CN105143493A - Method for manufacturing a metal coated and hot-formed steel component and a metal coated steel strip product - Google Patents
Method for manufacturing a metal coated and hot-formed steel component and a metal coated steel strip product Download PDFInfo
- Publication number
- CN105143493A CN105143493A CN201480022812.4A CN201480022812A CN105143493A CN 105143493 A CN105143493 A CN 105143493A CN 201480022812 A CN201480022812 A CN 201480022812A CN 105143493 A CN105143493 A CN 105143493A
- Authority
- CN
- China
- Prior art keywords
- thermoforming
- steel
- temperature
- beam column
- metal coated
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 208
- 239000010959 steel Substances 0.000 title claims abstract description 208
- 238000000034 method Methods 0.000 title claims abstract description 113
- 229910052751 metal Inorganic materials 0.000 title claims abstract description 42
- 239000002184 metal Substances 0.000 title claims abstract description 42
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 29
- 238000001953 recrystallisation Methods 0.000 claims abstract description 80
- 238000000576 coating method Methods 0.000 claims abstract description 65
- 239000011248 coating agent Substances 0.000 claims abstract description 59
- 229910000851 Alloy steel Inorganic materials 0.000 claims abstract description 15
- 238000003856 thermoforming Methods 0.000 claims description 88
- 239000013078 crystal Substances 0.000 claims description 60
- 230000008569 process Effects 0.000 claims description 58
- 238000010438 heat treatment Methods 0.000 claims description 52
- 238000005406 washing Methods 0.000 claims description 33
- 238000000137 annealing Methods 0.000 claims description 30
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 24
- 238000001816 cooling Methods 0.000 claims description 22
- 229910045601 alloy Inorganic materials 0.000 claims description 20
- 239000000956 alloy Substances 0.000 claims description 20
- 239000010960 cold rolled steel Substances 0.000 claims description 20
- 239000010955 niobium Substances 0.000 claims description 20
- 239000010936 titanium Substances 0.000 claims description 16
- 239000011701 zinc Substances 0.000 claims description 16
- 238000005275 alloying Methods 0.000 claims description 15
- 238000010791 quenching Methods 0.000 claims description 15
- 238000005097 cold rolling Methods 0.000 claims description 14
- 238000007493 shaping process Methods 0.000 claims description 12
- 229910052742 iron Inorganic materials 0.000 claims description 11
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 11
- 229910052799 carbon Inorganic materials 0.000 claims description 10
- 229910052758 niobium Inorganic materials 0.000 claims description 10
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 8
- 238000007747 plating Methods 0.000 claims description 8
- 229910052719 titanium Inorganic materials 0.000 claims description 8
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 7
- 238000007598 dipping method Methods 0.000 claims description 7
- 229910052725 zinc Inorganic materials 0.000 claims description 7
- 238000005246 galvanizing Methods 0.000 claims description 5
- 239000012535 impurity Substances 0.000 claims description 5
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims description 5
- 101100129500 Caenorhabditis elegans max-2 gene Proteins 0.000 claims description 3
- 230000006698 induction Effects 0.000 claims description 2
- 101100083446 Danio rerio plekhh1 gene Proteins 0.000 claims 2
- 230000006872 improvement Effects 0.000 abstract description 6
- 239000000463 material Substances 0.000 abstract description 3
- 230000003313 weakening effect Effects 0.000 abstract description 3
- 229910001566 austenite Inorganic materials 0.000 description 39
- 238000007669 thermal treatment Methods 0.000 description 17
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 14
- 230000008901 benefit Effects 0.000 description 10
- 238000010899 nucleation Methods 0.000 description 10
- 230000006911 nucleation Effects 0.000 description 10
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 7
- 230000008859 change Effects 0.000 description 7
- 229910052757 nitrogen Inorganic materials 0.000 description 7
- 230000000171 quenching effect Effects 0.000 description 7
- 238000002474 experimental method Methods 0.000 description 6
- 229910000734 martensite Inorganic materials 0.000 description 6
- 229910052796 boron Inorganic materials 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 230000009467 reduction Effects 0.000 description 5
- 229910000859 α-Fe Inorganic materials 0.000 description 5
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 4
- 239000011575 calcium Substances 0.000 description 4
- 239000011651 chromium Substances 0.000 description 4
- 238000005261 decarburization Methods 0.000 description 4
- 238000005516 engineering process Methods 0.000 description 4
- 238000005530 etching Methods 0.000 description 4
- 229910000765 intermetallic Inorganic materials 0.000 description 4
- 239000011572 manganese Substances 0.000 description 4
- 229910052710 silicon Inorganic materials 0.000 description 4
- 230000009466 transformation Effects 0.000 description 4
- 229910001297 Zn alloy Inorganic materials 0.000 description 3
- 229910052782 aluminium Inorganic materials 0.000 description 3
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 3
- 229910052804 chromium Inorganic materials 0.000 description 3
- 230000002349 favourable effect Effects 0.000 description 3
- 238000007654 immersion Methods 0.000 description 3
- 229910052748 manganese Inorganic materials 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 150000004767 nitrides Chemical class 0.000 description 3
- 229910052760 oxygen Inorganic materials 0.000 description 3
- 239000001301 oxygen Substances 0.000 description 3
- 238000003825 pressing Methods 0.000 description 3
- 239000010703 silicon Substances 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- 238000003466 welding Methods 0.000 description 3
- 229910000712 Boron steel Inorganic materials 0.000 description 2
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 description 2
- 229910000640 Fe alloy Inorganic materials 0.000 description 2
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 2
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 2
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 2
- 239000005864 Sulphur Substances 0.000 description 2
- XLOMVQKBTHCTTD-UHFFFAOYSA-N Zinc monoxide Chemical compound [Zn]=O XLOMVQKBTHCTTD-UHFFFAOYSA-N 0.000 description 2
- 239000004411 aluminium Substances 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 229910052791 calcium Inorganic materials 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 150000001875 compounds Chemical class 0.000 description 2
- 239000010949 copper Substances 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 230000003111 delayed effect Effects 0.000 description 2
- 238000011161 development Methods 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 229910001092 metal group alloy Inorganic materials 0.000 description 2
- 238000000465 moulding Methods 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 229910052698 phosphorus Inorganic materials 0.000 description 2
- 239000011574 phosphorus Substances 0.000 description 2
- 238000005554 pickling Methods 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 238000002203 pretreatment Methods 0.000 description 2
- 229910052761 rare earth metal Inorganic materials 0.000 description 2
- 150000002910 rare earth metals Chemical class 0.000 description 2
- 238000004381 surface treatment Methods 0.000 description 2
- 229910018125 Al-Si Inorganic materials 0.000 description 1
- 229910018520 Al—Si Inorganic materials 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910001335 Galvanized steel Inorganic materials 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- -1 aluminium-magnesium-zinc Chemical compound 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 238000004140 cleaning Methods 0.000 description 1
- 238000000641 cold extrusion Methods 0.000 description 1
- 238000010288 cold spraying Methods 0.000 description 1
- 239000000567 combustion gas Substances 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000001351 cycling effect Effects 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000001419 dependent effect Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000006477 desulfuration reaction Methods 0.000 description 1
- 230000023556 desulfurization Effects 0.000 description 1
- 230000004069 differentiation Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000006056 electrooxidation reaction Methods 0.000 description 1
- 238000009713 electroplating Methods 0.000 description 1
- 238000001125 extrusion Methods 0.000 description 1
- 238000007667 floating Methods 0.000 description 1
- 239000008397 galvanized steel Substances 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 238000007749 high velocity oxygen fuel spraying Methods 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 239000000543 intermediate Substances 0.000 description 1
- UQSXHKLRYXJYBZ-UHFFFAOYSA-N iron oxide Inorganic materials [Fe]=O UQSXHKLRYXJYBZ-UHFFFAOYSA-N 0.000 description 1
- KFZAUHNPPZCSCR-UHFFFAOYSA-N iron zinc Chemical compound [Fe].[Zn] KFZAUHNPPZCSCR-UHFFFAOYSA-N 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 229910001338 liquidmetal Inorganic materials 0.000 description 1
- 238000012423 maintenance Methods 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000005272 metallurgy Methods 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- NDLPOXTZKUMGOV-UHFFFAOYSA-N oxo(oxoferriooxy)iron hydrate Chemical compound O.O=[Fe]O[Fe]=O NDLPOXTZKUMGOV-UHFFFAOYSA-N 0.000 description 1
- 238000010422 painting Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 238000011084 recovery Methods 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000004904 shortening Methods 0.000 description 1
- 238000005507 spraying Methods 0.000 description 1
- 238000003860 storage Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 230000001360 synchronised effect Effects 0.000 description 1
- JBQYATWDVHIOAR-UHFFFAOYSA-N tellanylidenegermanium Chemical compound [Te]=[Ge] JBQYATWDVHIOAR-UHFFFAOYSA-N 0.000 description 1
- 238000011282 treatment Methods 0.000 description 1
- 238000009966 trimming Methods 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- 238000004804 winding Methods 0.000 description 1
- 239000011787 zinc oxide Substances 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
- C23C2/04—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
-
- 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
- C21D7/00—Modifying the physical properties of iron or steel by deformation
- C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/62—Quenching devices
- C21D1/673—Quenching devices for die quenching
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- 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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
-
- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
- C21D8/0473—Final recrystallisation annealing
-
- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0478—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing involving a particular surface treatment
-
- 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
-
- 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
- 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
-
- 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
-
- 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
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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
-
- 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
- C23C2/29—Cooling or quenching
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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
- 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
- C25D5/00—Electroplating characterised by the process; Pretreatment or after-treatment of workpieces
- C25D5/48—After-treatment of electroplated surfaces
- C25D5/50—After-treatment of electroplated surfaces by heat-treatment
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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
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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
- C21D2211/001—Austenite
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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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- 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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- 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
- C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
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- Chemical Kinetics & Catalysis (AREA)
- Thermal Sciences (AREA)
- Physics & Mathematics (AREA)
- Crystallography & Structural Chemistry (AREA)
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Abstract
The present invention relates to a method for manufacturing a metal coated and hot-formed steel component by direct hot-forming techniques and to a metal coated steel strip product for direct hot-forming. Improvements in mechanical properties of the metal coated and hot-formed steel component are difficult to be obtained without weakening the weldability. According to the invention, the grain structure of a metal coated steel strip made of hardenable steel alloy is deformed comprising non-recrystallized grains and a yield ratio (YS/TS) of said steel strip is higher than 0.75. Recrystallization of said grain structure is at least retarded or even totally avoided or leaved out prior to and during applying metal coating on the surface of the steel strip. This kind of material cannot be used in indirect press hardening, but fits excellently to direct hot press forming and provides possibility to affect mechanical properties without weakening weldability.
Description
Technical field
The present invention relates to the method for the steel beam column for being manufactured washing and thermoforming by direct thermoforming technology, and particularly relate to the so a kind of method according to independent claim 1.
The invention further relates to the metal coated steel strip product for direct thermoforming, and particularly relate to the so a kind of product according to independent claim 15.
Background technology
Thermoforming for the production of the superstrength steel beam column being particularly useful for automotive industry is perfect technique.As term, thermoforming comprises several such as hot stamping or hot-forming term.When also considering metallurgy phase transformation, usually use other term, such as die quenching (diequenching) and pressure quench (die quenching, presshardening).The most frequently used practice is direct thermoforming, and wherein the shape of steel beam column is formed as steel plate (steelsheet) at elevated temperatures.In the thermoforming process comprising pressure quench, by hardenable (hardenable) steel plate at high temperature thermoforming, use the extrusion forming die quenching of cooling subsequently.Therefore steel beam column is obtaining its shape and mechanical property in once pressurizeing.This is an example of the direct thermoforming process of the quenching comprised in pressurization.Alternately, in first steel plate can being pressurizeed first, cold-forming is preformed steel beam column, is heated by preformed steel beam column subsequently and thermoforming in the second pressurization.The latter is so-called indirect thermal moulding process, and wherein most distortion is normally carried out in cold extrusion forming.
Usually, this thermoforming technology is compared cold forming techniques and is provided several benefit, the formability of such as steel remarkable improvement in a heated state, and the spring-back effect of the reduction causing the dimensional precision of steel beam column to be improved.In addition, shaping needs at high temperature cause the less forming force of better material use efficiency.In addition, even if after pressure quench, steel beam column still comprises some deformabilities.But this well-known thermoforming process also has some shortcomings, such as oxide skin can be formed on the surface of the steel in the process of uncontrolled furnace atmosphere heating.Uncontrolled atmosphere herein means not use shielding gas.This ferriferous oxide must be removed before coating processes subsequently, thus cause cost to increase.In addition, exposed surface of steel plate may stand decarburization in heat-processed, and it can cause unacceptable loss of mechanical properties.These shortcomings limit thermoforming process use more wide in range in production superstrength automobile steel component.
Therefore, in recent years, in order to meet the needs day by day increased to more lightweight structure in automotive industry, determined that there is different metallic coatings, such as zinc or zinc-base or the steel plate of Al-Si coating be applicable to thermoforming.Exemplary patents about this is openly EP1143029A.Phase mutual diffusion between having been found that by the iron in coating and steel plate prevents or at least reduces the fusing of austenitization floating coat of steel.Those coatings are by known such as hot dip process or Electroplating Production, and they have protection steel surface by the ability of decarburization and/or oxidation.Several up-to-date development effort has been intended to develop the different coatings for thermoforming, to meet the challenge directly and in indirect thermal moulding process.Naturally, in indirect thermal is shaping, steel plate must be at room temperature plastic, is possible to make the coldmoulding in the first pressurization.This means must before coating by cold rolling steel band and softing annealing.Usually this can before coating in the temperature higher than recrystallization temperature such as at the temperature of 700-900 DEG C, in continuous annealing process, carry out the time in a large number or completely required for recrystallize.Therefore, according to prior art, if particularly steel band is intended to for comprising in the technique of cold-forming, then apply the softening annealing steel band with the microtexture be made up of recrystal grain.Therefore, equally in the later stage heating steps of thermoforming, softening annealing steel band in prior art, is employed.
In automobile assembly line, welding process is the method for attachment being most commonly used to connect this steel beam column.Particularly spot welding, is widely used in welding of automotive steel beam column, this is because such as it is applicable to steel-sheet fast method, and can fully automated.But, fast and the technique of automatization is provided with several requirement to the factor affecting steel beam column weldability.The general weldability of such as steel should be as well as possible, and lower CEV (carbon equivalent) value is high expectations.Usually the hardenable steel generally used, the boron steel of such as different grades, as 22MnB5, has the CEV value within the scope of very high 0.50-0.55.Particularly when considering the hardenable steel grade provided higher than the intensity of typical 22MnB5, produced problem is that CEV increases further and weakens weldability, and this is less desirable.In addition, when intensity increases, ductility is affected usually.Generally speaking, the mechanical property of the steel assembly of metallic coating and thermoforming is difficult to be improved when not weakening weldability.In addition, different application systems suffers the crack problem of several types.
Summary of the invention
Goal of the invention
First object of the present invention is to provide the steel band of the washing for direct thermoforming, and next is to provide the method for the steel beam column for the manufacture of washing and thermoforming, solves or at least alleviate one or more problems of prior art both it.
The object of the invention is to utilize the method for the steel beam column for the manufacture of washing and thermoforming according to claim 1 to realize.Object of the present invention still utilizes the strip product of washing according to claim 15 to realize.The preferred embodiment of the present invention is open in dependent claims 2-14 and 16-23.
The cutline of invention
According to the viewpoint presented above, contriver finds in directly hot-forming, due to shaping be the fact of carrying out at elevated temperatures, therefore in fact cold formability is not required, and by affecting the original grain structure of metal coated steel strip, the mechanical property of the washing of being produced by direct thermoforming process and the steel beam column of thermoforming may be affected and not weaken weldability.Therefore, the present invention is the yield ratio produced based on the original grain structure produced and based on metal coated steel strip product before thermoforming hot-plate.
According to the present invention, for direct thermoforming, the crystalline-granular texture of metal coated steel strip product be made up of hardenable steel alloy is the deformed grains structure of the crystal grain comprising non-recrystallization, and the yield ratio of strip product (YS/TS) is higher than 0.75.Before the recrystallize of described crystalline-granular texture applies metallic coating in steel strip surface, in process and immediately thereafter, be at least delayed, and even avoid completely or eliminate (leavedout).
According to the present invention, for the steel band of deformed grains structure with the crystal grain comprising non-recrystallization, carry out the step on surface metallic coating being applied to cold-rolled steel strip, to obtain the deformed grains structure still with the crystal grain comprising non-recrystallization and the metal coated steel strip product of yield ratio (YS/TS) had higher than 0.75, and will have the heating steps of strip product for thermoforming of the washing of deformed grains structure and high yield ratio (YS/TS).
This strip product can not be used successfully to indirect weighting quenching, but is applicable to directly hot-forming, and provides and affect mechanical property and the possibility that do not weaken weldability.This is because the crystalline-granular texture comprising the high deformation of the crystal grain of non-recrystallization comprises because the austenitizing heating before thermoforming and cooling causes high potential nucleus (i.e. nucleation site) number providing the austenite of compact grained austenite (γ) (γ) crystal grain.The volume fraction of the crystal grain of non-recrystallization is higher, the potential initial growth point of austenite crystal or the number of nucleation site higher.When this washing austenitic steel carries product in microtexture with fine grained austenite (γ) carries out thermoforming and cooling, particularly when thermoforming and pressure quench, have been found that the steel beam column of washing and thermoforming can comprise the mechanical property improved because of thinner original austenite (γ) crystal grain.When thermoforming and pressure quench, this original austenite (γ) can form thinner martensitic bag (packet) and block.This provide the possibility reducing alloying levels, thus do not lose intensity by reducing CEV to improve weldability.In addition, this strip product can provide the coating characteristic of improvement in hot-forming.
In addition, advantageously utilize according to strip product of the present invention in rapid heating and thermoforming circulation, this production making to comprise the equipment with different operating-cycling time is more smooth and easy.But, because initial original austenite (γ) grain-size may be very little, therefore also may be used for typical long-time according to steel band of the present invention, i.e. slow thermoforming circulation.This is because due to the present invention, initial original austenite (γ) particle size is less, it can compensate the grain growing that can occur when the time lengthening of austenitizing in stove at least partly.
Very importantly still, the metallic coating being applied to steel strip surface removes step by the ferric oxide got rid of after thermoforming that is above-mentioned, that carry out in typical uncontrolled furnace atmosphere, provides significant technology and economic advantages finally.In addition, metallic coating can prevent the decarburization in thermoforming process process, and it may be disadvantageous for the mechanical property of the steel assembly of thermoforming.
Accompanying drawing explanation
Fig. 1 is the schematic diagram according to step included in method of the present invention.
Fig. 2 is the diagrammatical time-hygrogram (not to scale (NTS)) according to step included in method of the present invention.
Fig. 3 illustrates the schematic diagram according to several replaceable embodiment of the present invention.
Fig. 4 illustrates the diagrammatical time-hygrogram (not to scale (NTS)) according to the feature of detailed embodiment of the present invention.
Fig. 5 illustrates the diagrammatical time-hygrogram (not to scale (NTS)) according to the feature of other detailed embodiment of the present invention.
Fig. 6 shows according to product made from steel 16 of the present invention.
Fig. 7 shows and works as T
max1the differentiation of crystalline-granular texture recrystallize during change.Picture is captured by opticmicroscope (LePera etching).
Fig. 8 shows the picture of the crystalline-granular texture of complete non-recrystallization.Picture is taken by opticmicroscope (Nital etching).
The brief description of reference number and term
1 step 1, provides the steel band be made up of hardenable steel alloy
2 steps 2, cold rolling
3 steps 3, heating (optionally)
3.1 steps 3.1, first time annealing (optionally)
4 steps 4, apply metallic coating
4.1 steps 4.1, apply metallic coating (optionally) by hot dip process
4.2 steps 4.2, plating (optionally)
5 steps 5, stamping-out (blanking, blanking)
6 steps 6, are heated above A
c1temperature
First heating zone of 6.1 steps 6
Second heating zone of 6.2 steps 6
7 steps 7, thermoforming
8 steps 8, cooling
9 steps 9, second time annealing (optionally)
The 10 deformed grains structures comprising the crystal grain of non-recrystallization
The 10.1 deformed grains structures comprising non-recrystallization crystal grain that there is not any reply
10.2 comprise the distortion of non-recrystallization crystal grain and the crystalline-granular texture that may reply
10.3 comprise the distortion of non-recrystallization crystal grain and the crystalline-granular texture of reply at least partly
11 steps 11, third time annealing (optionally)
12 close grain original austenites (γ), the austenite namely formed in step 6 process
13 steps 13, carry out the first preliminary thermal treatment (optionally)
14 steps 14, carry out the second preliminary thermal treatment (optionally)
15 steps 15, cooling (optionally)
16 for the strip product of the washing of direct thermoforming, i.e. washing thermoforming strip product
17 blanks (blank)
T
heatstart the time calculated to step 7 from step 6
T
baththe temperature of metallizing or metal alloy in hot dipping plating bath (bath)
T
maxtop temperature in step 13 or 14 processes
T
max1top temperature in step 3.1 process
T
max2top temperature in step 9 process
T
hot-dipthe temperature of steel band in step 4.1 process
T
rxrecrystallization temperature
A
c1in heat-processed, austenite (γ) starts the temperature formed
A
c3the temperature that in heat-processed, ferrite (α) to the conversion of austenite (γ) completes
A
r1the temperature that in process of cooling, austenite (γ) to the conversion of ferrite (α) completes
A
r3in process of cooling, austenite (γ) starts the temperature being converted into ferrite (α)
Embodiment
According to the present invention, the deformed grains structure of metal coated steel strip product comprises non-recrystallization crystal grain 10.1,10.2,10.3, and the yield ratio of strip product (YS/TS) is higher than 0.75.The recrystallize of described crystalline-granular texture, before steel strip surface applies metallic coating and in process, is at least delayed, and even avoids completely or eliminate.This one or morely optionally tentatively can control maximum heating temperature T in heat treatment step process by what such as carry out after for cold rolling step 2 but before the step 6 heat for austenitizing starts
maxcarry out, make T
maxlower than the recrystallization temperature T of deformed grains structure comprising non-recrystallization crystal grain
rx.Recrystallization temperature T
rxtogether depend on heat-up time with other factors, itself so that depend on line speed and the length of production equipment.Therefore, in step 6, also be there is by the steel plate 17 of described steel band stamping-out the deformed grains structure comprising non-recrystallization crystal grain, and use the yield ratio (YS/TS) higher than 0.75.
Recrystallization mechanism needs to occur at the lowest temperature.Recrystallization temperature T
rxbe that crystal grain in the crystalline network of wherein steel rearranges, make steel containing the temperature of significantly strain (strain) and deformed grains.It depends primarily on heat-up time and cold rolling draft (reductionrate).Therefore, T
rxmeant to comprise the deformed grains structure of non-recrystallization crystal grain before discussed thermal treatment, the recrystallization temperature under each particular case.Except several material parameter constant, can be based on, such as, the heat-up time depending on working condition of particular condition and draft calculate this temperature.But because deformed grains comprises high storage energy state, therefore they are thermodynamic instabilities.At least part of reply that Here it is as hereafter illustrated deformed grains structure can occur, but the crystalline-granular texture of metal coated steel strip is still distortion and comprises the reason of non-recrystallization crystal grain.
With reference to Fig. 1 and 2, show the essence of the present invention of the steel beam column of washing constructed in accordance and thermoforming.When starting, provide the steel band be made up of hardenable steel alloy in step 1.This steel band can by such as hot rolling also pickling subsequently (pickling) hot rolled strip acquisition.Steel band is with the quenching of the amount/degree expected, the amount required for martensitic transformation of the amount/degree namely expected comprises alloying element, so this steel band is made up of hardenable steel alloy.Described steel band stands step 2 further, wherein carries out cold rolling.This means that the thickness of steel band reduces in step 2 process.But the more important thing is as previously mentioned, the 2 couples of the present invention of this cold rolling step are necessary, especially because it provides the deformed grains structure 10.1 comprising non-recrystallization crystal grain to steel band.And then step 2 is in this deformed grains structure 10.1, and crystalline-granular texture is not replied, and namely it is in so-called fully hard (full-hard) state.After described step 2 is cold rolling, steel band stands step 4, metallic coating is applied to the cold-rolled steel strip surface with the deformed grains structure 10.1,10.2,10.3 comprising non-recrystallization crystal grain.In other words, described step 4, is applied to cold-rolled steel strip surface and carries out for following by metallic coating: have the deformed grains structure 10.1 comprising the non-recrystallization crystal grain that there is not any reply steel band or there is the distortion and the steel band of the crystalline-granular texture 10.2 that may reply that comprise non-recrystallization crystal grain or there is the distortion that comprises non-recrystallization crystal grain and the steel band of the crystalline-granular texture 10.3 of replying at least partly.Usually and contrary with the present invention, namely according to prior art, if especially steel band is intended to the technique for comprising cold-forming, as said above, this coating step 4 carries out for the softening annealing steel band be made up of the recrystal grain in microtexture.Therefore, in heating steps 6 afterwards, prior art uses the steel band of softening annealing equally.This step 4 provides corrosion-resistant coating for product made from steel, and protects steel surface to avoid decarburization in the heat-processed related in thermoforming process and/or oxidation.In fact, can be undertaken for the step 4 applied by diverse ways, wherein several can present later.As found out from Fig. 1 and 3, the strip product according to washing of the present invention obtains substantially after step 4.But, the annealing of step 9 second time can be carried out after step 4, the annealing of such as alloying zinc-plated (galvanneal) type (namely forms the intermetallic compound comprising the metallizing of iron and coating, as shown in Figures 4 and 5), and subsequently before strip product winding, (not shown) is cooled.Usually, but and unnecessary, strip product is transported to the place with thermal forming device from Zhi Gang factory with scroll.Cut to the product of certain length, namely sheet is also enough sometimes.Therefore, term strip product also comprises steel plate 17, as shown in Figure 6.
Refer again to Fig. 1, the metal coated steel strip product 16 of the application of the invention continues method of the present invention, and the method in fact provides the benefit of metal coated steel strip product of the present invention.Do not consider position or the types of transportation of product made from steel, after step 4, method comprises step 5, wherein from described metal coated steel strip product stamping-out steel plate 17, as shown in Figure 6.Such as, this can be completed by mechanical cutting device.Naturally, this blanking step 5 can not affect crystalline-granular texture and its performance.After this, in step 6 steel plate 17 is heated to the temperature that wherein microtexture comprises austenite (γ).Steel plate 17 is this means to be heated above A
c1, preferably higher than A
c3temperature.Preferably, in step 6, the local of not only heating steel sheet 17 by the heating of whole plate.Due to step 2 and 4 particular combination, after step 6, compact grained original austenite (γ) 12 can be obtained in the microtexture of steel plate 17.In other words, step 2 and 4 particular combination be to obtain compact grained original austenite (γ) 12 in step 6 process and afterwards in the microtexture of steel plate 17.A
c1lower limit, because otherwise cannot austenite be obtained.But, in heat-processed, two-phase temperature range (A
c1to A
c3) the two-phase microtexture of mixture of ferrite (α)-pearlitic grain having fine grained austenite (γ) and extend can be provided.A
c3be preferred lower limit, because can form the martensite of maximum like this in microtexture, and grain refining effect also can be more effective.Thus favourable equiaxed grain structures can also be obtained.But the temperature at the end of heating is preferably not higher than A
c3+ 50 DEG C, preferably not higher than A
c3+ 30 DEG C.Therefore, the step 11 third time annealing after step 6 can be carried out under the temperature in the scope of 880 to 950 DEG C.This is because at a higher temperature, too much grain growing may be there is.If steel plate 17 is heated above A
c3but lower than A
c3the temperature of+50 DEG C, can obtain the microtexture be made up of fine grained austenite (γ) 12 completely.Step 6 heats also may comprise the first heating zone 6.1 and the second heating zone 6.2, as shown in Figures 4 and 5.After step 6 heats, by steel plate 17 thermoforming in step 7 of heating.This can be, and such as pressing shaping device, carries out in instant heating pressing shaping device.It should be noted that described steel plate 17 relates to before step 6 or step 7, not significantly, preferably there is no the steel plate that (pre--) is shaped at all.In this step 7 process, steel plate 17 is thermoformed into shaping steel beam column, the shape of at least part of corresponding final steel component of its shape.After thermoforming, the steel beam column of shaping is cooled in step 8.Depend on the mechanical property of desired steel beam column, this can carry out in different mode as known in the art.Such as, cooling in pressure quench technique, can be undertaken by the pressing mold of active cooling.In this cooling step process, in steel beam column, there is desired microstructural change.Usually after the cooling step, trimming and/or some perforation can be carried out to steel beam column.Also may need before painting to remove the zinc oxide in coated steel component surface.The one-tenth Steel section member obtained can have the mechanical property of improvement.
It should be noted that the step except listing in independent claim, method also can comprise other steps.But, it should be noted that the step illustrated in the claims is carried out with given order (or given sequence), and other steps illustrated as follows can be there are between given step.
According to an embodiment, method also comprises carries out the first preliminary heat treated step 13 to cold-rolled steel strip.This first preliminary heat treatment step 13 carries out after step 2 with before step 4.Carry out described step 13, to make the top temperature T in this step 13 process
maxlower than the recrystallization temperature T of deformed grains structure 10.1,10.2 comprising non-recrystallization crystal grain
rx, in other words, T
max<T
rx.This temperature limitation provides, even if cold-rolled steel strip is through heat-treated, microtexture still keeps the deformed grains structure 10 comprising non-recrystallization crystal grain.In other words, at recrystallization temperature T
rxbelow anneal and will substantially keep by the cold rolling deformed grains caused.Therefore, metal coated steel strip product also keeps very high yield ratio (YS/TS), as this specification sheets describes in further detail subsequently.But this first preliminary thermal treatment is dispensable, is described as follows.
In order to improve metallic coating and cold-rolled steel strip steel surface between adhesion, this first preliminary thermal treatment 13 may be needs.This is step 4 situation of being undertaken by hot dip process 4.1 especially, as shown in Fig. 3,4 and 5.Other reasons of first preliminary thermal treatment 13 can be, in heat dipping coating line is installed, may be difficult to it be omitted completely or fundamentally change.But, in other coating processes, such as in plating or thermospray (such as high speed oxygen combustion gas spraying (HVOF) or pneumatic cold spraying) technique, unnecessaryly carry out this first preliminary thermal treatment 13, as shown in Figure 3, such as, but the first preliminary thermal treatment can be with, and, the surface treatment before coating step connects.
Preferably, described step 4 is carried out by the hot dip process 4.1 of steel band in metallizing bath.This is because hot dip process provides thick coat, it provides outstanding Corrosion Protection.The steel beam column be made up of hot dip process steel band, particularly hot-dip galvanized steel strip, is specially adapted to the finished product of such as Motor vehicles.In addition, the step 9 of the zinc-plated type annealing of such as alloying of optionally annealing for second time, due to the temperature that immersion raises at first, can carry out with having more efficiency.In other words, when hot dip process, second time annealing needs less temperature to increase.In addition.Hot dip process can form the natural diffuseness between iron in steel and metallizing.As shown in Figures 4 and 5, in this hot dip process step 4.1 process, by the steel band of preheating at specified temp T
hot-diplower immersion specified temp T
bathunder liquid metallizing bath in.In usual hot dipping plating bath, the temperature of metallizing is no more than 100 DEG C than the melt temperature of metallizing is high in bath.The temperature T when steel band being immersed bath
hot-dippreferably higher than temperature T
bath-100 DEG C, more preferably higher than temperature T
bath, as shown in Figures 4 and 5.When hot dip process, in the preliminary thermal treatment of step 13 first, carry out this preheat, it comprises hereafter shown several embodiments.
According to first embodiment of method, as shown in Figure 4, the preliminary thermal treatment of described step 13 first comprises step 3, and cold-rolled steel strip is heated above temperature T
baththe temperature T of-100 DEG C
hot-dip, wherein T
baththe temperature of metallizing in hot dipping plating bath, and at this T
hot-dipstep 4.1 hot dip process is carried out at temperature.More advantageously, carry out step 3 and heat cold-rolled steel strip extremely higher than temperature T
bathtemperature T
hot-dip.Such coating adheres to and improves.This first embodiment is preferred, and because it eliminates too much thermal treatment, it can be replied for a long time at elevated temperatures because of cold-rolled steel strip and/or recrystallize tendency reduces effect of the present invention.Therefore, in this embodiment shown in Fig. 4, the advantage according to galvanizing product made from steel of the present invention can be emphasized.Typical pre-treatment, such as surface cleaning and/or one or more other surface treatments, preferred pin carries out cold-rolled steel strip as usual.But, electrolytic clean or other do not need the method for significantly heating to be preferred.The pre-treatment on these surfaces improves coating and adheres to.
As shown in Figure 5, in alternative second embodiment, described step 13 comprises several step, and its first step is for be heated to the first annealing temperature T by cold-rolled steel strip
max1step 3.After this temperature T within the scope of 420 to 800 DEG C is carried out
max1under, more preferably basic lower than A
c1temperature under, carry out at the temperature such as within the scope of 420 to 695 DEG C for first time annealing step 3.1.First time annealing may be needed with by stove pretreating surface, and this improves the optional pretreatment process that coating adheres to.Other reasons of step 3.1 first time annealing can be, in coating line is installed, may be difficult to it be omitted completely or fundamentally change.As can be seen from Figure 5, be step 15 after step 3.1, steel band is cooled to higher than temperature T
baththe temperature T of-100 DEG C
hot-dip, wherein T
baththe temperature of metallizing in hot dipping plating bath, and at this T
hot-diphot dip process is carried out at temperature.More advantageously, carry out step 15 and cool cold-rolled steel strip extremely higher than temperature T
bathtemperature T
hot-dip.Such coating adhesion improves.In other words, in this embodiment, the deformed grains structure after cold rolling can by reducing continuous annealing temperature to recrystallization temperature T
rxbelow keep.
Recrystallization temperature T
rxdepend primarily on heat-up time and cold rolling draft, and its can by such as in the literature available Kolmogorov-Johnson-Mehl-Avrami (KJMA) equation obtain.
Fig. 7 shows the temperature T when first time annealing steps 3.1
max1during change, the experiment of crystalline-granular texture recrystallize develops, and step 3.1 is carried out after step 2 is cold rolling.Picture is taken by opticmicroscope (LePera etching).Hardenable steel alloy has following composition: C:0.23%, Si:0.25%, Mn:1.25%, Al:0.03%, Cr:0.2%, Ti:0.037% and B:0.003%.As can be seen from the experiment, work as T
max1as test 1 and 2 be in the scope of 420 to 800 DEG C time, obtain the distortion that comprises non-recrystallization crystal grain and the crystalline-granular texture 10.3 of replying at least partly.As found out, if T
max1higher than 800 DEG C, as in the experiment 3 and 4 of Fig. 7, the crystalline-granular texture 10 comprising non-recrystallization crystal grain is difficult to keep, and easily, if not inevitably, can occur rapidly recrystallize completely.Crystalline-granular texture in experiment 3 and 4 is perfect recrystallization.
Have been found that microalloying can hinder perfect recrystallization.This is at temperature A
c1and be special needs between 800 DEG C.But under the typical carbon content of the temperature more than 800 DEG C and all C:0.25% according to appointment, austenite (γ) becomes main/most phase, reduces benefit of the present invention.The steel band of experiment 1 and 2 has the yield ratio (YS/TS) higher than 0.75 and the steel band of testing 3 and 4 has yield ratio lower than 0.75.
Fig. 8 shows the picture (Nital etching) of the crystalline-granular texture of complete non-recrystallization, and it is the temperature T of use less than 695 DEG C in experiment 5
max1obtain.This steel band has the yield ratio (YS/TS) higher than 0.80.
Preferably, start in 3 minutes that calculate when described step 7 thermoforming is heating from step 6, i.e. t
heat≤ 3 minutes.This is because more compact grained original austenite (γ) 12 can be obtained like this.So also make process furnace (equipment in step 6) synchronous with the process furnace of reasonable size better with the cycling time of shaped device (equipment in step 7).These stoves are excessive is disadvantageous, because when shaped device interrupts, such as when tool failure, all blanks 17 in stove are broken rapidly by the heat-up time owing to extending, and it may cause such as grain growing and apply unsuccessfully.
But, because this initial original austenite (γ) grain-size may be very little, also may be used for typical long-time according to steel band of the present invention, i.e. slow thermoforming circulation.This is because according to the present invention, initial original austenite (γ) grain-size is less, grain growing when it can compensate the austenitizing time occurring in and extend in stove at least partly.
Still more preferably, using higher than 20 DEG C/s, preferably carrying out the described step 6 for heating higher than the average heating rate of 30 DEG C/s.This can pass through, such as, provide the induction heating equipment of high heating rate to carry out.Can more advantageously realize benefit of the present invention like this, because the proper time of the release of grain growing and/or dislocation (dislocation) (it provides the nucleation site of austenite (γ) crystal grain) reduces, cause thinner austenite (γ) grain-size.Due to these reasons, step 11 third time annealing, namely remains on austenite (γ) scope as shown in Figures 4 and 5, also preferably keeps shorter, is such as less than 2 minutes and even is less than 1 minute.Of short duration maintenance may be necessary to giving some time homogenizing of austenite (γ), but it should remain on inferior limit as far as possible to avoid grain growing.Therefore, described step 7 thermoforming can step 6 heat start time calculate 3 minutes in so that 2 minutes in start, i.e. t
heat≤ 3 minutes and even t
heat≤ 2 minutes.When heating rate is higher than 100 DEG C/s, t can be obtained
heat≤ 1 minute, this processed the improvement causing mechanical property extremely fast.High heating rate cause for the manufacture of have improve the washing of mechanical property and the steel beam column of thermoforming method in smooth Production Flow Chart.
As shown in Figures 4 and 5, comprise the first heating zone 6.1 and the second heating zone 6.2 according to the heating steps 6 of an embodiment, and the heating rate of the second heating zone 6.2 is lower than the heating rate of the first heating zone 6.1.But the average heating rate of step 6 can be as given above.In second heating zone 6.2, lower heating rate improves the coating property in step 6 heating and step 7 thermoforming process, in first heating zone 6.1, higher heating rate decreases the release of nucleation site simultaneously, and supports the nucleation that austenite (γ) is more intensive.
As can be seen from Figure 4 and 5, method also preferably so but and optionally comprise, after step 4 and before step 6, carry out the step 14 of the second preliminary thermal treatment 14, it is included in the recrystallization temperature T lower than the deformed grains structure 10.1,10.2,10.3 comprising non-recrystallization crystal grain
rxtemperature T
max2under, in the temperature range of 450 to 600 DEG C, such as carry out the step 9 of second time annealing.In other words, T
max2<T
rx.But this step 9 second time annealing can under any circumstance be carried out, and in other words, do not consider whether or how step 13 realizes, and how step 4 realizes.When carrying out this and optionally comprising the second preliminary thermal treatment 14 of step 9, metal coated steel strip product and its performance obtain in this step 14 thus.Step 9 also can be referred to as the zinc-plated step 9 of alloying, and its step 4 preferably and then for applying is carried out.High heating rate in step 6 process and low heat-up time t
heatwhen, this step 9 is particularly preferred, this is because it provides iron pre-alloyed in the washing of steel band, its when benefit of the present invention above-disclosed step 6 add rapidly hanker realizing time, be particularly advantageous.As described above, in step 6 process that heating or step 11 third time anneal rapidly, the too much time may not be there is to wait for that appropriate iron level diffuses into metallizing.But, in order to improve hot-forming property and the quality of coating, washing layer is in austenitization, interface particularly between steel and coating, may need that there is specific intermetallic compound and/or sosoloid, because the problem relating to LME (Liquid Metal Embrittlement) can be avoided like this.For this reason, the annealing of step 9 second time when being included in the rapid heating cycle of product made from steel thermoforming according to the present invention, in other words at short t
heatwhen be highly preferred.
As being appreciated that from the above, the preliminary thermal treatment of step 13 first and/or the preliminary thermal treatment of step 14 second all can cause the reply of deformed grains structure 10.1.But, even if can occur some reply, distortion and reply crystalline-granular texture 10.3 still comprise non-recrystallization crystal grain, this is because reply substantially do not affect grain shape.Therefore, add in step 6 and hanker, the steel plate 17 of the crystalline-granular texture (10.3) of at least part of reply and the distortion having and comprise non-recrystallization crystal grain can be used.Non-recrystallization crystal grain means to have their shapes in cold rolling middle acquisition, such as from the crystal grain of the softening annealing equi-axed crystal shape of typical metal coated steel strip differentiable elongated (along rolling direction) grain shape.In other words, " non-recrystallization crystal grain " is adopted not anneal higher than at the temperature of recrystallization temperature to be described in herein, to avoid the state of the steel plate of the minimizing of the physical strength usually occurred in thermal treatment cold-rolled steel strip or steel plate process.
In certain production environments, the partial, re-crystallization of the crystalline-granular texture that also may deform.Recrystallize can be divided into nucleation process and process of growth.Although the top temperature T of preliminary thermal treatment 13,14
max1and/or T
max2lower than the recrystallization temperature T of deformed grains structure comprising non-recrystallization crystal grain
rx, but if heat-up time is long, there will be the situation of partial, re-crystallization.Therefore, step 6 add hanker crystalline-granular texture that operable steel plate 17 has comprise with regard to volume percent higher than 70% non-recrystallization crystal grain, and more preferably higher than 95% non-recrystallization crystal grain.But this steel plate most preferably used maintains the crystalline-granular texture of complete non-recrystallization.Reply and/or partial, re-crystallization may not provide any benefit, but can be inevitable event in certain production environments, such as relate in the hot dip process zinc wire of process furnace at some.
As described above, in step 2 process, the thickness of steel band reduces.Reduction degree (reductiondegree) normally 30-95%, but preferred 25-65%.This is because the recrystallize motivating force that lower draft causes is less, this, when particularly described method comprises optional preliminary heat treatment step 13 and/or 14, can be favourable.But, in other cases, also higher draft can be used.
According to an embodiment, be enough to be induced to small part for cooling the cooling step 8 of described forming steel component, the rate of cooling of the preferably quenching of forming steel component is completely carried out.The rate of cooling needed depends on Steel Alloy, plate thickness and thermoforming degree, but can be such as higher than 10 DEG C/s, or higher than 30 DEG C/s.Such as, for 22MnB5, may be required higher than the rate of cooling of 30 DEG C/s for obtaining martensitic microstructure completely.Which ensure that the superstrength of steel beam column.
According to an embodiment, step 7 thermoforming is at 450-850 DEG C, carries out in the temperature range of preferred 500-700 DEG C, this is because can reduce the risk of the coating failure caused by LME like this.In addition, avoid the recrystallize of austenite (γ) crystal grain, cause thin original austenite (γ) crystal grain to extend in the process of step 7 thermoforming.Lower limit is because otherwise can start martensitic transformation in thermoforming process.The upper limit is for guaranteeing one or more above-mentioned benefit.In this embodiment, method comprises the pre-cooled step (not shown) of rate of cooling to hot-forming temperature of use quickening, and described pre-cooled step was carried out before step 7 thermoforming.Like this in pre-cooled process, together with suitable alloying, austenite (γ) can be avoided to decompose.
Preferably, the described step 7 for thermoforming is carried out in the mould of shaped device, and described cooling step 8 carries out in the mold.Which ensure that the dimensional precision of steel beam column, this is because mould prevents dimensional change from occurring in process of cooling.
Preferably, described metallic coating is zinc (Zn) type coating.This is because advantageously realize benefit of the present invention like this, because Zn makes to use lower application temperature, particularly in immersion, this is the relatively low melt temperature due to Zn.In addition, zinc base coat provides electrochemical corrosion resistant.
As previously described, steel band is made up of hardenable steel alloy.Therefore, it can comprise following alloy with regard to weight percent:
Surplus is iron and inevitable impurity.In addition, some inevitable residue content may be there are.
Particularly when comprising the hot dip process step 4.1 of preliminary heat treatment step 13 and/or 14, with regard to quality or weight percent, the microalloy belonging to one or more alloying elements of the group be made up of titanium (Ti), vanadium (V), niobium (Nb) of 0.01-0.1% is preferred, this is because microalloy is by improving recrystallization temperature T
rx, in the process of carrying out preliminary heat treated optional step 13 and/or 14, prevent recrystallize.In addition, they also hinder austenite (γ) grain growing in step 6, step 11 and step 7 process.Therefore, using microalloy element to be highly preferred, particularly in hot dip process, but is also when other coating methods.
Have been found that niobium is alloying element favourable in the present invention, and therefore use this hardenable steel alloy of Nb:0.005-0.1%, the preferably 0.01-0.08% comprised with regard to weight percent, to improve recrystallization temperature T
rxwith the grain-size controlled in austenitization.
Hardenable chemical composition and its reason can illustrate in greater detail subsequently in this manual.Then, describe in more detail according to product of the present invention.
Product according to the present invention is the metal coated steel strip be made up of hardenable steel alloy, and this product is intended to for direct thermoforming, as mentioned before.This is because the crystalline-granular texture of described steel band is the deformed grains structure 10 comprising non-recrystallization crystal grain, and the yield ratio of strip product (YS/TS) is higher than 0.75, as shown in Figure 6.
Yield ratio (YS/TS) can define based on by the obtainable yield strength of usually known Elongation test (YS) and tensile strength (TS).Rp0.2 is preferably used as yield strength (YS).
Therefore, metal coated steel strip product only keeps very little and limited cold deformation ability, and it substantially by means of only thermoforming, namely can be shaped in direct thermoforming process.But, owing to there is the deformed grains structure 10 comprising non-recrystallization crystal grain, more original austenite (γ) nucleation site is there is in direct thermoforming process, original austenite (γ) crystal grain thus can be thinner, the problem for prior art provides solution or is at least alleviate.In addition, this strip product can provide the coating characteristic of improvement.
In addition, strip product is preferably cold-rolled steel strip, particularly by using this cold-rolled steel strip of reduction degree within the scope of 30-95%, preferably 25-65%.Reduction degree means thickness of strips in cold-rolled process and reduces per-cent.As mentioned before, cold rolling be apply in step 4 before, carry out in step 2.The thickness of strip product can be less than 5mm, preferably in the scope of 0.4 to 2.5mm.
Preferably, the crystalline-granular texture of described metal coated steel strip comprise with regard to volume percent higher than 70% non-recrystallization crystal grain, and more preferably higher than 95% non-recrystallization crystal grain.The method analyzing the volume fraction of non-recrystallization crystal grain in crystalline-granular texture is defined by the open WO2012/053636A1 of such as patent.Most preferably, the crystalline-granular texture of described metal coated steel strip is complete non-recrystallization.Also fully hard term can be used.This is because non-recrystallization crystal grain more and reply fewer, the nucleation site of austenite crystal is more.But the number of nucleation site can reduce because replying in some embodiments.Therefore, the crystalline-granular texture of this metal coated steel strip can be partly or entirely reply, as crystalline-granular texture 10.3.
Crystalline-granular texture due to described steel band is the deformed grains structure comprising non-recrystallization crystal grain, the yield ratio (YS/TS) of strip product higher than 0.75, preferably higher than 0.80 and most preferably higher than 0.90.High yield ratio and non-recrystallization crystal grain one are all the nucleation site that austenite provides a large amount of.
Yield strength (YS) the also preferred representative value higher than this series products of described strip product, preferably higher than 550MPa, more preferably higher than 650MPa.Yield strength (YS) and/or yield ratio (YR) higher, the Recovery and recrystallization of metal coated steel strip product occurs fewer, this so that mean thinner austenite crystal.As comparative example, the typical yield strength (YS) of hardenable boron steel can within the scope of 400-450MPa, namely lower than 500MPa.The intensity mentioned is the value before step 6 or step 7, i.e. the value of strip product in the typical transit environment of Zhi Gang factory.As being appreciated that preferably by this specification sheets, strip product hardens being included in the step of thermoforming process subsequently, and namely it is not in transport condition, namely hardens before stamping-out in steps of 5.In other words, the microtexture of steel band 16 or one or more plate 17 was preferably the mixed structure of ferrite and pearlite before step 6 heats.After possible hardening, in step 8, yield strength (YS) can higher than 900MPa, preferably higher than 1100MPa.
Comprise the distortion of non-recrystallization crystal grain and the characteristic that the crystalline-granular texture 10.3 of replying at least partly can have be yield ratio (YS/TS) higher than 0.80, preferably higher than 0.90, and higher than 3% percentage of total elongation.
As from being appreciated that steel band/plate 16,17 is for the manufacture of the intermediates in the method for the steel beam column of washing and thermoforming above with in accompanying drawing.Therefore, the performance of steel band/plate 16,17 and crystalline-granular texture are not objects of the present invention, but the novel method of the object as the performance of the steel beam column reached about washing and thermoforming.
Preferably, the hardenable steel alloy that strip product is made up of it comprises below with regard to weight percent:
Surplus is iron and inevitable impurity.
Particularly when comprising the hot dip process step 4.1 of preliminary heat treatment step 13 and/or 14, with regard to quality or weight percent, the microalloy belonging to one or more alloying elements of the group be made up of titanium (Ti), vanadium (V), niobium (Nb) of 0.01-0.1% is preferred, this is because microalloy is by improving recrystallization temperature T
rx, in the process of carrying out preliminary heat treated optional step 13 and/or 14, prevent recrystallize.In addition, they also hinder austenite (γ) grain growing in step 6, step 11 and step 7 process.Therefore, microalloy element is used to be highly preferred when hot dip process.
Next, the reason of brief description hardenable steel alloy given above.Carbon C is the fundamental element increasing steel hardenability, and it mainly determines the hardness of steel after brinelling and tensile strength.Therefore, the carbon of at least 0.08% is preferred, and the preferred lower limit of carbon is 0.15%.But if carbon is more than 0.45%, weldability will weaken too much.Therefore, preferably, the upper limit of carbon is 0.3%.Manganese Mn and chromium Cr increases hardenability very effective element, and preferably use them thus its total amount in the scope of 0.5-3.5%.But too high content may weaken ductility, therefore, more preferably, Mn and Cr total amount is in the scope of 0.8-2.0%.Silicon Si is also the element increasing hardenability.In addition, it can use as reductor.But Si content is preferably limited in lower than 1%, because too high silicon will cause surface imperfection.Most preferably, silicon is made to become alloy in the scope of 0.05-0.5%.Aluminium can be made to become alloy up to 0.2%, but more preferably in scope 0.01-0.15% or 0.01-0.06%, become alloy, using as deoxidation agent.Can also use up to 1% nickel and copper Cu to increase hardenability, but its content more preferably respectively below 0.5% and 0.2% below, with avoid increase cost of alloy.Boron increases the effectively element of hardenability, and level of alloy is relatively low, up to 0.01%.By by within the scope of 0.0001-0.005%, boron alloyed within the scope of preferred 0.001-0.005%, very advantageously solves hardenability.In this case, the titanium Ti of 0.01-0.1% also must be made to become alloy and to form TiN to avoid boron and nitrogen.If make the Ti higher than the stoichiometry (i.e. Ti>3.4N) relative to nitrogen become alloy, excessive titanium also by forming TiC, can hinder the alligatoring of austenite (γ) crystal grain in step 11 third time annealing process.But, if do not make boron become alloy, then can not consider titanium or make the Ti up to 0.2% become alloy to increase the effect of precipitation.The niobium Nb up to 0.2% can be made to become alloy, but preferably in scope 0.005-0.1%, become alloy, more preferably in scope 0.01-0.08%, to improve recrystallization temperature (T
rx) and the grain-size that controls in austenitization.Niobium forms the nitride, carbonitride and/or the carbide that hinder recrystallize.Molybdenum Mo can also be made to become alloy up to 1%, to promote martensitic transformation and to improve recrystallization temperature.But, because Mo is relatively costly alloying element, its content is more preferably limited in up to 0.2%.The vanadium V up to 0.5% can be made to become alloy to increase hardenability.But from the angle of cost of alloy, the V up to 0.2% is preferred.Also it can be used as microalloy element with the content of 0.01-0.1%.Owing to being included in Calcium treatment possible in melting processing, in steel, calcium Ca can be comprised.Therefore, the Ca such as up to 0.01% or 0.0001-0.005% can be comprised.
Inevitable impurity can be such as nitrogen N, phosphorus P, sulphur S, oxygen O and REM (rare earth metal).Nitrogen N is that the microalloy element that can exist in steel is combined formation nitride and carbonitride, thus it can form the element of precipitation.The reason of the nitrogen of at least 0.001% content can be comprised in Here it is steel.But the nitrogen higher than 0.01% will make nitride alligatoring, therefore nitrogen content preferably should be limited in 0.001-0.01%.Phosphorus P is inevitably included in steel usually, and may be limited to 0.06%, because higher content may be harmful to ductility.The best upper limit of P is 0.02%.But excessive reduction P may be unfavorable economically, therefore can apply the lower limit of 0.005%.Therefore, P content can be 0.005-0.06%.Sulphur S is inevitably included in steel usually, and may be limited to the content lower than 0.02%, preferably lower than 0.01% content.But excessive desulfurization may be unfavorable economically, the lower limit of 0.0001% therefore can be applied.Therefore, S content can be 0.0001-0.02%.Also may reside in steel as inevitable elemental oxygen O, but may be limited to lower than 0.005%, more preferably lower than 0.002%.This is because it can exist as the inclusion that may weaken performance.Make REM preferably more than typical inevitable content.
Hardenable steel alloy can also mean quench index (quenchingindex) DI of steel
inch(DI
inch) be equal to or higher than 3, as calculated by known formula formula obtainable in ASTMA255-67.
Metallic coating mentioned Anywhere in this specification sheets and claim relates to metal and metal alloy coating.Similarly, zinc base coat relates to zinc and Zinc alloy coated, its have in metallic coating with regard to weight percent higher than 50% Zn.
Zinc base coat is preferably according to the metallic coating of metal coated steel strip product of the present invention as being appreciated that by the previous section of this specification sheets.In other words, steel band is zinc-plated.More preferably, steel band is galvanizing.
Owing to carrying out the second preliminary heat treated step 14 comprising the annealing of step 9 second time, in the metallic coating of steel band, the pre-alloyed of iron can be there is.This means that the iron in steel band diffuses into metallic coating, thus form the metallic coating compound of dissimilar iron alloy, intermetallic compound and/or sosoloid.Such as, Fe-Zn compound, Fe-Zn intermetallic compound and/or Fe-Zn sosoloid, can be formed as coating owing to comprising the step 14 of step 9.
Therefore, according to preferred embodiment, the metallic coating of steel band is the metallic coating of iron alloy, more preferably galvannealed coating (ironalloyedzinccoating), such as alloying galvanizing coating.This means that the metallic coating (alloying galvanizing coating) of the strip product according to this embodiment can comprise except Zn, the Fe of the 5-50% with regard to weight percent.Iron zinc (pre--) alloy coat provides the possibility of shortening heat shaping middle heating period, thus facilitates the realization of effect of the present invention.
In other embodiments, the metallic coating of steel band is aluminium or aluminium-magnesium-zinc alloy coating.This means can comprise except Zn according to the metallic coating of the strip product of this embodiment, the Al of the 1-20% with regard to weight percent and the Mg of optional 1-5%.
In another embodiment, the metallic coating of steel band is electrolytic coating, comprises the Fe lower than 2% with regard to quality or weight percent, the Al lower than 1% and the Zn higher than 97%.
It is evident that to those skilled in the art, along with technical development, the present invention's design can realize in every way.The present invention and embodiment thereof are not limited to above-described embodiment, but can change within the scope of the claims.
Claims (23)
1., for the manufacture of washing and a method for the steel beam column of thermoforming, wherein, described method is to comprise the following steps to definite sequence:
Step 1, for providing the steel band be made up of hardenable steel alloy, and
Step 2, for cold rolling described steel band to obtain the cold-rolled steel strip with the deformed grains structure comprising non-recrystallization crystal grain, and
Step 4, for metallic coating being applied to the surface of described cold-rolled steel strip, still there is the deformed grains structure (10.1,10.2,10.3) that comprises non-recrystallization crystal grain and the metal coated steel strip product (16) of yield ratio (YS/TS) had higher than 0.75 to obtain, and
Step 5, for from described metal coated steel strip product stamping-out steel plate (17), and
Step 6, for being heated above A by described steel plate (17)
c1, preferably higher than A
c3temperature, and
Step 7, for by heating described steel plate (17) thermoforming with obtains shaping steel beam column, and
Step 8, for cooling the steel beam column of described shaping.
2. according to claim 1 for the manufacture of washing and the method for the steel beam column of thermoforming, wherein, described method also comprises carries out the first preliminary heat treated step 13 to described cold-rolled steel strip, described step 13 after step 2 and carried out before step 4, and carries out described step 13 to make the top temperature (T in this step 13 process
max) lower than the described recrystallization temperature (T comprising the deformed grains structure (10.1,10.2) of non-recrystallization crystal grain
rx), in other words, T
max<T
rx.
3. according to claim 2 for the manufacture of washing and the method for the steel beam column of thermoforming, wherein, carry out described step 4 by hot dip process in the bath of metallizing (4.1) described steel band.
4. according to claim 3 for the manufacture of washing and the method for the steel beam column of thermoforming, wherein, described step 13 comprises the following steps:
Step 3, for being heated above temperature T by described cold-rolled steel strip
bathtemperature (the T of-100 DEG C
hot-dip), T
baththe temperature of metallizing in hot dipping plating bath, and at this (T
hot-dip) temperature carries out for hot dip process step 4.1.
5. according to claim 3 for the manufacture of washing and the method for the steel beam column of thermoforming, wherein, described step 13 is to comprise the following steps to definite sequence:
Step 3, for being heated to the first annealing temperature (T by described cold-rolled steel strip
max1), and
Step 3.1, at 420 DEG C to the temperature (T within the scope of 800 DEG C
max1), more preferably lower than A
c1temperature control once anneal, and
Step 15, for being cooled to described steel band higher than temperature T
bathtemperature (the T of-100 DEG C
hot-dip), T
baththe temperature of metallizing in hot dipping plating bath, and at this (T
hot-dip) temperature carries out for hot dip process step 4.1.
6. according in any one of the preceding claims wherein for the manufacture of washing and the method for the steel beam column of thermoforming, wherein, in 3 minutes that calculate from the described step 6 for heating, i.e. t
heat≤ 3 minutes, start the described step 7 for thermoforming.
7. according in any one of the preceding claims wherein for the manufacture of washing and the method for the steel beam column of thermoforming, wherein, average heating rate in described step 6 process is higher than 20 DEG C/s, and preferably higher than 30 DEG C/s, and described heating is such as undertaken by induction heating equipment.
8. according to aforementioned claim 1 to 7, especially according to any one of claim 6-7 for the manufacture of washing and the method for the steel beam column of thermoforming, wherein, described method is also included in after step 4 and for carrying out the second preliminary heat treated step 14 before step 6, described step 14 is included in the recrystallization temperature (T lower than the deformed grains structure comprising non-recrystallization crystal grain (10.1,10.2,10.3)
rx) temperature (T
max2), the temperature such as in the scope of 450 to 600 DEG C, in other words, T
max2<T
rx, for the step 9 of second time annealing.
9. according in any one of the preceding claims wherein for the manufacture of washing and the method for the steel beam column of thermoforming, wherein, the described step 8 for cooling the steel beam column of described shaping is carried out to be enough to induce the rate of cooling that is at least part of, that preferably quench completely of the steel beam column of described shaping.
10. according in any one of the preceding claims wherein for the manufacture of washing and the method for the steel beam column of thermoforming, wherein, described step 7 for thermoforming is carried out in the mould of shaped device, and carries out in the mold for the described step 8 cooled.
11. according in any one of the preceding claims wherein for the manufacture of washing and the method for the steel beam column of thermoforming, wherein, described metallic coating is zinc base coat.
12. according in any one of the preceding claims wherein for the manufacture of washing and the method for the steel beam column of thermoforming, wherein, according to weight percent, described hardenable steel alloy comprises following:
Surplus is iron and inevitable impurity.
13. is according to claim 12 for the manufacture of washing and the method for the steel beam column of thermoforming, and wherein, according to weight percent, described hardenable alloy comprises further:
The microalloy with one or more alloying elements belonging to the group be made up of titanium (Ti), vanadium (V), niobium (Nb) of 0.01-0.1%.
14. is according to claim 13 for the manufacture of washing and the method for the steel beam column of thermoforming, and wherein, according to weight percent, described hardenable alloy comprises further:
The niobium (Nb) of 0.005-0.1%, the more preferably niobium (Nb) of 0.01-0.08%.
15. 1 kinds of metal coated steel strip products (16) for direct thermoforming be made up of hardenable Steel Alloy, wherein, the crystalline-granular texture of described steel band is the deformed grains structure (10.1,10.2,10.3) comprising non-recrystallization crystal grain, and the yield ratio of described strip product (YS/TS) is higher than 0.75.
The 16. metal coated steel strip products (16) for direct thermoforming according to claim 15, wherein, the yield ratio (YS/TS) of described strip product) higher than 0.80 and most preferably higher than 0.90.
17. metal coated steel strip products (16) for direct thermoforming according to claim 15 or 16, wherein, the yield strength (YS) of described strip product higher than 550MPa, preferably higher than 650MPa.
18. according to the metal coated steel strip product (16) for direct thermoforming in any one of the preceding claims wherein, wherein, according to volume percent, the described crystalline-granular texture of described metal coated steel strip comprises the non-recrystallization crystal grain higher than 70%, more preferably higher than 95% non-recrystallization crystal grain, most preferably, the described crystalline-granular texture of metal coated steel strip is complete non-recrystallization.
19. metal coated steel strip products (16) for direct thermoforming according to arbitrary aforementioned claim, wherein, according to weight percent, described hardenable steel alloy comprises following:
Surplus is iron and inevitable impurity.
The 20. metal coated steel strip products (16) for direct thermoforming according to claim 19, wherein, according to weight percent, described hardenable alloy comprises further:
The microalloy with one or more alloying elements belonging to the group be made up of titanium (Ti), vanadium (V), niobium (Nb) of 0.01-0.1%.
The 21. metal coated steel strip products (16) for direct thermoforming according to claim 20, wherein, according to weight percent, described hardenable alloy comprises further:
The niobium (Nb) of 0.005-0.1%, the more preferably niobium (Nb) of 0.01-0.08%.
22. metal coated steel strip products (16) for direct thermoforming according to arbitrary aforementioned claim, wherein, described metallic coating is zinc base coat.
The 23. metal coated steel strip products (16) for direct thermoforming according to claim 22, wherein, described metallic coating is galvannealed coating, such as alloying galvanizing coating.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| FI20135173A FI124825B (en) | 2013-02-22 | 2013-02-22 | Process for producing a metal-coated and hot-worked steel component and metal-coated steel strip product |
| FI20135173 | 2013-02-22 | ||
| PCT/IB2014/059153 WO2014128656A1 (en) | 2013-02-22 | 2014-02-21 | Method for manufacturing a metal coated and hot-formed steel component and a metal coated steel strip product |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN105143493A true CN105143493A (en) | 2015-12-09 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201480022812.4A Pending CN105143493A (en) | 2013-02-22 | 2014-02-21 | Method for manufacturing a metal coated and hot-formed steel component and a metal coated steel strip product |
Country Status (4)
| Country | Link |
|---|---|
| EP (1) | EP2959030A4 (en) |
| CN (1) | CN105143493A (en) |
| FI (1) | FI124825B (en) |
| WO (1) | WO2014128656A1 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111263830A (en) * | 2016-12-21 | 2020-06-09 | 安赛乐米塔尔公司 | Method for producing a coated steel sheet |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2019222950A1 (en) | 2018-05-24 | 2019-11-28 | GM Global Technology Operations LLC | A method for improving both strength and ductility of a press-hardening steel |
| WO2019241902A1 (en) | 2018-06-19 | 2019-12-26 | GM Global Technology Operations LLC | Low density press-hardening steel having enhanced mechanical properties |
| HUE063767T2 (en) * | 2018-12-18 | 2024-01-28 | Arcelormittal | A press hardened part with high resistance to delayed fracture and a manufacturing process thereof |
| US11530469B2 (en) * | 2019-07-02 | 2022-12-20 | GM Global Technology Operations LLC | Press hardened steel with surface layered homogenous oxide after hot forming |
Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH01127622A (en) * | 1987-11-10 | 1989-05-19 | Kawasaki Steel Corp | Production of high-tensile zinc hot dipped steel plate having excellent press bendability and shape characteristic |
| US5069981A (en) * | 1988-07-07 | 1991-12-03 | Sumitomo Metal Industries, Ltd. | Steel sheet dip-plated with a Zn-Al alloy and process for the manufacture thereof |
| JP2006274378A (en) * | 2005-03-30 | 2006-10-12 | Nippon Steel Corp | High yield ratio high strength cold rolled steel sheet, high yield ratio high strength hot dip galvanized steel sheet, high yield ratio high strength alloyed hot dip galvanized steel sheet, and method for producing them |
| JP2008156680A (en) * | 2006-12-21 | 2008-07-10 | Nippon Steel Corp | High-strength cold rolled steel sheet having high yield ratio, and its production method |
| JP2009274122A (en) * | 2008-05-16 | 2009-11-26 | Toyota Motor Corp | Press forming method and press formed product |
| WO2011154831A1 (en) * | 2010-06-07 | 2011-12-15 | Rautaruukki Oyj | Method for producing a hot-rolled steel product, and a hot-rolled steel |
| CA2814630A1 (en) * | 2010-10-22 | 2012-04-26 | Nippon Steel & Sumitomo Metal Corporation | Method for manufacturing hot stamped body and hot stamped body |
| CN102439179A (en) * | 2009-05-11 | 2012-05-02 | 罗奇钢铁公司 | Method for manufacturing hot rolled steel strip product, and hot rolled steel strip product |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| MX2013002063A (en) * | 2010-08-31 | 2013-04-05 | Tata Steel Ijmuiden Bv | Method for hot forming a coated metal part and formed part. |
-
2013
- 2013-02-22 FI FI20135173A patent/FI124825B/en not_active IP Right Cessation
-
2014
- 2014-02-21 EP EP14754753.3A patent/EP2959030A4/en not_active Withdrawn
- 2014-02-21 WO PCT/IB2014/059153 patent/WO2014128656A1/en active Application Filing
- 2014-02-21 CN CN201480022812.4A patent/CN105143493A/en active Pending
Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH01127622A (en) * | 1987-11-10 | 1989-05-19 | Kawasaki Steel Corp | Production of high-tensile zinc hot dipped steel plate having excellent press bendability and shape characteristic |
| US5069981A (en) * | 1988-07-07 | 1991-12-03 | Sumitomo Metal Industries, Ltd. | Steel sheet dip-plated with a Zn-Al alloy and process for the manufacture thereof |
| JP2006274378A (en) * | 2005-03-30 | 2006-10-12 | Nippon Steel Corp | High yield ratio high strength cold rolled steel sheet, high yield ratio high strength hot dip galvanized steel sheet, high yield ratio high strength alloyed hot dip galvanized steel sheet, and method for producing them |
| JP2008156680A (en) * | 2006-12-21 | 2008-07-10 | Nippon Steel Corp | High-strength cold rolled steel sheet having high yield ratio, and its production method |
| JP2009274122A (en) * | 2008-05-16 | 2009-11-26 | Toyota Motor Corp | Press forming method and press formed product |
| CN102439179A (en) * | 2009-05-11 | 2012-05-02 | 罗奇钢铁公司 | Method for manufacturing hot rolled steel strip product, and hot rolled steel strip product |
| WO2011154831A1 (en) * | 2010-06-07 | 2011-12-15 | Rautaruukki Oyj | Method for producing a hot-rolled steel product, and a hot-rolled steel |
| CA2814630A1 (en) * | 2010-10-22 | 2012-04-26 | Nippon Steel & Sumitomo Metal Corporation | Method for manufacturing hot stamped body and hot stamped body |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111263830A (en) * | 2016-12-21 | 2020-06-09 | 安赛乐米塔尔公司 | Method for producing a coated steel sheet |
Also Published As
| Publication number | Publication date |
|---|---|
| FI124825B (en) | 2015-02-13 |
| FI20135173A (en) | 2014-08-23 |
| WO2014128656A1 (en) | 2014-08-28 |
| EP2959030A1 (en) | 2015-12-30 |
| EP2959030A4 (en) | 2016-08-17 |
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