WO2008132303A1 - Acier pour formage a chaud ou trempe sous outil, a ductilite amelioree - Google Patents
Acier pour formage a chaud ou trempe sous outil, a ductilite amelioree Download PDFInfo
- Publication number
- WO2008132303A1 WO2008132303A1 PCT/FR2008/000278 FR2008000278W WO2008132303A1 WO 2008132303 A1 WO2008132303 A1 WO 2008132303A1 FR 2008000278 W FR2008000278 W FR 2008000278W WO 2008132303 A1 WO2008132303 A1 WO 2008132303A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- steel
- blank
- coating
- temperature
- hot
- Prior art date
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 73
- 239000010959 steel Substances 0.000 title claims abstract description 73
- 238000010791 quenching Methods 0.000 title description 7
- 230000000171 quenching effect Effects 0.000 title description 7
- 239000000203 mixture Substances 0.000 claims abstract description 28
- 238000004519 manufacturing process Methods 0.000 claims abstract description 22
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 16
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 14
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 9
- 229910052742 iron Inorganic materials 0.000 claims abstract description 8
- 229910001563 bainite Inorganic materials 0.000 claims abstract description 7
- 239000012535 impurity Substances 0.000 claims abstract description 7
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 7
- 229910052791 calcium Inorganic materials 0.000 claims abstract description 6
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 6
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 6
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 5
- 238000000576 coating method Methods 0.000 claims description 37
- 239000011248 coating agent Substances 0.000 claims description 36
- 238000001816 cooling Methods 0.000 claims description 29
- 229910045601 alloy Inorganic materials 0.000 claims description 26
- 239000000956 alloy Substances 0.000 claims description 26
- 229910052782 aluminium Inorganic materials 0.000 claims description 16
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 14
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 9
- 229910052725 zinc Inorganic materials 0.000 claims description 9
- 239000011701 zinc Substances 0.000 claims description 9
- 239000010960 cold rolled steel Substances 0.000 claims description 7
- 238000005275 alloying Methods 0.000 claims description 6
- 229910052710 silicon Inorganic materials 0.000 abstract description 13
- 229910052804 chromium Inorganic materials 0.000 abstract description 6
- 229910052802 copper Inorganic materials 0.000 abstract description 5
- 229910052757 nitrogen Inorganic materials 0.000 abstract description 5
- 238000010438 heat treatment Methods 0.000 description 27
- 239000010936 titanium Substances 0.000 description 11
- 229910052719 titanium Inorganic materials 0.000 description 9
- 238000003466 welding Methods 0.000 description 9
- 239000011572 manganese Substances 0.000 description 8
- 238000000034 method Methods 0.000 description 8
- 238000012360 testing method Methods 0.000 description 8
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 7
- 239000010955 niobium Substances 0.000 description 7
- 239000010703 silicon Substances 0.000 description 7
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 6
- 238000005260 corrosion Methods 0.000 description 6
- 230000007797 corrosion Effects 0.000 description 6
- 229910052748 manganese Inorganic materials 0.000 description 6
- 229910052799 carbon Inorganic materials 0.000 description 5
- 239000011651 chromium Substances 0.000 description 5
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 5
- 229910001566 austenite Inorganic materials 0.000 description 4
- 230000008901 benefit Effects 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 4
- 239000011575 calcium Substances 0.000 description 4
- 239000000470 constituent Substances 0.000 description 4
- 239000010949 copper Substances 0.000 description 4
- 238000005098 hot rolling Methods 0.000 description 4
- 229910052758 niobium Inorganic materials 0.000 description 4
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 4
- 239000002244 precipitate Substances 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 230000008569 process Effects 0.000 description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 3
- 230000008859 change Effects 0.000 description 3
- 238000005261 decarburization Methods 0.000 description 3
- 239000007788 liquid Substances 0.000 description 3
- 239000000758 substrate Substances 0.000 description 3
- 230000009466 transformation Effects 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 2
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 2
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 238000007598 dipping method Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 230000002787 reinforcement Effects 0.000 description 2
- 238000007493 shaping process Methods 0.000 description 2
- 230000035939 shock Effects 0.000 description 2
- 230000006641 stabilisation Effects 0.000 description 2
- 238000011105 stabilization Methods 0.000 description 2
- 239000011593 sulfur Substances 0.000 description 2
- 229910000838 Al alloy Inorganic materials 0.000 description 1
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 description 1
- 229910052684 Cerium 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
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- -1 TiN nitrides Chemical class 0.000 description 1
- 229910001297 Zn alloy Inorganic materials 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- 230000001464 adherent effect Effects 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 229910052787 antimony Inorganic materials 0.000 description 1
- WATWJIUSRGPENY-UHFFFAOYSA-N antimony atom Chemical compound [Sb] WATWJIUSRGPENY-UHFFFAOYSA-N 0.000 description 1
- 230000000712 assembly Effects 0.000 description 1
- 238000000429 assembly Methods 0.000 description 1
- 238000010923 batch production Methods 0.000 description 1
- 229910052797 bismuth Inorganic materials 0.000 description 1
- JCXGWMGPZLAOME-UHFFFAOYSA-N bismuth atom Chemical compound [Bi] JCXGWMGPZLAOME-UHFFFAOYSA-N 0.000 description 1
- ZMIGMASIKSOYAM-UHFFFAOYSA-N cerium Chemical compound [Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce][Ce] ZMIGMASIKSOYAM-UHFFFAOYSA-N 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 238000010924 continuous production Methods 0.000 description 1
- 239000002826 coolant Substances 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 238000000151 deposition Methods 0.000 description 1
- 230000008021 deposition Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000010891 electric arc Methods 0.000 description 1
- 238000004070 electrodeposition Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 101150034785 gamma gene Proteins 0.000 description 1
- 238000007542 hardness measurement Methods 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 229910052746 lanthanum Inorganic materials 0.000 description 1
- FZLIPJUXYLNCLC-UHFFFAOYSA-N lanthanum atom Chemical compound [La] FZLIPJUXYLNCLC-UHFFFAOYSA-N 0.000 description 1
- 238000012423 maintenance Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 239000004848 polyfunctional curative Substances 0.000 description 1
- 238000002203 pretreatment Methods 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 230000003014 reinforcing effect Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 230000003068 static effect Effects 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 150000003568 thioethers Chemical class 0.000 description 1
- 238000012546 transfer Methods 0.000 description 1
- 238000000844 transformation Methods 0.000 description 1
- 238000001771 vacuum deposition Methods 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
- B32B15/012—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of aluminium or an aluminium alloy
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
- B32B15/013—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of a metal other than iron or aluminium
-
- 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
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- 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
- 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
- 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
- C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips 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
- 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
- C21D8/0405—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 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
- C21D8/0478—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
- C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- 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
- C23C2/04—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
-
- 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
- C23C2/12—Aluminium or alloys based thereon
-
- 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
-
- 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
-
- 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
- C21D1/68—Temporary coatings or embedding materials applied before or during heat 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
- Y10T428/12736—Al-base component
- Y10T428/1275—Next to Group VIII or IB metal-base component
- Y10T428/12757—Fe
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
- Y10T428/12771—Transition metal-base component
- Y10T428/12785—Group IIB metal-base component
- Y10T428/12792—Zn-base component
- Y10T428/12799—Next to Fe-base component [e.g., galvanized]
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
- Y10T428/12771—Transition metal-base component
- Y10T428/12861—Group VIII or IB metal-base component
- Y10T428/12951—Fe-base component
- Y10T428/12972—Containing 0.01-1.7% carbon [i.e., steel]
Definitions
- the invention relates to the manufacture of hot-rolled or cold-rolled steel parts having, after hot forming or tool quenching, particularly favorable and homogeneous properties of resistance, elongation and corrosion resistance.
- steel parts combining high mechanical strength, high impact resistance and good corrosion resistance.
- This type of combination is particularly desirable in the automotive industry where significant vehicle lightening is sought.
- This can be achieved in particular by using steel parts with high mechanical properties whose microstructure is martensitic or bainito-martensitic: anti-intrusion parts, structural or participating in the safety of motor vehicles such as crossbars shocks, reinforcements door or foot, require for example the above qualities.
- the patent FR2780984 thus discloses an aluminum-coated steel sheet having a very high resistance after heat treatment, this treatment comprising heating between Ac 3 and 1200 ° C. and then hot forming within a tool.
- the elements of the composition of the steel are as follows: C: 0.15-0.5%, Mn: 0.5% -3%, Si: 0.1% -0.5%, Cr: 0, 0.1-1%, Ti ⁇ 0.2%, Al, P ⁇ 0.1%, S ⁇ 0.05%, B: 0.0005% -0.08%.
- the alloy compound formed by interdiffusion of pre-coating and steel during heat treatment provides protection against decarburization and corrosion.
- the implementation of a steel comprising 0.231% C, 1.15% Mn, 0.239% Si, 0.043% Al, 0.020% P, 0.0038% S, 0.179% Cr, 0.009% Cu. , 0.020% Ni, 0.032% Ti, 0.0042% N, 0.0051% Ca, 0.0028% B, makes it possible to obtain, after hot forming, a strength greater than 1500 MPa, associated with a totally martensitic structure . In return for this very high level of resistance, the elongation at break is relatively low after heat treatment, of the order of 5%. Some structural applications, however, do not require such a high level of resistance but require, on the other hand, a tensile elongation capacity greater than 15%.
- the present invention aims to solve the problems mentioned above. It aims in particular to provide hot-rolled or cold-rolled steel parts having, simultaneously after hot forming or tool quenching, a strength greater than 500 MPa, an elongation at break greater than 15%, for a range of thickness ranging from 0.5 to 4 mm.
- the invention also aims to provide parts with excellent homogeneity of structure and characteristics mechanical, that is to say whose resistance and elongation do not vary in the different parts of the parts, even if the rate of local deformation or local cooling rate is not uniform during manufacture.
- the invention also aims to provide readily weldable steel parts by the usual assembly processes (resistance welding, arc, LASER) welding parts that can be performed before or after hot forming or quenching under a tool.
- the subject of the invention is a steel part whose composition comprises, the contents being expressed by weight: 0.040% ⁇ C ⁇ 0.100%, 0.80% ⁇ Mn ⁇ 2.00%, Si ⁇ 0, 30%, S ⁇ 0.005%, P ⁇ 0.030%, 0.010% ⁇ Al ⁇ 0.070%, 0.015% ⁇ Nb ⁇ 0.100%, 0.030% ⁇ Ti ⁇ 0.080%, N ⁇ 0.009%, Cu ⁇ 0.100%, Ni ⁇ 0.100 %, Cr ⁇ 0.100%, Mo ⁇ 0.100%, Ca ⁇ 0.006%, the remainder of the composition consisting of iron and unavoidable impurities resulting from the elaboration, the microstructure of the steel consisting of at least 75 % equiaxed ferrite, martensite in an amount greater than or equal to 5% and less than or equal to 20%, and bainite in an amount of less than or equal to 10%
- the invention also relates to a steel part according to the characteristics below.
- the composition of the steel comprises, the contents being expressed by weight: 0.050% ⁇ C ⁇ 0.080%, 1, 20% ⁇ Mn ⁇ 1, 70%, Si ⁇ 0.070%, S ⁇ 0.004% , P ⁇ 0.020%, 0.020% ⁇ Al ⁇ 0.040%, 0.030% ⁇ Nb ⁇ 0.070%, 0.060% ⁇ Ti ⁇ 0.080%, N ⁇ 0.009%, Cu ⁇ 0.100%, Ni ⁇ 0.100%, Cr ⁇ 0.100%, Mo ⁇ 0.100%, Ca ⁇ 0.005%, the remainder of the composition being made of iron and unavoidable impurities resulting from the elaboration.
- the average ferritic grain size of the steel of the piece is less than 6 micrometers.
- the steel part is coated with an alloy layer over the entire thickness of this layer.
- This alloy layer results from at least one alloy heat treatment between the steel and a pre-coating, the latter being an alloy based on zinc or aluminum.
- the strength of the steel piece is greater or equal to 500 MPa and its elongation at break is greater than 15%.
- the invention also relates to a welded object of which at least one of the parts is a part according to any one of the above characteristics.
- the invention also relates to a method of manufacturing a coated steel part, comprising the steps of supplying a hot-rolled or cold-rolled steel sheet of the above composition, and then carrying out a pre-treatment. coating the sheet, the pre-coating being an alloy based on zinc or aluminum.
- the sheet is cut to obtain a blank and then possibly welded this blank.
- the blank is optionally deformed cold and then heated to a temperature TR in an oven so as to form, by alloying between the steel and the pre-coating, a layer alloyed with the surface of the blank, the alloying being carried out on the entire layer, and so as to confer a completely austenitic structure on the steel.
- the blank is removed from the oven and then optionally deformed hot to obtain a room which is cooled under conditions suitable for imparting the mechanical characteristics targeted for it.
- the subject of the invention is also a method for manufacturing a part, comprising the steps according to which a hot-rolled or cold-rolled steel sheet is supplied, of composition according to the preceding claim, and then cutting the sheet metal. to get a blank.
- the blank is optionally soldered and then this blank is optionally deformed in the cold state. This is heated to a temperature T R in an oven so as to give a completely austenitic structure to the steel and then the blank is removed from the oven. If necessary, a hot deformation is carried out to obtain a part, then this part is cooled under conditions suitable for imparting the mechanical characteristics targeted for it, and then a coating of the part is optionally carried out.
- the temperature T R is between 880 and 950 ° C. and the holding time t R at this temperature is between 3 and 10 minutes.
- the average cooling rate VR between the temperature T R and 400 0 C is between 30 and 80 ° C / s.
- the average cooling rate V R between the temperature T R and 400 0 C is preferably between 35 and 60 ° C / s.
- the invention also relates to the use of a part or object above, or manufactured according to one of the methods described above, for the manufacture of structural parts or safety for land vehicle to engine, for the field of agricultural machinery or shipbuilding.
- FIG. 1 shows the microstructure of a steel according to the invention after heat treatment
- FIG. 2 shows the microstructure of a steel not according to the invention, after heat treatment
- carbon plays an important role in the quenchability and mechanical strength obtained after cooling following the austenitization treatment. Below a content of 0.040% by weight, it is not possible to obtain a resistance greater than 500 MPa under all cooling conditions. Beyond a content of 0.100%, there is the risk of forming a too large proportion of martensite under the fastest cooling conditions, for example when the parts are held within a cooled tool. The elongation at break can then be less than 15%.
- a carbon content of between 0.050 and 0.080% makes it possible to obtain a high stability of the resistance and elongation characteristics as a function of the manufacturing conditions as well as a very good weldability in the usual assembly processes.
- manganese In addition to its role as a deoxidizer, manganese also has a significant effect on hardenability, especially when its weight content is at least 0.80%. Beyond 2.00%, its gammagene character however leads to the formation of a band structure too marked. A range of 1.20-1.70% Mn is preferred so as to obtain satisfactory quenchability without risk of segregation. In addition, one thus obtains a very good toughness in conditions of static or dynamic mechanical stressing.
- - Silicon contributes to the deoxidation of liquid steel and contributes to the hardening of steel. Its content must however be limited to avoid the excessive formation of surface oxides and to promote the coating and weldability. An addition of more than 0.30% by weight of silicon would lead to a possible stabilization of the austenite after cooling in the tool, which is not sought here. A silicon content of less than 0.070% is preferred to obtain the above results.
- aluminum allows deoxidation of the liquid steel.
- An amount preferably comprised between 0.020 and 0.040% makes it possible to avoid any stabilization of the austenite.
- Titanium and niobium belong to the category of micro-alloy elements, which are effective elements even for small amounts ranging from a few 3 to a few 10 -2 %:
- niobium content of the steel is between 0.015 and 0.100%
- fine carbonitride hardeners Nb (CN) precipitates form in the austenite or in the ferrite during hot rolling. These precipitates also make it possible to limit the growth of the austenitic grain during a possible welding.
- a niobium content between 0.030 and 0.070% makes it possible to obtain appreciable hardening while moderately increasing the mechanical characteristics at high temperature, which makes it possible to limit the forces during hot rolling on striped trains.
- titanium content When the titanium content is between 0.030 and 0.080% by weight, precipitation takes place in the form of TiN nitrides at very high temperature, then at a lower temperature in the austenite in the form of fine TiC carbides leading to hardening. TiN precipitates effectively limit the growth of the austenitic grain during any welding operations.
- a titanium content of between 0.060 and 0.080% makes it possible to obtain a more intense precipitation of TiC or of titanium carbosulfides. -
- the nitrogen content is less than 0.009% to avoid a precipitation of TiN which would occur as soon as the solidification in a coarse form.
- niobium and titanium are in precipitated form.
- a complete austenitization of the steel is subsequently carried out followed by quenching in a tooling.
- the inventors have demonstrated that the precipitates, in particular titanium, effectively slow down the growth of the austenitic grain during heating and limit the formation of secondary constituents of great hardness which reduce the ductility. This control of the size of the austenitic grain makes it possible to obtain a low sensitivity to the variation of the cooling rate.
- composition of the steel may also comprise elements such as copper, chromium, nickel or molybdenum which contribute to the increase of the resistance by hardening in solid solution or by their influence on the quenchability.
- elements such as copper, chromium, nickel or molybdenum which contribute to the increase of the resistance by hardening in solid solution or by their influence on the quenchability.
- their individual content must be limited to 0.1%, under penalty of forming bainitic structures after austenitization furnace, these structures being sensitive to a variation of the cooling rate.
- the steel may also comprise a calcium addition of up to 0.006%, and preferably 0.005%, for the purpose of globulizing the sulphides and improving the fatigue resistance.
- the manufacturing method according to the invention is as follows:
- micro-alloy elements are in precipitated form: we can for example manufacture the sheets and blanks by pouring liquid steel followed by heating at 1100 0 C. Hot rolling will be carried out with a temperature end of rolling lower than 940 0 C. Then will be cooled to 500- 700 0 C with a speed between 20 and 100 ° C / s. After cooling down with air, the sheet is then wound at a temperature between 450 and 680 ° C. These conditions make it possible to obtain a fine and dispersed precipitation of the micro-alloy elements.
- the invention can be implemented on a sheet or blank, bare or pre-coated.
- a pre-coating of the sheet is carried out, the pre-coating being an alloy based on zinc or aluminum.
- This pre-coating can in particular be carried out by a hot dipping, electrodeposition or vacuum deposition method.
- the deposition can be carried out in a single step or by combination of successive steps.
- the deposit is preferably carried out continuously.
- the thickness of this pre-coating can be between 5 and 35 micrometers in order to obtain a coating resistant to the conditions of implementation.
- the alloy of the pre-coating may be aluminum or an alloy based on aluminum: for example, the pre-coating may be carried out by hot quenching in an aluminum-based bath which also comprises 8 to 11%. by weight of silicon and 2 to 4% of iron.
- the pre-coating alloy may also be zinc or a zinc-based alloy.
- This zinc alloy may also contain aluminum, for example in an amount of up to 5% by weight.
- the zinc-based alloy may also optionally contain one or more elements such as silicon, lead, antimony, bismuth, lanthanum or cerium.
- the pre-coated sheet is then cut to obtain a flank of geometry in relation to that of the final piece to obtain.
- the blank pre-coated with other steel elements is optionally soldered. It is known that some applications do not require the same level of mechanical characteristics in every point of the parts. There has thus been a development of the patched blanks, which are assemblies from steel sheets possibly having different compositions or thicknesses.
- the pre-coated blank according to the invention can thus be incorporated by welding into a more complex assembly. The welding can be carried out by a continuous process, for example by LASER beam, by electric arc, or by a batch process such as, for example, spot resistance welding.
- the blank can be assembled to one or more other steel blanks the composition and the thickness may be identical or different, so as to obtain in the final stage parts whose mechanical characteristics, after shaping and heat treatment, vary within them and are locally adapted to the subsequent solicitations.
- the composition by weight of the blanks assembled with the blank according to the invention will comprise, for example: C: 0.040-0.25% C, 0.8-2% Mn, Si 0 0, 4%, AI ⁇ 0.1%.
- the pre-coated blank is optionally deformed in the cold state.
- This deformation can be carried out so as to be closer to a greater or lesser degree of the final geometry of the part that we want to obtain.
- it may be supplemented by deformation carried out hot, as will be discussed below.
- the piece is then heated and then undergoes a shaping step within a tool. This last step aims to avoid possible deformation of the parts to cooling and to ensure a particular cooling cycle through a suitable contact between the part and the tooling.
- This conformation step is therefore characterized by a minimum applied effort of the tooling on the part.
- the blank is heated in a heat treatment furnace.
- This treatment is intended to achieve a complete austenitization of steel.
- this treatment also aims to form a coating capable of protecting its surface during the treatment and during the subsequent use of the room.
- the role of the aluminum or zinc pre-coating is as follows: during furnace heating, an alloying reaction between the steel substrate and the pre-coating occurs and an alloy layer is formed on the surface of the flan. Alliation occurs over the entire thickness of the precoat. Depending on the composition of the pre-coating, one or more intermetallic phases are formed in this alloy layer. The melting temperature of these phases being greater than the temperature at which the part is carried, the coating does not melt at high temperature.
- pre-coating the alloy before heating, and "coating" the alloy layer formed during heating. The heat treatment therefore modifies the nature of the pre-coating and its geometry, since the thickness of the coating is greater than that of the pre-coating due to the diffusion reactions towards the steel substrate.
- the heat treatment forms a temperature-resistant layer.
- This layer protects the substrate by avoiding contact with the furnace atmosphere. Consequently, it avoids the problems of decarburization or oxidation that would occur if the heating was performed on a part without pre-coating.
- the formed coatings also have the advantage of being adherent and of being adapted to the possible hot forming operations which will follow.
- the heating is carried out at a temperature TR greater than Ac3, the latter temperature denoting the end of austenitic transformation temperature of the steel at heating.
- the temperature T R is preferably between 880 and 950 ° C.
- a hold t R of 3 to 10 minutes at TR can be carried out so as to homogenize the temperature of the blank.
- the heated blank is then removed from the furnace and transferred into a tool where it performs either a hot deformation to obtain the desired geometry for the part, or a simple conformation as described above. .
- a hot deformation to obtain the desired geometry for the part, or a simple conformation as described above.
- the blank has not been deformed beforehand, it is at the hot deformation stage that the deformation will be completely achieved.
- the presence of the part within the tooling leads to a cooling which intervenes essentially by thermal conduction.
- the cooling rate depends on parameters such as the transfer time between the furnace and the tooling, the thickness and the temperature of the part, the possible cooling of the tool itself by a coolant, the maintenance more or less length of the piece in the tooling.
- the part can be transferred to another tool, called "secondary" tooling that controls the end of the cooling cycle.
- V R this parameter designates the average cooling rate between the room temperature TR of the furnace outlet and the temperature of the furnace. 400 ° C. This temperature range between TR and 400 ° C. covers a particular range where allotropic transformations leading to the desired microstructures for the steel compositions according to the invention take place.
- the speed V R is between 30 and 80 ° C / s: when V R is less than 30 ° C / s, the part structure is very predominantly ferritic and a resistance level greater than 500 MPa can not always be reached.
- the speed VR is between 35 and 60 ° C./s, the variability of the mechanical properties obtained is particularly small.
- the microstructure according to the invention consists of at least 75% of equiaxed fine ferrite, this percentage corresponding to the surface fraction which can be measured for example on a polished and etched cut.
- the equiaxed qualifier designates a structure whose average ratio between the greatest length of ferritic grains and the smallest length does not exceed 1, 2.
- the average ferritic grain size is less than 6 micrometers, so as simultaneously to obtain a high strength and an elongation at break much greater than 15%.
- the structure also comprises martensite, the surface fraction of which is between 5 and 20%.
- This constituent is in the form of islets dispersed within the ferritic matrix, the size of these islets being generally less than or equal to that of ferritic grains. In this fine and dispersed form, the presence of 5 to 20% of martensite makes it possible to increase the mechanical strength without reducing the ductility too much.
- the structure may also include bainite in a quantity limited to
- the formed parts thus obtained can then be optionally assembled by welding to other elements of identical or different thickness or composition, so as to constitute for example a more complex structure.
- the formed parts can naturally be coated after heat treatment with a suitable coating if requirements against corrosion are required for them.
- Hot-rolled or cold-rolled steel sheets having a thickness ranging from 1.2 to 2 mm, with the following weight composition:
- Table 1 Composition of the steel (% by weight) The underlined values indicate characteristics outside the invention
- Steels A and B are steels of composition according to the invention.
- Steels C and D are reference steels.
- Hot rolled steel sheet has a thickness of 2mm.
- Steel B was tested in the form of 2mm thick hot-rolled sheets, and 1.5mm and 1.2mm thick cold rolled and annealed sheets.
- Steels C and D are cold-rolled and annealed reference steels of 1.2 mm thickness.
- the sheets of these different steels were pre-coated by dipping in a molten bath of an aluminum alloy comprising 9.3% of silicon and 2.8% of iron, the remainder being made of aluminum and impurities. inevitable.
- the thickness of the precoat is about 25 microns per side. The sheets were then cut into blanks.
- the blanks were then heated to a temperature T R for a holding time t R indicated in Table 2.
- Some steels were subjected to several test conditions such as steel B under conditions marked B1 to B3. .
- the heating conditions all lead to a complete austenitic transformation of the steels.
- the pre-coating is transformed into an alloyed layer over its entire thickness.
- This alloy coating, high melting point and high hardness has a high resistance to corrosion and avoids oxidation and decarburization of the underlying steel base during and after the heating phase.
- microstructures obtained after heat treatment were examined on polished and etched sections.
- the average size of ferritic grain was determined by means of image analyzes.
- FIG. 1 An example of a microstructure is shown in FIG. 1.
- the structure, relative to test B1, is composed of 93% equiaxial ferrite having an average size of 5 micrometers, and 7% of martensite.
- Tests A1, A2, B1, B2 all lead to structures consisting of more than 75% equiaxed ferrite, martensite in an amount of between 5% and 20%, and less than 10% of bainite.
- a too high cooling rate (100 ° C./s, test B3) leads to a proportion of martensite slightly greater than 20%. Martensite is present in the form of islands may exceed 5 micrometers. The elongation is then less than 15%.
- Steel C contains too much carbon and silicon, and does not contain enough micro-alloy elements for effective grain control: even under cooling conditions of 35 ° C / s, It is not ferritic but mainly bainitic as illustrated in Figure 2 relating to test C1. The elongation is then less than 15%. When the cooling rate increases (tests C2 and C3), the structure becomes predominantly martensitic with traces of bainite. The lengthening undergoes a notable reduction.
- Steel D has an insufficient content of manganese and titanium and contains an excessive amount of sulfur. As a result, the resistance is insufficient, less than 500 MPa in the test condition D1.
- the elastic limit is between 430 and 475 MPa, the resistance between 580 and 650 MPa, the elongation at break between 17 and 22%.
- the steel and the method according to the invention are characterized by the fact that the properties remain very homogeneous within the same room. In particular, the resistance and elongation at break remain greater than 500 MPa and 15% respectively, whatever the rate of deformation considered.
- the invention thus allows the manufacture of coated parts with high characteristics of strength and ductility, having these characteristics homogeneously in all the rooms.
- the steels according to the invention are not very sensitive to a modification of the manufacturing parameters, which presents an advantage in the event of unexpected waiting on the production line, or in case of a change of manufacture (pieces of different thickness passing successively within the same oven for example).
- These parts will be used profitably for the manufacture of safety parts, including structural parts or reinforcement, for the construction of motor vehicles, and in the field of agricultural machinery or shipbuilding.
Abstract
Description
Claims
Priority Applications (16)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
ES08775621T ES2387229T3 (es) | 2007-03-14 | 2008-03-03 | Acero para la formación en caliente o al temple bajo herramienta, con ductilidad mejorada |
PL08775621T PL2137327T3 (pl) | 2007-03-14 | 2008-03-03 | Stal do obróbki na gorąco lub hartowania w tłoczniku, o ulepszonej ciągliwości |
BRPI0809006-8A BRPI0809006B1 (pt) | 2007-03-14 | 2008-03-03 | "part obtained by deformation and cooling on a tool and processes for production of a part". |
CN2008800078916A CN101631880B (zh) | 2007-03-14 | 2008-03-03 | 用于在工具中热成形或淬火的具有改善的延展性的钢 |
JP2009553176A JP5726419B2 (ja) | 2007-03-14 | 2008-03-03 | 延性が改善された装置レス熱間成形または焼入れ用鋼 |
KR1020187032044A KR102008641B1 (ko) | 2007-03-14 | 2008-03-03 | 개선된 연성을 갖는 툴리스 열간 성형 또는 급냉용 강 |
US12/530,791 US8722203B2 (en) | 2007-03-14 | 2008-03-03 | Steel, for hot forming or quenching in a tool, having improved ductility |
EP08775621A EP2137327B1 (fr) | 2007-03-14 | 2008-03-03 | Acier pour formage a chaud ou trempe sous outil, a ductilite amelioree |
CA2680623A CA2680623C (fr) | 2007-03-14 | 2008-03-03 | Acier pour formage a chaud ou trempe sous outil, a ductilite amelioree |
KR1020197022301A KR20190091571A (ko) | 2007-03-14 | 2008-03-03 | 개선된 연성을 갖는 툴리스 열간 성형 또는 급냉용 강 |
KR1020177008499A KR101952525B1 (ko) | 2007-03-14 | 2008-03-03 | 개선된 연성을 갖는 툴리스 열간 성형 또는 급냉용 강 |
MX2009009769A MX2009009769A (es) | 2007-03-14 | 2008-03-03 | Acero para formacion en caliente o enfriamiento en una herramienta, que tiene ductilidad mejorada. |
KR1020157010080A KR20150048913A (ko) | 2007-03-14 | 2008-03-03 | 개선된 연성을 갖는 툴리스 열간 성형 또는 급냉용 강 |
AT08775621T ATE556152T1 (de) | 2007-03-14 | 2008-03-03 | Stahl für werkzeugloses warmformen oder abschrecken mit erhöhter biegbarkeit |
MA32198A MA31235B1 (fr) | 2007-03-14 | 2009-09-02 | Acier pour formage a chaud ou trempe sous outil, a ductilite amelioree |
US14/249,902 US9611517B2 (en) | 2007-03-14 | 2014-04-10 | Process for manufacturing steel, for hot forming or quenching in a tool, having improved ductility |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
FRPCT/FR2007/000441 | 2007-03-14 | ||
PCT/FR2007/000441 WO2008110670A1 (fr) | 2007-03-14 | 2007-03-14 | Acier pour formage a chaud ou trempe sous outil a ductilite amelioree |
Related Child Applications (2)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US12/530,791 A-371-Of-International US8722203B2 (en) | 2007-03-14 | 2008-03-03 | Steel, for hot forming or quenching in a tool, having improved ductility |
US14/249,902 Continuation US9611517B2 (en) | 2007-03-14 | 2014-04-10 | Process for manufacturing steel, for hot forming or quenching in a tool, having improved ductility |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2008132303A1 true WO2008132303A1 (fr) | 2008-11-06 |
Family
ID=38799374
Family Applications (2)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/FR2007/000441 WO2008110670A1 (fr) | 2007-03-14 | 2007-03-14 | Acier pour formage a chaud ou trempe sous outil a ductilite amelioree |
PCT/FR2008/000278 WO2008132303A1 (fr) | 2007-03-14 | 2008-03-03 | Acier pour formage a chaud ou trempe sous outil, a ductilite amelioree |
Family Applications Before (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/FR2007/000441 WO2008110670A1 (fr) | 2007-03-14 | 2007-03-14 | Acier pour formage a chaud ou trempe sous outil a ductilite amelioree |
Country Status (17)
Country | Link |
---|---|
US (2) | US8722203B2 (fr) |
EP (1) | EP2137327B1 (fr) |
JP (1) | JP5726419B2 (fr) |
KR (5) | KR20190091571A (fr) |
CN (1) | CN101631880B (fr) |
AR (1) | AR065764A1 (fr) |
AT (1) | ATE556152T1 (fr) |
BR (1) | BRPI0809006B1 (fr) |
CA (1) | CA2680623C (fr) |
ES (1) | ES2387229T3 (fr) |
MA (1) | MA31235B1 (fr) |
MX (1) | MX2009009769A (fr) |
PL (1) | PL2137327T3 (fr) |
RU (1) | RU2423532C1 (fr) |
UA (1) | UA99127C2 (fr) |
WO (2) | WO2008110670A1 (fr) |
ZA (1) | ZA200905998B (fr) |
Cited By (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP2664682A1 (fr) | 2012-05-16 | 2013-11-20 | ThyssenKrupp Steel Europe AG | Acier destiné à la fabrication d'un composant en acier, produit plat en acier en étant constitué, composant en étant issu et leur procédé de fabrication |
KR20160078807A (ko) | 2014-12-24 | 2016-07-05 | 주식회사 포스코 | 연신율 및 충격 인성이 우수한 열간 프레스 부재 및 그 제조방법 |
KR20160114019A (ko) | 2016-09-21 | 2016-10-04 | 주식회사 포스코 | 연신율 및 충격 인성이 우수한 열간 프레스 부재 및 그 제조방법 |
WO2019069938A1 (fr) | 2017-10-02 | 2019-04-11 | 新日鐵住金株式会社 | Article moulé par estampage à chaud, tôle d'acier pour estampage à chaud, et procédés de production de ceux-ci |
WO2019102424A1 (fr) | 2017-11-24 | 2019-05-31 | Arcelormittal | Procédé de fabrication d'une ébauche en acier soudée à l'aide d'un fil d'apport présentant une teneur en carbone définie, ébauche soudée associée, procédé de fabrication d'une pièce soudée avec pièce en acier formée par pressage à chaud et refroidie et pièce associée |
KR20210117316A (ko) | 2019-04-01 | 2021-09-28 | 닛폰세이테츠 가부시키가이샤 | 핫 스탬프 성형품 및 그 제조 방법 |
KR20210124324A (ko) | 2019-04-01 | 2021-10-14 | 닛폰세이테츠 가부시키가이샤 | 핫 스탬프 성형품 및 핫 스탬프용 강판, 그리고 그것들의 제조 방법 |
US11319610B2 (en) | 2015-07-09 | 2022-05-03 | Arcelormittal | Steel for press hardening and press hardened part manufactured from such steel |
Families Citing this family (45)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP1767659A1 (fr) * | 2005-09-21 | 2007-03-28 | ARCELOR France | Procédé de fabrication d'une pièce en acier de microstructure multi-phasée |
DE102010004081C5 (de) * | 2010-01-06 | 2016-11-03 | Benteler Automobiltechnik Gmbh | Verfahren zum Warmformen und Härten einer Platine |
CN102230129A (zh) * | 2011-07-12 | 2011-11-02 | 内蒙古包钢钢联股份有限公司 | 一种含稀土高强度钢板及其热处理工艺 |
CN102251177A (zh) * | 2011-07-12 | 2011-11-23 | 内蒙古包钢钢联股份有限公司 | 一种含稀土高强度钢板及其轧制方法 |
WO2013014481A1 (fr) | 2011-07-26 | 2013-01-31 | Arcelormittal Investigación Y Desarrollo Sl | Pièce d'acier soudée préalablement mise en forme à chaud à très haute résistance mécanique et procédé de fabrication |
CN105648311B (zh) * | 2011-08-09 | 2018-03-30 | 新日铁住金株式会社 | 在低温下的冲击能吸收特性和耐haz软化特性优异的高屈服比热轧钢板 |
UA109963C2 (uk) * | 2011-09-06 | 2015-10-26 | Катана сталь, яка затвердіває внаслідок виділення часток після гарячого формування і/або загартовування в інструменті, яка має високу міцність і пластичність, та спосіб її виробництва | |
CN102367554A (zh) * | 2011-10-28 | 2012-03-07 | 内蒙古包钢钢联股份有限公司 | 一种工程机械用高性能调质钢板及其生产工艺 |
BR112014017020B1 (pt) | 2012-01-13 | 2020-04-14 | Nippon Steel & Sumitomo Metal Corp | chapa de aço laminada a frio e método para produzir chapa de aço laminada a frio |
ES2666968T3 (es) * | 2012-01-13 | 2018-05-08 | Nippon Steel & Sumitomo Metal Corporation | Artículo moldeado por estampado en caliente y método para producir un artículo moldeado por estampado en caliente |
CA2866466C (fr) * | 2012-03-28 | 2016-10-25 | Nippon Steel & Sumitomo Metal Corporation | Ebauche personnalisee pour un estampage a chaud, element estampe a chaud et procedes de production de ces derniers |
DE102012006941B4 (de) * | 2012-03-30 | 2013-10-17 | Salzgitter Flachstahl Gmbh | Verfahren zur Herstellung eines Bauteils aus Stahl durch Warmumformen |
CN102747295B (zh) * | 2012-07-27 | 2014-06-18 | 武汉钢铁(集团)公司 | 一种利用控轧控冷方法生产的贝氏体薄钢板及其制备方法 |
KR101448473B1 (ko) * | 2012-12-03 | 2014-10-10 | 현대하이스코 주식회사 | 테일러 웰디드 블랭크, 그 제조방법 및 이를 이용한 핫스탬핑 부품 |
CN103114292B (zh) * | 2013-02-18 | 2015-01-07 | 梅河口市弘业无缝钢管有限公司 | 激光熔敷多元共渗复合处理的油井管、生产工艺及装置 |
CN105074038B (zh) * | 2013-04-02 | 2016-12-14 | 新日铁住金株式会社 | 热冲压成型体、冷轧钢板以及热冲压成型体的制造方法 |
CZ2013281A3 (cs) * | 2013-04-22 | 2015-05-27 | Západočeská Univerzita V Plzni | Způsob výroby ocelových dílů |
DE202013011800U1 (de) | 2013-07-24 | 2014-10-27 | GM Global Technology Operations LLC (n. d. Gesetzen des Staates Delaware) | Linienverstärktes Kraftfahrzeugblech, insbesondere Karosserieblech |
MX2016006777A (es) * | 2013-11-29 | 2016-09-07 | Nippon Steel & Sumitomo Metal Corp | Componente de lamina de acero formada en caliente y metodo para producir el mismo asi como la lamina de acero para formacion en caliente. |
MX2016007799A (es) | 2013-12-20 | 2016-09-07 | Nippon Steel & Sumitomo Metal Corp | Miembro de lamina de acero prensada en caliente, y metodo para producir el mismo, y lamina de acero para prensado en caleinte. |
US20160326608A1 (en) | 2014-01-06 | 2016-11-10 | Nippon Steel & Sumitomo Metal Corporation | Hot-formed member and method of manufacturing same |
DE102014010661A1 (de) * | 2014-07-18 | 2016-01-21 | GM Global Technology Operations LLC (n. d. Ges. d. Staates Delaware) | Blech und Verfahren zu dessen Behandlung |
WO2016016676A1 (fr) | 2014-07-30 | 2016-02-04 | ArcelorMittal Investigación y Desarrollo, S.L. | Procédé de fabrication de tôles d'acier, pour durcissement sous presse, et pièces obtenues par ce procédé |
WO2016132165A1 (fr) * | 2015-02-19 | 2016-08-25 | Arcelormittal | Procede de fabrication d'une piece phosphatable a partir d'une tole revetue d'un revetement a base d'aluminium et d'un revetement de zinc |
BR112017020165A2 (pt) * | 2015-03-31 | 2018-06-05 | Nippon Steel & Sumitomo Metal Corporation | chapa de aço para estampagem a quente e método para produção de chapa de aço para estampagem a quente e corpo formado por estampagem a quente |
WO2017017485A1 (fr) | 2015-07-30 | 2017-02-02 | Arcelormittal | Procédé de fabrication d'une pièce phosphatable à partir d'une tôle d'acier revêtue d'un revêtement métallique à base d'aluminium |
WO2017017484A1 (fr) * | 2015-07-30 | 2017-02-02 | Arcelormittal | Procédé pour la fabrication d'une pièce durcie qui ne présente pas de problèmes lme (liquide metal embrittlement - fragilité par les métaux liquides) |
WO2017017483A1 (fr) | 2015-07-30 | 2017-02-02 | Arcelormittal | Tôle d'acier revêtue d'un revêtement métallique à base d'aluminium |
DE102015014490A1 (de) | 2015-11-10 | 2017-05-11 | GM Global Technology Operations LLC (n. d. Ges. d. Staates Delaware) | Verfahren zur Verarbeitung eines Blechwerkstücks |
WO2017187215A1 (fr) * | 2016-04-29 | 2017-11-02 | Arcelormittal | Feuille d'acier ordinaire enduite d'un revêtement protecteur |
JP6424195B2 (ja) * | 2016-11-14 | 2018-11-14 | 株式会社豊田中央研究所 | 熱間プレス成形方法 |
WO2018096387A1 (fr) | 2016-11-24 | 2018-05-31 | Arcelormittal | Tôle d'acier laminé à chaud et revêtu pour estampage à chaud, pièce d'acier revêtu estampé à chaud, et ses procédés de fabrication |
CN107190203B (zh) * | 2017-05-31 | 2019-07-23 | 武汉钢铁有限公司 | 用薄板坯直接轧制的屈服强度≥800MPa热轧薄板及生产方法 |
WO2018220430A1 (fr) | 2017-06-02 | 2018-12-06 | Arcelormittal | Tôle d'acier destinée à la fabrication de pièces trempées à la presse, pièce trempée à la presse présentant une association de résistance élevée et de ductilité d'impact, et procédés de fabrication de cette dernière |
MX2020004596A (es) * | 2017-11-02 | 2020-08-06 | Ak Steel Properties Inc | Acero templado en prensa con propiedades personalizadas despues de un tratamiento termico novedoso. |
DE102017131247A1 (de) | 2017-12-22 | 2019-06-27 | Voestalpine Stahl Gmbh | Verfahren zum Erzeugen metallischer Bauteile mit angepassten Bauteileigenschaften |
DE102017131253A1 (de) | 2017-12-22 | 2019-06-27 | Voestalpine Stahl Gmbh | Verfahren zum Erzeugen metallischer Bauteile mit angepassten Bauteileigenschaften |
WO2019166852A1 (fr) | 2018-02-27 | 2019-09-06 | Arcelormittal | Procédé de production d'une pièce en acier soudée au laser durcie à la presse et pièce en acier soudée au laser durcie à la presse |
DE102018133143A1 (de) * | 2018-11-06 | 2020-05-07 | Salzgitter Flachstahl Gmbh | Innenhochdruck umgeformtes Bauteil aus Stahl und Verwendung eines Stahls für Vorprodukte zur Herstellung eines innenhochdruckumgeformten Bauteiles sowie Vorprodukt hierfür |
CN109821951B (zh) | 2018-12-06 | 2020-07-21 | 苏州普热斯勒先进成型技术有限公司 | 一种耐腐蚀热冲压零件的制备方法及装置 |
JP7235621B2 (ja) | 2019-08-27 | 2023-03-08 | 株式会社神戸製鋼所 | 低強度ホットスタンプ用鋼板、ホットスタンプ部品およびホットスタンプ部品の製造方法 |
WO2021125577A1 (fr) | 2019-12-20 | 2021-06-24 | 현대제철 주식회사 | Composant estampé à chaud et procédé de fabrication associé |
CN114981461B (zh) | 2020-01-16 | 2024-03-01 | 日本制铁株式会社 | 热冲压成形体 |
CN112301276B (zh) * | 2020-10-12 | 2021-10-22 | 马鞍山钢铁股份有限公司 | 一种高强、高耐候冷轧双相耐候钢的制作方法 |
CN112962021B (zh) * | 2021-01-25 | 2022-06-10 | 唐山钢铁集团有限责任公司 | 激光拼焊后用于整体热冲压成形的强塑钢板及生产方法 |
Citations (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP1013785A1 (fr) * | 1998-12-24 | 2000-06-28 | Sollac | Procédé de réalisation d'une pièce à partir d'une bande de tôle d'acier laminée et notamment laminée à chaud |
EP1143029A1 (fr) * | 2000-04-07 | 2001-10-10 | Usinor | Procédé de réalisation d'une pièce à très hautes caractéristiques mécanique, mise en forme par emboutissage, à partir d'une bande de tôle d'acier laminée et notamment laminée à chaud et revêtue |
EP1146132A1 (fr) * | 1999-10-22 | 2001-10-17 | Kawasaki Steel Corporation | Tole d'acier galvanisee par immersion a chaud presentant de bonnes qualites de resistance, de formabilite et de galvanisation |
EP1195447A1 (fr) * | 2000-04-07 | 2002-04-10 | Kawasaki Steel Corporation | Tole d'acier laminee a chaud, tole d'acier laminee a froid et tole d'acier galvanisee par immersion a chaud ayant d'excellentes caracteristiques de durcissement au vieillissement par ecrouissage, et procede pour leur production |
FR2833504A1 (fr) * | 2001-12-14 | 2003-06-20 | Usinor | Procede de mise en forme a chaud et notamment l'obtention de tout ou partie d'une roue de vehicule automobile |
FR2883007A1 (fr) * | 2005-03-11 | 2006-09-15 | Usinor Sa | Procede de fabrication d'une piece d'acier revetu presentant une tres haute resistance apres traitement thermique |
Family Cites Families (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP3698046B2 (ja) * | 1999-10-22 | 2005-09-21 | Jfeスチール株式会社 | 加工性およびめっき性に優れた高強度溶融亜鉛めっき鋼板ならびにその製造方法 |
EP1193322B1 (fr) * | 2000-02-29 | 2006-07-05 | JFE Steel Corporation | Tole d'acier laminee a froid a haute resistance presentant d'excellentes proprietes de durcissement par vieillissement par l'ecrouissage |
JP4333940B2 (ja) * | 2001-08-31 | 2009-09-16 | 新日本製鐵株式会社 | アルミ系めっき鋼板を用いた高強度自動車部材の熱間プレス方法 |
CN100434564C (zh) * | 2001-10-23 | 2008-11-19 | 住友金属工业株式会社 | 热压成型方法,其电镀钢材及其制备方法 |
KR100467487B1 (ko) * | 2001-10-26 | 2005-01-24 | 현대자동차주식회사 | 자동차용 강판의 강성강화 방법 및 그 성형품 |
JP4400079B2 (ja) * | 2002-03-29 | 2010-01-20 | Jfeスチール株式会社 | 超微細粒組織を有する冷延鋼板の製造方法 |
JP4168750B2 (ja) * | 2002-12-27 | 2008-10-22 | Jfeスチール株式会社 | 超微細粒組織を有し疲労特性に優れる溶融亜鉛めっき冷延鋼板の製造方法 |
JP4506434B2 (ja) * | 2004-11-29 | 2010-07-21 | Jfeスチール株式会社 | 剛性に優れた高強度鋼板およびその製造方法 |
KR100676935B1 (ko) * | 2005-06-25 | 2007-02-02 | 신닛뽄세이테쯔 카부시키카이샤 | 가공성이 우수한 고강도 합금화 용융 아연 도금 강판 및 그제조 방법 |
CN102242306B (zh) * | 2005-08-03 | 2013-03-27 | 住友金属工业株式会社 | 热轧钢板及冷轧钢板及它们的制造方法 |
-
2007
- 2007-03-14 WO PCT/FR2007/000441 patent/WO2008110670A1/fr active Application Filing
-
2008
- 2008-03-03 UA UAA200910344A patent/UA99127C2/ru unknown
- 2008-03-03 EP EP08775621A patent/EP2137327B1/fr active Active
- 2008-03-03 KR KR1020197022301A patent/KR20190091571A/ko not_active Application Discontinuation
- 2008-03-03 MX MX2009009769A patent/MX2009009769A/es active IP Right Grant
- 2008-03-03 AT AT08775621T patent/ATE556152T1/de active
- 2008-03-03 BR BRPI0809006-8A patent/BRPI0809006B1/pt active IP Right Grant
- 2008-03-03 JP JP2009553176A patent/JP5726419B2/ja active Active
- 2008-03-03 RU RU2009137930/02A patent/RU2423532C1/ru active
- 2008-03-03 CA CA2680623A patent/CA2680623C/fr active Active
- 2008-03-03 WO PCT/FR2008/000278 patent/WO2008132303A1/fr active Application Filing
- 2008-03-03 KR KR1020177008499A patent/KR101952525B1/ko active IP Right Grant
- 2008-03-03 KR KR1020157010080A patent/KR20150048913A/ko active Application Filing
- 2008-03-03 US US12/530,791 patent/US8722203B2/en active Active
- 2008-03-03 KR KR1020097019061A patent/KR20090128414A/ko not_active Application Discontinuation
- 2008-03-03 KR KR1020187032044A patent/KR102008641B1/ko active IP Right Grant
- 2008-03-03 CN CN2008800078916A patent/CN101631880B/zh active Active
- 2008-03-03 ES ES08775621T patent/ES2387229T3/es active Active
- 2008-03-03 PL PL08775621T patent/PL2137327T3/pl unknown
- 2008-03-14 AR ARP080101077A patent/AR065764A1/es active IP Right Grant
-
2009
- 2009-08-27 ZA ZA200905998A patent/ZA200905998B/xx unknown
- 2009-09-02 MA MA32198A patent/MA31235B1/fr unknown
-
2014
- 2014-04-10 US US14/249,902 patent/US9611517B2/en active Active
Patent Citations (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP1013785A1 (fr) * | 1998-12-24 | 2000-06-28 | Sollac | Procédé de réalisation d'une pièce à partir d'une bande de tôle d'acier laminée et notamment laminée à chaud |
EP1146132A1 (fr) * | 1999-10-22 | 2001-10-17 | Kawasaki Steel Corporation | Tole d'acier galvanisee par immersion a chaud presentant de bonnes qualites de resistance, de formabilite et de galvanisation |
EP1143029A1 (fr) * | 2000-04-07 | 2001-10-10 | Usinor | Procédé de réalisation d'une pièce à très hautes caractéristiques mécanique, mise en forme par emboutissage, à partir d'une bande de tôle d'acier laminée et notamment laminée à chaud et revêtue |
EP1195447A1 (fr) * | 2000-04-07 | 2002-04-10 | Kawasaki Steel Corporation | Tole d'acier laminee a chaud, tole d'acier laminee a froid et tole d'acier galvanisee par immersion a chaud ayant d'excellentes caracteristiques de durcissement au vieillissement par ecrouissage, et procede pour leur production |
FR2833504A1 (fr) * | 2001-12-14 | 2003-06-20 | Usinor | Procede de mise en forme a chaud et notamment l'obtention de tout ou partie d'une roue de vehicule automobile |
FR2883007A1 (fr) * | 2005-03-11 | 2006-09-15 | Usinor Sa | Procede de fabrication d'une piece d'acier revetu presentant une tres haute resistance apres traitement thermique |
WO2006097593A1 (fr) * | 2005-03-11 | 2006-09-21 | Arcelor France | Procede de fabrication d'une piece d'acier revetu presentant une tres haute resistance apres traitement thermique |
Cited By (11)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP2664682A1 (fr) | 2012-05-16 | 2013-11-20 | ThyssenKrupp Steel Europe AG | Acier destiné à la fabrication d'un composant en acier, produit plat en acier en étant constitué, composant en étant issu et leur procédé de fabrication |
KR20160078807A (ko) | 2014-12-24 | 2016-07-05 | 주식회사 포스코 | 연신율 및 충격 인성이 우수한 열간 프레스 부재 및 그 제조방법 |
US11319610B2 (en) | 2015-07-09 | 2022-05-03 | Arcelormittal | Steel for press hardening and press hardened part manufactured from such steel |
KR20160114019A (ko) | 2016-09-21 | 2016-10-04 | 주식회사 포스코 | 연신율 및 충격 인성이 우수한 열간 프레스 부재 및 그 제조방법 |
WO2019069938A1 (fr) | 2017-10-02 | 2019-04-11 | 新日鐵住金株式会社 | Article moulé par estampage à chaud, tôle d'acier pour estampage à chaud, et procédés de production de ceux-ci |
KR20200047634A (ko) | 2017-10-02 | 2020-05-07 | 닛폰세이테츠 가부시키가이샤 | 핫 스탬프 성형품 및 핫 스탬프용 강판 그리고 그들의 제조 방법 |
US11565299B2 (en) | 2017-10-02 | 2023-01-31 | Nippon Steel Corporation | Hot stamped product, steel sheet for hot stamp, and manufacturing method thereof |
WO2019102424A1 (fr) | 2017-11-24 | 2019-05-31 | Arcelormittal | Procédé de fabrication d'une ébauche en acier soudée à l'aide d'un fil d'apport présentant une teneur en carbone définie, ébauche soudée associée, procédé de fabrication d'une pièce soudée avec pièce en acier formée par pressage à chaud et refroidie et pièce associée |
US11945503B2 (en) | 2017-11-24 | 2024-04-02 | Arcelormittal | Method for producing a welded steel blank and associated welded blank |
KR20210117316A (ko) | 2019-04-01 | 2021-09-28 | 닛폰세이테츠 가부시키가이샤 | 핫 스탬프 성형품 및 그 제조 방법 |
KR20210124324A (ko) | 2019-04-01 | 2021-10-14 | 닛폰세이테츠 가부시키가이샤 | 핫 스탬프 성형품 및 핫 스탬프용 강판, 그리고 그것들의 제조 방법 |
Also Published As
Publication number | Publication date |
---|---|
UA99127C2 (ru) | 2012-07-25 |
WO2008110670A1 (fr) | 2008-09-18 |
CN101631880B (zh) | 2012-07-04 |
US8722203B2 (en) | 2014-05-13 |
KR20190091571A (ko) | 2019-08-06 |
US20100221572A1 (en) | 2010-09-02 |
EP2137327A1 (fr) | 2009-12-30 |
ZA200905998B (en) | 2010-04-28 |
RU2009137930A (ru) | 2011-04-20 |
KR102008641B1 (ko) | 2019-08-07 |
MX2009009769A (es) | 2009-10-07 |
AR065764A1 (es) | 2009-07-01 |
ATE556152T1 (de) | 2012-05-15 |
JP2010521584A (ja) | 2010-06-24 |
PL2137327T3 (pl) | 2012-10-31 |
CN101631880A (zh) | 2010-01-20 |
ES2387229T3 (es) | 2012-09-18 |
RU2423532C1 (ru) | 2011-07-10 |
BRPI0809006A2 (pt) | 2014-09-16 |
MA31235B1 (fr) | 2010-03-01 |
KR20170038119A (ko) | 2017-04-05 |
KR20180122489A (ko) | 2018-11-12 |
BRPI0809006B1 (pt) | 2017-11-21 |
KR20150048913A (ko) | 2015-05-07 |
EP2137327B1 (fr) | 2012-05-02 |
JP5726419B2 (ja) | 2015-06-03 |
KR101952525B1 (ko) | 2019-02-26 |
US20140216612A1 (en) | 2014-08-07 |
CA2680623C (fr) | 2013-02-05 |
KR20090128414A (ko) | 2009-12-15 |
CA2680623A1 (fr) | 2008-11-06 |
US9611517B2 (en) | 2017-04-04 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
EP2137327B1 (fr) | Acier pour formage a chaud ou trempe sous outil, a ductilite amelioree | |
EP3783116B1 (fr) | Tôles prerevêtues permettant la fabrication de pieces d'acier revêtues et durcies a la presse | |
CN111492075B (zh) | 钢板、热浸镀锌钢板和合金化热浸镀锌钢板 | |
EP1929053B1 (fr) | Procede de fabrication d une piece en acier de microstructure multi-phasee | |
EP2171112B1 (fr) | Procede de fabrication de tôles d'acier a hautes caracteristiques de resistance et de ductilite, et tôles ainsi produites | |
EP1943368B1 (fr) | Procede de fabrication d'une piece a tres hautes caracteristiques mecaniques a partir d'une tole laminee et revetue | |
CA3071152C (fr) | Procede de fabrication de toles d'acier pour durcissement sous presse, et pieces obtenues par ce procede | |
US9481916B2 (en) | Method of thermomechanical shaping a final product with very high strength and a product produced thereby | |
WO2007118939A1 (fr) | Procede de fabrication d'une piece soudee a tres hautes caracteristiques mecaniques a partir d'une tole laminee et revetue | |
CA3065036C (fr) | Procede de fabrication de pieces d'acier a haute resistance mecanique et ductilite amelioree, et pieces obtenues par ce procede | |
EP2707513A1 (fr) | Procede de fabrication d'acier martensitique a tres haute resistance et tôle ou piece ainsi obtenue | |
EP2753723A1 (fr) | Acier lamine durcissant par precipitation apres formage a chaud et/ou trempe sous outil a tres haute resistance et ductilite et son procede de fabrication | |
WO2011104443A1 (fr) | Procédé de fabrication d'une pièce a partir d'une tôle revêtue d'aluminium ou d'alliage d'aluminium |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
WWE | Wipo information: entry into national phase |
Ref document number: 200880007891.6 Country of ref document: CN |
|
DPE2 | Request for preliminary examination filed before expiration of 19th month from priority date (pct application filed from 20040101) | ||
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 08775621 Country of ref document: EP Kind code of ref document: A1 |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2008775621 Country of ref document: EP |
|
ENP | Entry into the national phase |
Ref document number: 2680623 Country of ref document: CA |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2009553176 Country of ref document: JP Ref document number: 5359/CHENP/2009 Country of ref document: IN Ref document number: MX/A/2009/009769 Country of ref document: MX Ref document number: 1020097019061 Country of ref document: KR |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2009137930 Country of ref document: RU |
|
WWE | Wipo information: entry into national phase |
Ref document number: A200910344 Country of ref document: UA |
|
WWE | Wipo information: entry into national phase |
Ref document number: 12530791 Country of ref document: US |
|
ENP | Entry into the national phase |
Ref document number: PI0809006 Country of ref document: BR Kind code of ref document: A2 Effective date: 20090914 |
|
WWE | Wipo information: entry into national phase |
Ref document number: 1020157010080 Country of ref document: KR |