ti：
Less than 0.100% (including 0%) and V：Less than 0.100% (include 0%) and Nb, Ti and V add up to 0.005~0.100%.It is excellent
It is 0.007~0.040% to select total amount.
The high-strength steel sheet of the present invention can contain following component as any condition.
Cr：Less than 0.3%
Trace element as the action effect for not damaging the present invention can contain Cr.If Cr contents more than 0.3%,
Sometimes due to the raising of quenching degree and excessively generate martensite, cause the reduction of yield ratio.Therefore, when adding Cr, Cr contents
For less than 0.3%.
Mo：Less than 0.3%
Trace element as the action effect for not damaging the present invention can contain Mo.However, if Mo contents exceed
0.3%, then sometimes due to the raising of quenching degree and excessively generate martensite, cause the reduction of yield ratio.Therefore, Mo is added
When, Mo contents are less than 0.3%.
B：Less than 0.005%
Trace element as the action effect for not damaging the present invention can contain B.However, if B content exceedes
0.005%, then sometimes due to the raising of quenching degree and excessively generate martensite, cause the reduction of yield ratio.Therefore, B is added
When, B content is less than 0.005%.
Cu：Less than 0.3%
Trace element as the action effect for not damaging the present invention can contain Cu.However, if Cu contents exceed
0.3%, then sometimes due to the raising of quenching degree and excessively generate martensite, cause the reduction of yield ratio.Therefore, Cu is added
When, Cu contents are less than 0.3%.
Ni：Less than 0.3%
Trace element as the action effect for not damaging the present invention can contain Ni.However, if Ni contents exceed
0.3%, then sometimes due to the raising of quenching degree and excessively generate martensite, cause the reduction of yield ratio.Therefore, Ni is added
When, Ni contents are less than 0.3%.
Sb：Less than 0.3%
Trace element as the action effect for not damaging the present invention can contain Sb.However, if Sb contents exceed
0.3%, then cause the embrittlement of high-strength steel sheet.Therefore, when adding Sb, Sb contents are less than 0.3%.
Remainder other than the above is Fe and inevitable impurity.In addition, in the present invention, than that described above,
The conduct of the element such as Sn, Co, W, Ca, Na, Mg, which can be contained, in the micro scope of action effect for not damaging the present invention to keep away
The impurity exempted from." micro scope " is to instigate these elements to add up to less than 0.01%.
(2) structure of steel
The structure of steel of the high-strength steel sheet of the present invention is in terms of area occupation ratio by ferrite：More than 90%, pearlite and cementite
It is total:0~10%, martensite and retained austenite is total：0~3% is formed.In addition, in the structure of steel, above-mentioned iron element
The average crystal particle diameter of body is less than 15.0 μm, Nb carbide and the average grain diameter of Ti carbide and/or V carbide be 5~
50nm, Nb carbide and the amount of precipitation of Ti carbide and/or V carbide it is total be calculated as 0.005 with volume fraction~
0.050%.
Ferrite：More than 90%
Ferrite has good ductility, contains in structure of steel as principal phase, its content is calculated as 90% with area occupation ratio
More than.When ferritic content is less than 90% in terms of area occupation ratio, it cannot get high yield ratio of the present invention as target, in addition, drawing
The anisotropy for stretching characteristic also becomes larger.Therefore, ferritic content is calculated as more than 90% with area occupation ratio.Preferably more than 95%.
It should illustrate that the structure of steel of high-strength steel sheet of the invention can be that single-phase (ferritic content is calculated as ferrite with area occupation ratio
100%).
Pearlite and cementite it is total：0~10%
Pearlite and cementite are effective for obtaining required yield strength and tensile strength.But if pearlite and
Cementite it is total in terms of area occupation ratio more than 10%, then cannot high yield ratio of the present invention as target, tensile properties it is each
Anisotropy also becomes larger.Therefore, pearlite and the total of cementite are calculated as 0~10% with area occupation ratio.Preferably 0~5%.
Martensite and retained austenite it is total：0~3%
Structure of steel can contain the martensite and retained austenite for adding up to 0~3% in terms of area occupation ratio.If martensite and residual
Adding up to more than 3% for remaining austenite, then cannot get more than 0.70 yield ratio.Therefore, martensite and retained austenite is total
For 0~3%.
Ferritic average crystal particle diameter is less than 15.0 μm
By ferritic average crystal particle diameter be adjusted to required scope for obtain the present invention as a purpose 0.70 with
On high yield ratio be important.If ferritic average crystal particle diameter more than 15.0 μm, cannot get more than 0.70 bend
Take ratio.Therefore, ferritic average crystal particle diameter is less than 15.0 μm.Preferably less than 10.0 μm.In addition, the average crystalline substance of ferrite
The lower limit of body particle diameter is not particularly limited, and during less than 1.0 μm, tensile strength, yield strength excessively increase sometimes, cause to bend
Property, extensibility be deteriorated, therefore, ferrite average crystal particle diameter is preferably more than 1.0 μm.
Ferritic average aspect ratio is less than 5.0
If ferritic average aspect ratio is more than 5.0, the increase of non-recrystallization ferrite, the anisotropy of tensile properties
Increase.In the present invention, ferritic average aspect ratio is preferably less than 4.5, and more preferably less than 4.2.
Nb carbide and the average grain diameter of Ti carbide and/or V carbide are 5~50nm
Nb carbide, Ti carbide, V carbide are mainly separated out in ferrite intragranular, its average grain diameter is to as the present invention
The high yield that has concurrently of target than the isotropism with tensile properties be important.When above-mentioned particle diameter is less than 5nm, not only surrender
Intensity and tensile strength excessively increase, and the anisotropy of tensile properties also increases.If above-mentioned particle diameter is bent more than 50nm
The increase for taking intensity becomes inadequate, and can not obtain the high yield ratio of the target as the present invention.Therefore, Nb carbide and Ti
The particle diameter of carbide and/or V carbide is 5~50nm.It is more than 10nm as the preferred average grain diameter of lower limit.It is preferred as the upper limit
Average grain diameter is below 40nm.In addition, in the present invention, measure with not differentiating between Nb carbide, Ti carbide, V carbide average
Particle diameter.
Nb carbide and the total of the amount of precipitation of Ti carbide and V carbide are calculated as 0.005~0.050% with volume fraction
Nb carbide and the amount of precipitation of Ti carbide and V carbide are adjusted to required scope to as the present invention's
The high yield that has concurrently of target than the isotropism with tensile properties is important.If Nb carbide and Ti carbide and V carbon
The total of the amount of precipitation of compound is less than 0.005% in terms of volume fraction, then the increase of yield strength becomes inadequate, and can not obtain this
The target high yield ratio of invention.If Nb carbide and the amount of precipitation of Ti carbide and V carbide is total in terms of volume fraction
More than 0.050%, then ferritic recrystallization is suppressed significantly and yield strength and tensile strength excessively increase, and then, stretching
The anisotropy increase of characteristic.Therefore, Nb carbide and the amount of precipitation of Ti carbide and V carbide is total in terms of volume fraction
For 0.005~0.050%.It is more than 0.010% as the preferably total volume fraction of lower limit.It is as the preferably total volume fraction of the upper limit
Less than 0.040%.In addition, when without Ti carbide, Ti carbide is 0, and when without V carbide, V carbide is 0.
It should illustrate that the area occupation ratio on each tissue, using SEM to from the steel perpendicular to the section in rolling width direction
The scope that the thickness of slab 1/8~3/8 centered on 1/4 position of thickness of slab direction is played in plate surface side is observed, and passes through ASTM E
Point counting method described in 562-05 is obtained.Ferritic average crystal particle diameter is obtained by operating as follows：Using SEM to
The scope of thickness of slab 1/8~3/8 centered on above-mentioned 1/4 position of thickness of slab is observed, and is figured out by viewing area and crystal grain
Imitate circular diameter.For ferritic average aspect ratio, light microscope can be used on the section vertical with rolling width direction
Observation is 1/4 position in thickness of slab direction from surface of steel plate, by obtaining each crystal grain described in the table 1 of JIS G 0551
The method of average line segment length calculates rolling direction and the average crystal grain length in thickness of slab direction, by (the average crystal grain of rolling direction
Length)/(the average crystal grain length in thickness of slab direction) obtain.Nb carbide, Ti carbide, the particle diameter of V carbide are by will be high-strength
Spend steel plate and make film sample, calculated equivalent diameter (being calculated by viewing area and population) by tem observation image and obtained.
Total volume fraction of Nb carbide, Ti carbide and V carbide is obtained by extracting residua analysis.
(3) manufacturing condition
The high-strength steel sheet of the present invention by operating manufacture as follows：The steel melting that will be formed with mentioned component, passes through casting
After making manufacture slab (steel disc), hot rolling, cold rolling are carried out, then, is annealed in continuous annealing furnace.It can carry out after hot rolling
Pickling.Hereinafter, the manufacturing method of the present invention with hot-rolled process, cold rolling process, annealing operation is illustrated.It should say
Bright, in the following description, temperature refers to surface temperature.
Casting method is not particularly limited, if do not occur the segregation of significant component composition, tissue it is uneven, then may be used
To be cast by any one of ingot casting method, continuous casting process.
Hot rolling can directly be rolled the block of high temperature, and the slab that can also will be cooled to room temperature add again
Heat is rolled.In addition, in the case of there is the surface defects such as splitting on the time point of slab, grinder etc. can be utilized real
Apply slab repairing.When being reheated to slab, in order to melt Nb carbide and Ti carbide and/or V carbide, preferably
It is heated to more than 1100 DEG C.
Hot-rolled process is by steel hot rolling, is 10 in the holdup time of the temperature province of final rolling temperature~650 DEG C after the hot rolling
Steel plate is cooled down under conditions of below second, in the process that 500~700 DEG C are batched.
In hot rolling, roughing, finish rolling are implemented to slab.Then, the coiler plate after hot rolling is formed into coils of hot rolled.Heat
Roughing condition and finish rolling condition in rolling are not particularly limited, as long as being determined according to conventional method.If final rolling temperature is small
In Ar3 points, then the thick ferrite that generation is extended in rolling direction in the structure of steel of hot rolled steel plate sometimes, leads after annealing
Cause the reduction of ductility.Therefore, final rolling temperature is preferably more than Ar3 points.It should illustrate that Ar3 points are obtained by operating as follows：Make
With transformation temperature measurement device (such as FORMASTER testing machines) from austenite one phase temperature province with 1 DEG C/s continuous coo1ings when
The temperature that measure ferrite transformation starts.
The holdup time of the temperature province of final rolling temperature~650 DEG C：Less than 10 seconds
In cooling after hot rolling, the holdup time of the temperature province by suitably controlling final rolling temperature~650 DEG C, energy
Enough suppress the coarsening of ferritic average crystal particle diameter.Therefore, above-mentioned cooling condition is important in the present invention.If in finish rolling
In cooling afterwards the holdup time of the temperature province of final rolling temperature~650 DEG C more than 10 seconds, then after the batching of hot rolling exceedingly
Thick Nb carbide, Ti carbide, V carbide are separated out, therefore, ferrite crystal grain easily becomes thick in annealing, iron element
The average crystal particle diameter of body is more than 15.0 μm, and therefore, yield ratio reduces.Therefore, final rolling temperature~650 DEG C in above-mentioned cooling
The holdup time of temperature province is less than 10 seconds.It should illustrate that the lower limit of above-mentioned holdup time is not particularly limited, from annealing
When equably make Nb carbide, Ti carbide, V Carbide Precipitations and make ferrite crystal particle diameter become uniformly from the viewpoint of,
It is preferred that it is detained more than 1 second.In addition, becoming for the average grain diameter for suppressing Nb carbide etc. outside the scope of the invention or Nb carbide etc.
Amount of precipitation total the reasons why becoming outside the scope of the invention, the lower limit for limiting the temperature province of above-mentioned holdup time is 650 DEG C.
Coiling temperature：500~700 DEG C
Coiling temperature is for by adjusting Nb carbide, Ti carbide, the amount of precipitation of V carbide and their average grain
Footpath and by after annealing ferrite average crystal particle diameter control for less than 15.0 μm be important.In the width of steel plate
Centre, coiling temperature be less than 500 DEG C when, above-mentioned carbide will not be fully separated out in the cooling after batching, annealing heating and
Thick carbide is separated out during soaking, ferrite crystal particle diameter coarsening, therefore, cannot get high yield ratio, and then, tensile strength
Also diminish.If coiling temperature more than 700 DEG C, separates out thick Nb carbide, Ti carbide, V in the cooling after batching
Carbide, the ferrite crystal particle diameter coarsening in annealing, therefore, cannot get high yield ratio, and then, tensile strength also diminishes.
Therefore, coiling temperature is 500~700 DEG C.It it is more than 550 DEG C as the preferable coiling temperature of lower limit.Preferably rolled up as the upper limit
It is less than 650 DEG C to take temperature.
Cold rolling process is the process for the hot rolled steel plate cold rolling that will be obtained in above-mentioned hot-rolled process.The rolling rate of cold rolling is 75%
Below.Preferably 30~75%.If rolling rate, more than 75%, the average particle diameter became of carbide is thick, this can not be obtained
The high YR of target of application, it is therefore desirable to be less than 75%.If rolling rate is more than 30%, make ferrite fully when annealing
Recrystallization, obtains isotropic tensile properties, therefore preferably.
Annealing is formed by being warming up to the process cooled down after soaking temperature using continuous annealing furnace.Annealing in the present invention
Process is following process：By 650~750 DEG C of the cold-rolled steel sheet obtained in cold rolling process in continuous annealing furnace in heating
Temperature province is detained using the holdup time as more than 60 seconds, in soaking temperature after the delay：760~880 DEG C, soaking when
Between；Soaking is carried out under conditions of less than 120 seconds, the holdup time of 400~500 DEG C of temperature province is 100 seconds after the soaking
Cooled down under conditions of below.
In the holdup time of 650~750 DEG C of temperature province during heating：Less than 60 seconds
The holdup time in 650~750 DEG C during heating is to controlling the ferritic average aspect ratio after annealing 5.0
It is important manufacturing condition below.If the holdup time in 650~750 DEG C during heating, ferrite rolled more than 60 seconds
The easy grain growth in direction processed, therefore ferritic average aspect ratio is more than 5.0.Therefore, in 650~750 DEG C during heating
Holdup time is less than 60 seconds.The holdup time in 650~750 DEG C during heating is preferably set to less than 50 seconds.In addition, when being detained
Between lower limit be not particularly limited, if the holdup time is too short, ferritic recrystallization can not be carried out fully, thus be detained when
Between be preferably more than 5 seconds.
Soaking temperature：760~880 DEG C, soaking time：Less than 120 seconds
Soaking temperature and soaking time are important conditions in terms of ferrite average crystal particle diameter is controlled.Soaking temperature
During less than 760 DEG C, ferritic recrystallization becomes inadequate, the anisotropy increase of tensile properties.If soaking temperature exceedes
880 DEG C, then ferrite average crystal particle diameter coarsening and cannot be as the yield ratio of the target of the present invention, tensile strength also become
It is small.Therefore, soaking temperature is 760~880 DEG C.In addition, if soaking time is more than 120 seconds, then ferrite average crystal particle diameter
Coarsening, therefore, cannot be as the tensile strength and high yield ratio of the target of the present invention.Therefore, soaking time for 120 seconds with
Under.Preferably less than 60 seconds.It should illustrate that the lower limit of soaking time is not particularly limited, from each to different of reduction tensile properties
From the viewpoint of property, ferrite is preferably set fully to recrystallize, therefore soaking time is preferably more than 30 seconds.
Mode of heating when heating and soaking is not particularly limited, and can utilize radiant tube mode, straight fiery mode of heating etc.
Carry out.
The cooling condition in cooling after soaking be 400~500 DEG C of temperature province holdup time be less than 100 seconds.
Holdup time is 100 seconds below for making the average grain diameter of carbide be that below 50nm is necessary.It should illustrate that the holdup time
Lower limit be not particularly limited, if extremely short, solid solution C in ferrite increase and resistance to aging characteristic is deteriorated, or need
Excessive investment to cooling device, it is therefore preferable that more than 5 seconds.More preferably more than 10 seconds.Here, " 400~500 DEG C of temperature
The holdup time in degree region " refers to the total of the time for the temperature that the steel plate in cooling is 400~500 DEG C, if cooling stopping
Temperature is more than 400 DEG C, then refers to total as 500 DEG C of time from cooling stops temperature.In addition, in the temperature province
Delay equivalent to Wetted constructures.It should illustrate that other cooling conditions are not particularly limited, cooling can be enumerated and stop temperature
For 400~500 DEG C, the condition of 30 DEG C/below s of average cooling rate.
It can implement plating to the surface of the high-strength steel sheet as above obtained.Plating is preferably zinc-plated, by the present invention's
High-strength steel sheet implementation is zinc-plated, and zinc coat is formed on high-strength steel sheet.Cover in zinc (electrogalvanizing, galvanizing by dipping etc.), it is also preferred that
The galvanizing by dipping impregnated in galvanizing by dipping bath.
Dip galvanized is formed by carrying out galvanizing by dipping to high-strength steel sheet, alloying is implemented to the dip galvanized
Handle and form alloyed hot-dip zinc-coated layer.In the case where implementing Alloying Treatment, when keeping temperature less than 450 DEG C, sometimes
Alloying will not be sufficiently carried out, and plating adaptation, corrosion resistance are deteriorated.In addition, if temperature is kept then to have more than 560 DEG C
When alloying exceedingly carry out and compacting when produce dusting the problems such as.Therefore, it is preferably 450~560 DEG C to keep temperature.Separately
Outside, when the retention time is less than 5 seconds, alloying will not be carried out fully sometimes and plating adaptation, corrosion resistance are deteriorated, and therefore, be protected
It is preferably more than 5 seconds to hold the time.
Thereafter, the skin-pass that elongation is 0.1~5.0% can be implemented as needed.
By above method, the high-strength steel sheet of the target as the present invention is obtained.Even if to the high strength steel of the present invention
Plate implements surface treatment and the applications such as chemical conversion treatment, the processing of organic system epithelium, will not damage the mesh as the present invention
Target characteristic.
Embodiment
Hereinafter, the present invention is explained by embodiment.
After when by the plate slab of the steel A~M formed with the component shown in table 1, soaking 1 is small at 1250 DEG C, in till soleplate
After being suppressed under conditions of 900 DEG C more than thick 3.2mm, Ar3 point of final rolling temperature, cool down under the conditions shown in Table 2, with the institute of table 2
The coiling temperature shown batches.After the hot rolled steel plate pickling of manufacture, implement the cold rolling of final thickness of slab 1.4mm and cold-rolled steel is made
Plate, the annealing of the condition shown in implementation table 2 and manufacture the high-strength steel sheet of No.1~31.It should illustrate that cooling in annealing
Cooling condition be cooling stop temperature be 480 DEG C, average cooling rate is 20 DEG C/below s, the temperature province at 400~500 DEG C
The holdup time of (500 DEG C~cooling stops the temperature province of temperature) is 30 seconds.When unreal plating is covered, annealing using CAL into
OK.In addition, when implementing plating, implement galvanizing by dipping or alloyed hot-dip zinc-coated using CGL.Coating layer is set to be plated for alloyed hot-dip
During zinc layers, implement to keep the Alloying Treatment of 10 seconds at 510 DEG C.
Structure of steel observation and tension test are carried out to obtained high-strength steel sheet.
On the area occupation ratio of structure of steel, the area occupation ratio respectively organized is using SEM to from perpendicular to compacting width
The scope that the thickness of slab 1/8~3/8 centered on 1/4 position of thickness of slab direction is played in the surface of steel plate side in section is observed and passed through
Point counting method described in ASTM E 562-05 is obtained.Ferritic average crystal particle diameter is obtained in the following way：Utilize
SEM observes the scope of the thickness of slab 1/8~3/8 centered on above-mentioned 1/4 position of thickness of slab, by viewing area and crystallization grain number
Calculate equivalent diameter.For ferritic average aspect ratio, optical microphotograph is used on the section vertical with rolling width direction
Sem observation is 1/4 position in thickness of slab direction from surface of steel plate, by obtaining each crystal grain described in the table 1 of JIS G 0551
The method of average line segment length calculate rolling direction and the average crystal grain length in thickness of slab direction, by (the average crystalline substance of rolling direction
Grain length)/(the average crystal grain length in thickness of slab direction) obtain.Carbide (Nb carbide, Ti carbide, V carbide) is averaged
Particle diameter is obtained in the following way：Tem observation is carried out, equivalent diameter is obtained by image procossing.Nb carbide, Ti carbide
Obtained with total volume fraction of V carbide by extracting residua analysis.Observation carries out in each 10 visuals field, and it is average to calculate it.
It should illustrate that the results are shown in table 2 (by table 2-1 and table 2-2 included together as table 2), the α of table 2 refers to ferrite, and P refers to
Pearlite, M refer to martensite, and θ refers to cementite, and α particle diameters refer to ferrite average crystal particle diameter, and M (C, N) particle diameter refers to be carbonized
The average grain diameter of thing, M (C, N) volume fraction refer to the total of the amount of precipitation of Nb carbide, Ti carbide and V carbide.On in addition,
The M stated in M (C, N) refers to Nb, Ti or V.
On tensile strength (TS) and yield ratio (YR), use what is extracted in a manner of draw direction is vertical with rolling direction
JIS5 tension test sheets, the tension test according to JIS Z 2241 are obtained.The anisotropy of tensile properties is to use draw direction
Yield strength in the tension test that the direction parallel with rolling direction the carries out direction vertical with rolling direction with draw direction
The difference of yield strength in the tension test of progress is evaluated, and difference is set to "○" for the test film of below 30MPa, will be exceeded
The test film of 30MPa is set to "×".In addition, by tensile strengths of the 330MPa less than 500MPa, more than 0.70 surrender
It is better than being evaluated as.
[table 2-1]
(note 1) underscore is represented outside the scope of the invention, and bad characteristic is good.
(note 2) ※ is represented due to remaining non-recrystallization tissue, so can not measure.
[table 2-2]
(note 1) underscore is represented outside the scope of the invention, and bad characteristic is good.
(note 2) ※ is represented due to remaining non-recrystallization tissue, so can not measure.
The observation result of structure of steel, stretch test result are shown in table 2.No.1~3,6,8,9,12~16,18,19,22,
24th, in 25,28, meet the full terms of the present invention, therefore the high yield ratio as the target of the present invention and stretching spy can be obtained
The small high-strength steel sheet of the anisotropy of property.On the other hand, No.4,5,7,10,11,17,20,21,23,26,27,29,30,31
In, component composition or manufacturing condition can not obtain being used as this outside the scope of the present invention, not obtain required structure of steel
The high-strength steel sheet of the target of invention.
Industrial applicability
The high-strength steel sheet of the present invention is suitable for requirement high yield ratio and tensile properties centered on car inner plate component etc.
Isotropic field.
Claims (11)
1. a kind of high-strength steel sheet, wherein, component composition contains C in terms of quality %：0.02% less than 0.10%, Si：
Less than 0.10%, Mn：Less than 1.0%, P：Less than 0.10%, S：Less than 0.020%, Al：0.01~0.10%, N：0.010%
Below, Nb：0.005~0.070%, Ti：Less than 0.100% and include 0%, V：Less than 0.100% and include 0%, Yi Jihe
Nb, Ti and V of meter 0.005~0.100%, remainder are made of Fe and inevitable impurity,
Structure of steel is in terms of area occupation ratio by ferrite：More than 90%, pearlite and cementite is total:0~10%, martensite and residual
Remaining austenite adds up to：0~3% is formed,
The ferritic average crystal particle diameter is less than 15.0 μm, and average aspect ratio is less than 5.0,
The high-strength steel sheet contains Nb carbide and Ti carbide and/or V carbide, the Nb carbide and Ti carbide
And/or the average grain diameter of V carbide is 5~50nm,
The total of the amount of precipitation of Nb carbide, Ti carbide and V carbide is calculated as 0.005~0.050% with volume fraction.
2. high-strength steel sheet according to claim 1, wherein, the component composition further contains Cr in terms of quality %：
Less than 0.3%, Mo：Less than 0.3%, B：Less than 0.005%, Cu：Less than 0.3%, Ni：Less than 0.3%, Sb：In less than 0.3%
Appoint it is one kind or two or more.
3. high-strength steel sheet according to claim 1 or 2, wherein, there is zinc coat on surface.
4. high-strength steel sheet according to claim 3, wherein, the zinc coat is dip galvanized.
5. high-strength steel sheet according to claim 4, wherein, the dip galvanized is alloyed hot-dip zinc-coated layer.
6. high-strength steel sheet according to claim 3, wherein, the zinc coat is electro-galvanized layer.
7. a kind of manufacture method of high-strength steel sheet, is the manufacture method of the high-strength steel sheet described in claim 1 or 2, has
Following process：
Hot-rolled process, by steel hot rolling, after the hot rolling, the temperature province of final rolling temperature~650 DEG C holdup time for 10 seconds with
Steel plate is cooled down under conditions of lower, is batched at 500~700 DEG C；
Cold rolling process, cold rolling is carried out by the hot rolled steel plate obtained in the hot-rolled process with less than 75% rolling rate；And
Annealing operation, cold prolongs steel plate 650~750 DEG C when continuous annealing furnace is to heat up by what is obtained in the cold rolling process
The holdup time of temperature province was detained for less than 60 seconds, in soaking temperature after the delay：760~880 DEG C, soaking when
Between：Soaking is carried out under conditions of less than 120 seconds, the bar for being less than 100 seconds in the holdup time of 400~500 DEG C of temperature provinces
Cooled down under part.
8. the manufacture method of high-strength steel sheet according to claim 7, have and cold after the annealing operation is prolonged into steel plate
Carry out the plating process of plating.
9. the manufacture method of high-strength steel sheet according to claim 8, wherein, the plating is at galvanizing by dipping
Reason.
10. the manufacture method of high-strength steel sheet according to claim 9, have and cold after the plating process is prolonged into steel plate
Carry out the alloying step of Alloying Treatment.
11. the manufacture method of high-strength steel sheet according to claim 8, wherein, the plating is electrogalvanizing processing.
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Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN109355583A (en) * | 2018-11-09 | 2019-02-19 | 唐山钢铁集团有限责任公司 | A kind of cold rolled annealed steel band of less anisotropy low-alloy high-strength and its production method |
| CN109963959A (en) * | 2018-10-02 | 2019-07-02 | 日本制铁株式会社 | The manufacturing method of carburizing steel plate and carburizing steel plate |
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| CN114381654A (en) * | 2020-10-21 | 2022-04-22 | 宝山钢铁股份有限公司 | 780 MPa-grade cold-rolled high-strength galvanized steel plate and manufacturing method thereof |
| CN115011873A (en) * | 2022-05-26 | 2022-09-06 | 包头钢铁（集团）有限责任公司 | Hot-galvanized high-strength structural steel with yield strength of 550MPa and production method thereof |
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Citations (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1051764A (en) * | 1989-11-16 | 1991-05-29 | 川崎制铁株式会社 | The high tensile strength cold-rolled steel sheet of stretching flanging characteristic good and hot-dip galvanized steel sheet and manufacture method thereof |
| JP2003293083A (en) * | 2002-04-01 | 2003-10-15 | Sumitomo Metal Ind Ltd | Hot rolled steel sheet and method of producing hot rolled steel sheet and cold rolled steel sheet |
| JP2010285656A (en) * | 2009-06-11 | 2010-12-24 | Nippon Steel Corp | Precipitation strengthening type cold rolled steel sheet, and method for producing the same |
| CN102834539A (en) * | 2010-04-09 | 2012-12-19 | 杰富意钢铁株式会社 | High-strength steel sheet having excellent hot rolling workability, and process for production thereof |
| CN102906295A (en) * | 2010-03-31 | 2013-01-30 | 杰富意钢铁株式会社 | Hot-dip galvanized steel sheet with high tensile strength and superior processability and method for producing same |
| CN102959117A (en) * | 2010-06-25 | 2013-03-06 | 杰富意钢铁株式会社 | High-tension/hot-rolled steel sheet having excellent workability, and method for producing same |
| CN103003460A (en) * | 2010-07-15 | 2013-03-27 | 杰富意钢铁株式会社 | High yield ratio high-strength hot-dip galvanized steel sheet with excellent ductility and hole expansion properties, and manufacturing method thereof |
| CN103469090A (en) * | 2013-09-17 | 2013-12-25 | 北京科技大学 | Annealing method of ultrahigh-strength hot-forming steel |
| CN103732779A (en) * | 2011-08-17 | 2014-04-16 | 株式会社神户制钢所 | High-strength hot-rolled steel plate |
| CN103842540A (en) * | 2011-09-29 | 2014-06-04 | 杰富意钢铁株式会社 | Hot-dip galvanized steel sheet and method for producing same |
| CN103917680A (en) * | 2011-11-08 | 2014-07-09 | 杰富意钢铁株式会社 | High-tensile-strength hot-rolled steel sheet and method for producing same |
| CN103930582A (en) * | 2011-11-08 | 2014-07-16 | 杰富意钢铁株式会社 | High-tensile-strength hot-rolled steel sheet and method for producing same |
| CN104060069A (en) * | 2013-08-07 | 2014-09-24 | 攀钢集团攀枝花钢铁研究院有限公司 | Cold-rolled steel plate and manufacturing method and application thereof |
Family Cites Families (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS4740099Y1 (en) | 1967-04-24 | 1972-12-05 | ||
| JP2688384B2 (en) * | 1989-11-16 | 1997-12-10 | 川崎製鉄株式会社 | High-strength cold-rolled steel sheet and hot-dip galvanized steel sheet having excellent stretch flange characteristics, and methods for producing the same |
| JPH06322479A (en) | 1993-05-14 | 1994-11-22 | Nippon Steel Corp | Good workability hot dip plated high strength steel sheet excellent in fatigue property and local deformability and its production |
| JP5082773B2 (en) * | 2007-10-31 | 2012-11-28 | Ｊｆｅスチール株式会社 | High tensile cold-rolled steel sheet and method for producing the same |
| JP4995109B2 (en) | 2008-02-07 | 2012-08-08 | 新日本製鐵株式会社 | High-strength cold-rolled steel sheet excellent in workability and impact resistance and method for producing the same |
| EP2799562B1 (en) * | 2011-12-27 | 2015-10-14 | JFE Steel Corporation | Hot-rolled steel sheet and process for manufacturing same |
| KR101518588B1 (en) * | 2013-10-01 | 2015-05-07 | 주식회사 포스코 | Precipitation hardening steel sheet having excellent yield strength and yield ratio and method for manufacturing the same |
| WO2015118864A1 (en) | 2014-02-05 | 2015-08-13 | Ｊｆｅスチール株式会社 | High-strength hot-rolled steel sheet and production method therefor |
-
2016
- 2016-08-18 CN CN201680047641.XA patent/CN107923013B/en active Active
- 2016-08-18 MX MX2018001946A patent/MX2018001946A/en unknown
- 2016-08-18 WO PCT/JP2016/003781 patent/WO2017029814A1/en active Application Filing
- 2016-08-18 JP JP2016567261A patent/JP6123957B1/en active Active
- 2016-08-18 KR KR1020187004178A patent/KR102084867B1/en active IP Right Grant
Patent Citations (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1051764A (en) * | 1989-11-16 | 1991-05-29 | 川崎制铁株式会社 | The high tensile strength cold-rolled steel sheet of stretching flanging characteristic good and hot-dip galvanized steel sheet and manufacture method thereof |
| JP2003293083A (en) * | 2002-04-01 | 2003-10-15 | Sumitomo Metal Ind Ltd | Hot rolled steel sheet and method of producing hot rolled steel sheet and cold rolled steel sheet |
| JP2010285656A (en) * | 2009-06-11 | 2010-12-24 | Nippon Steel Corp | Precipitation strengthening type cold rolled steel sheet, and method for producing the same |
| CN102906295A (en) * | 2010-03-31 | 2013-01-30 | 杰富意钢铁株式会社 | Hot-dip galvanized steel sheet with high tensile strength and superior processability and method for producing same |
| CN102834539A (en) * | 2010-04-09 | 2012-12-19 | 杰富意钢铁株式会社 | High-strength steel sheet having excellent hot rolling workability, and process for production thereof |
| CN102959117A (en) * | 2010-06-25 | 2013-03-06 | 杰富意钢铁株式会社 | High-tension/hot-rolled steel sheet having excellent workability, and method for producing same |
| CN103003460A (en) * | 2010-07-15 | 2013-03-27 | 杰富意钢铁株式会社 | High yield ratio high-strength hot-dip galvanized steel sheet with excellent ductility and hole expansion properties, and manufacturing method thereof |
| CN103732779A (en) * | 2011-08-17 | 2014-04-16 | 株式会社神户制钢所 | High-strength hot-rolled steel plate |
| CN103842540A (en) * | 2011-09-29 | 2014-06-04 | 杰富意钢铁株式会社 | Hot-dip galvanized steel sheet and method for producing same |
| CN103917680A (en) * | 2011-11-08 | 2014-07-09 | 杰富意钢铁株式会社 | High-tensile-strength hot-rolled steel sheet and method for producing same |
| CN103930582A (en) * | 2011-11-08 | 2014-07-16 | 杰富意钢铁株式会社 | High-tensile-strength hot-rolled steel sheet and method for producing same |
| CN104060069A (en) * | 2013-08-07 | 2014-09-24 | 攀钢集团攀枝花钢铁研究院有限公司 | Cold-rolled steel plate and manufacturing method and application thereof |
| CN103469090A (en) * | 2013-09-17 | 2013-12-25 | 北京科技大学 | Annealing method of ultrahigh-strength hot-forming steel |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109963959A (en) * | 2018-10-02 | 2019-07-02 | 日本制铁株式会社 | The manufacturing method of carburizing steel plate and carburizing steel plate |
| CN109355583A (en) * | 2018-11-09 | 2019-02-19 | 唐山钢铁集团有限责任公司 | A kind of cold rolled annealed steel band of less anisotropy low-alloy high-strength and its production method |
| TWI721696B (en) * | 2018-12-20 | 2021-03-11 | 日商杰富意鋼鐵股份有限公司 | Steel plate for tank and manufacturing method thereof |
| TWI728659B (en) * | 2019-01-30 | 2021-05-21 | 日商杰富意鋼鐵股份有限公司 | High-carbon hot-rolled steel plate and manufacturing method thereof |
| CN114381654A (en) * | 2020-10-21 | 2022-04-22 | 宝山钢铁股份有限公司 | 780 MPa-grade cold-rolled high-strength galvanized steel plate and manufacturing method thereof |
| CN115011873A (en) * | 2022-05-26 | 2022-09-06 | 包头钢铁（集团）有限责任公司 | Hot-galvanized high-strength structural steel with yield strength of 550MPa and production method thereof |
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| JPWO2017029814A1 (en) | 2017-08-17 |
| CN107923013B (en) | 2020-06-16 |
| MX2018001946A (en) | 2018-06-19 |
| JP6123957B1 (en) | 2017-05-10 |
| WO2017029814A1 (en) | 2017-02-23 |
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| KR20180030109A (en) | 2018-03-21 |
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