CN110892087A - 具有高可电阻点焊性的经锌涂覆的钢板 - Google Patents
具有高可电阻点焊性的经锌涂覆的钢板 Download PDFInfo
- Publication number
- CN110892087A CN110892087A CN201880037315.XA CN201880037315A CN110892087A CN 110892087 A CN110892087 A CN 110892087A CN 201880037315 A CN201880037315 A CN 201880037315A CN 110892087 A CN110892087 A CN 110892087A
- Authority
- CN
- China
- Prior art keywords
- equal
- steel
- percent
- zinc
- temperature
- 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.)
- Granted
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 173
- 239000010959 steel Substances 0.000 title claims abstract description 173
- 239000011701 zinc Substances 0.000 title claims abstract description 65
- 229910052725 zinc Inorganic materials 0.000 title claims abstract description 49
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 title claims abstract description 45
- 238000000576 coating method Methods 0.000 claims abstract description 47
- 239000011248 coating agent Substances 0.000 claims abstract description 46
- 239000000203 mixture Substances 0.000 claims abstract description 39
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 38
- 238000000034 method Methods 0.000 claims abstract description 36
- 229910001297 Zn alloy Inorganic materials 0.000 claims abstract description 35
- 239000012298 atmosphere Substances 0.000 claims abstract description 28
- 229910001338 liquidmetal Inorganic materials 0.000 claims abstract description 26
- 229910052760 oxygen Inorganic materials 0.000 claims abstract description 21
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims abstract description 20
- 229910052742 iron Inorganic materials 0.000 claims abstract description 20
- 238000004519 manufacturing process Methods 0.000 claims abstract description 19
- 239000001301 oxygen Substances 0.000 claims abstract description 19
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims abstract description 18
- 239000012535 impurity Substances 0.000 claims abstract description 16
- 238000002791 soaking Methods 0.000 claims abstract description 16
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 15
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Chemical compound O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims abstract description 14
- 229910052739 hydrogen Inorganic materials 0.000 claims abstract description 13
- 239000001257 hydrogen Substances 0.000 claims abstract description 13
- 239000010960 cold rolled steel Substances 0.000 claims abstract description 10
- UQSXHKLRYXJYBZ-UHFFFAOYSA-N Iron oxide Chemical compound [Fe]=O UQSXHKLRYXJYBZ-UHFFFAOYSA-N 0.000 claims abstract description 8
- 150000002431 hydrogen Chemical class 0.000 claims abstract description 8
- 238000003723 Smelting Methods 0.000 claims abstract description 4
- 239000012299 nitrogen atmosphere Substances 0.000 claims abstract description 4
- 238000003466 welding Methods 0.000 claims description 51
- 229910052710 silicon Inorganic materials 0.000 claims description 39
- 229910052799 carbon Inorganic materials 0.000 claims description 37
- 229910052748 manganese Inorganic materials 0.000 claims description 30
- 229910052782 aluminium Inorganic materials 0.000 claims description 27
- 229910052804 chromium Inorganic materials 0.000 claims description 22
- 229910001566 austenite Inorganic materials 0.000 claims description 19
- 238000002347 injection Methods 0.000 claims description 14
- 239000007924 injection Substances 0.000 claims description 14
- 239000000758 substrate Substances 0.000 claims description 13
- 238000001816 cooling Methods 0.000 claims description 9
- 238000010438 heat treatment Methods 0.000 claims description 9
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 8
- 229910000734 martensite Inorganic materials 0.000 claims description 8
- 230000000717 retained effect Effects 0.000 claims description 8
- 230000036961 partial effect Effects 0.000 claims description 6
- 238000009864 tensile test Methods 0.000 claims description 6
- 238000009713 electroplating Methods 0.000 claims description 5
- 230000008569 process Effects 0.000 claims description 5
- 229910001563 bainite Inorganic materials 0.000 claims description 4
- 238000003618 dip coating Methods 0.000 claims description 3
- 238000005259 measurement Methods 0.000 claims description 2
- 229910052698 phosphorus Inorganic materials 0.000 abstract description 6
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 abstract description 5
- 239000011572 manganese Substances 0.000 description 59
- 239000011651 chromium Substances 0.000 description 29
- 238000000137 annealing Methods 0.000 description 23
- 238000005336 cracking Methods 0.000 description 8
- 230000009466 transformation Effects 0.000 description 8
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 7
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 7
- 239000010703 silicon Substances 0.000 description 7
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 6
- 239000007788 liquid Substances 0.000 description 5
- 229910052796 boron Inorganic materials 0.000 description 4
- 239000010949 copper Substances 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 150000001247 metal acetylides Chemical class 0.000 description 4
- 229910052759 nickel Inorganic materials 0.000 description 4
- 229910052758 niobium Inorganic materials 0.000 description 4
- 239000010955 niobium Substances 0.000 description 4
- 238000007254 oxidation reaction Methods 0.000 description 4
- 238000012360 testing method Methods 0.000 description 4
- 239000010936 titanium Substances 0.000 description 4
- 229910052719 titanium Inorganic materials 0.000 description 4
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 3
- 230000008859 change Effects 0.000 description 3
- 238000005097 cold rolling Methods 0.000 description 3
- 229910052802 copper Inorganic materials 0.000 description 3
- 238000001336 glow discharge atomic emission spectroscopy Methods 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 230000004048 modification Effects 0.000 description 3
- 238000012986 modification Methods 0.000 description 3
- 229910052750 molybdenum Inorganic materials 0.000 description 3
- 230000003647 oxidation Effects 0.000 description 3
- 230000006641 stabilisation Effects 0.000 description 3
- 238000011105 stabilization Methods 0.000 description 3
- 229910052717 sulfur Inorganic materials 0.000 description 3
- 229910052720 vanadium Inorganic materials 0.000 description 3
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 2
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 2
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 2
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 2
- 238000005275 alloying Methods 0.000 description 2
- 239000004411 aluminium Substances 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 238000005246 galvanizing Methods 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 230000002829 reductive effect Effects 0.000 description 2
- 230000035945 sensitivity Effects 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- VEXZGXHMUGYJMC-UHFFFAOYSA-M Chloride anion Chemical compound [Cl-] VEXZGXHMUGYJMC-UHFFFAOYSA-M 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910003023 Mg-Al Inorganic materials 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- 238000010793 Steam injection (oil industry) Methods 0.000 description 1
- QAOWNCQODCNURD-UHFFFAOYSA-L Sulfate Chemical compound [O-]S([O-])(=O)=O QAOWNCQODCNURD-UHFFFAOYSA-L 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 239000011324 bead Substances 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 239000011247 coating layer Substances 0.000 description 1
- 229910052681 coesite Inorganic materials 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 229910052906 cristobalite Inorganic materials 0.000 description 1
- 238000005261 decarburization Methods 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000004925 denaturation Methods 0.000 description 1
- 230000036425 denaturation Effects 0.000 description 1
- 230000001419 dependent effect Effects 0.000 description 1
- 238000000151 deposition Methods 0.000 description 1
- 238000005137 deposition process Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000006073 displacement reaction Methods 0.000 description 1
- 238000004993 emission spectroscopy Methods 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 238000007373 indentation Methods 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 230000008595 infiltration Effects 0.000 description 1
- 238000001764 infiltration Methods 0.000 description 1
- 230000003993 interaction Effects 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 238000005304 joining Methods 0.000 description 1
- 239000010410 layer Substances 0.000 description 1
- 230000000670 limiting effect Effects 0.000 description 1
- 238000012886 linear function Methods 0.000 description 1
- 229910052749 magnesium Inorganic materials 0.000 description 1
- 239000011777 magnesium Substances 0.000 description 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 238000007747 plating Methods 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 230000001376 precipitating effect Effects 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000004881 precipitation hardening Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 150000003839 salts Chemical class 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000000377 silicon dioxide Substances 0.000 description 1
- 229910000679 solder Inorganic materials 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 229910001220 stainless steel Inorganic materials 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 229910052682 stishovite Inorganic materials 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 229910052905 tridymite Inorganic materials 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
- 238000007740 vapor deposition Methods 0.000 description 1
- -1 zinc-aluminium-magnesium Chemical compound 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/50—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for welded joints
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K11/00—Resistance welding; Severing by resistance heating
- B23K11/10—Spot welding; Stitch welding
- B23K11/11—Spot welding
-
- 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
- C23C2/02—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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K11/00—Resistance welding; Severing by resistance heating
- B23K11/10—Spot welding; Stitch welding
- B23K11/11—Spot welding
- B23K11/115—Spot welding by means of two electrodes placed opposite one another on both sides of the welded parts
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K11/00—Resistance welding; Severing by resistance heating
- B23K11/16—Resistance welding; Severing by resistance heating taking account of the properties of the material to be welded
- B23K11/163—Welding of coated materials
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K31/00—Processes relevant to this subclass, specially adapted for particular articles or purposes, but not covered by only one of the preceding main groups
- B23K31/12—Processes relevant to this subclass, specially adapted for particular articles or purposes, but not covered by only one of the preceding main groups relating to investigating the properties, e.g. the weldability, of materials
- B23K31/125—Weld quality monitoring
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K37/00—Auxiliary devices or processes, not specially adapted to a procedure covered by only one of the preceding main groups
- B23K37/04—Auxiliary devices or processes, not specially adapted to a procedure covered by only one of the preceding main groups for holding or positioning work
- B23K37/0408—Auxiliary devices or processes, not specially adapted to a procedure covered by only one of the preceding main groups for holding or positioning work for planar work
-
- 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
- C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
- C21D1/20—Isothermal quenching, e.g. bainitic hardening
-
- 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
- C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
- C21D1/22—Martempering
-
- 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
- C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
- C21D1/76—Adjusting the composition of the atmosphere
-
- 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
- C21D6/002—Heat treatment of ferrous alloys containing Cr
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
-
- 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
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
-
- 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
-
- 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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
-
- 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
- C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
-
- 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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
-
- 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
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
- C22C38/18—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
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
-
- 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
- C22C38/56—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.7% by weight of carbon
-
- 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
-
- 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
- C23C2/0222—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating in a reactive atmosphere, e.g. oxidising or reducing atmosphere
-
- 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
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
- C23C2/024—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by cleaning or etching
-
- 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
- C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
- C23C2/36—Elongated material
- C23C2/40—Plates; Strips
-
- C—CHEMISTRY; METALLURGY
- 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
- C23F—NON-MECHANICAL REMOVAL OF METALLIC MATERIAL FROM SURFACE; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL; MULTI-STEP PROCESSES FOR SURFACE TREATMENT OF METALLIC MATERIAL INVOLVING AT LEAST ONE PROCESS PROVIDED FOR IN CLASS C23 AND AT LEAST ONE PROCESS COVERED BY SUBCLASS C21D OR C22F OR CLASS C25
- C23F17/00—Multi-step processes for surface treatment of metallic material involving at least one process provided for in class C23 and at least one process covered by subclass C21D or C22F or class C25
-
- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K2101/00—Articles made by soldering, welding or cutting
- B23K2101/006—Vehicles
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K2103/00—Materials to be soldered, welded or cut
- B23K2103/02—Iron or ferrous alloys
- B23K2103/04—Steel or steel 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
-
- 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
- C21D2211/008—Martensite
-
- C—CHEMISTRY; METALLURGY
- C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
- C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
- C25D3/00—Electroplating: Baths therefor
- C25D3/02—Electroplating: Baths therefor from solutions
- C25D3/22—Electroplating: Baths therefor from solutions of zinc
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Organic Chemistry (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Crystallography & Structural Chemistry (AREA)
- Quality & Reliability (AREA)
- Optics & Photonics (AREA)
- Electrochemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Coating With Molten Metal (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
一种用于生产具有高于900MPa的抗拉强度的经锌或锌合金涂覆的钢板的方法,所述钢板用于制造包含平均不多于两个深度为100μm或更大的液态金属脆裂纹/焊点的电阻点焊焊点,所述方法包括以下顺序步骤:提供冷轧钢板,以重量百分比计,所述冷轧钢板的标称组成包含:0.07%≤C≤0.5%,0.3%≤Mn≤5%,0.010%≤Al≤1%,0.010%≤Si≤2.45%,其中0.35%≤(Si+Al)≤2.5%,0.001%≤Cr≤1.0%,0.001%≤Mo≤0.5%,以及任选地,0.005%≤Nb≤0.1%,0.005%≤V≤0.2%,0.005%≤Ti≤0.1%,0.0001%≤B≤0.004%,0.001%≤Cu≤0.5%,0.001%≤Ni≤1.0%,剩余部分为铁和来自熔炼的不可避免的杂质,所述不可避免的杂质的含量为例如:S<0.003%,P<0.02%,N<0.008%;将冷轧钢板在具有气氛(A1)的炉区中加热至550℃至Ac1+50℃的温度T1,以使铁不被氧化,所述气氛(A1)包含按体积计2%至15%的氢气,余量为氮气和不可避免的杂质;然后在温度T≥T1下在高于(0.07%/小时×α)的注射流量Q下向炉气氛中添加选自水蒸气或氧气中的至少一种要素,以获得露点DP2为‑15℃至铁/铁氧化物平衡露点的温度Te的气氛(A2),如果所述要素为水蒸气,则α等于1,或者如果所述要素为氧气,则α等于0.52;然后将所述板在氮的气氛(A2)下的炉区中从温度T1加热至720℃至1000℃的温度T2,所述氮的气氛(A2)包含按体积计2%至15%的氢气和大于0.1%的CO,其中氧气分压高于10‑21atm.,其中所述板从温度T1直至温度T2下的均热结束的持续时间tD为100秒至500秒;将所述板在T2下均热;然后将所述板以10℃/秒至400℃/秒的速率冷却;然后用锌或锌合金涂料涂覆所述板。
Description
本发明涉及高强度经锌涂覆的钢板的制造,所述钢板使得可以获得对由液态金属致脆(Liquid Metal Embrittlement)引起的裂纹形成具有低敏感性的特别适合于汽车行业的要求的电阻点焊焊点。
经锌或锌合金涂覆的钢板对于耐腐蚀性非常有效,并因此广泛用于汽车行业。然而,经验表明,某些钢的焊接可能由于称为液态金属致脆(“LME”)或液态金属辅助开裂(“Liquid Metal Assisted Cracking,LMAC”)的现象而引起特定裂纹的出现。这种现象的特征在于,在施加的应力或者由约束、热膨胀或相变引起的内部应力下,液态Zn沿着下面的钢基材的晶界渗入。已经认识到,较高的应力水平增加LME风险。由于在焊接期间存在的应力本身特别依赖于母材的强度水平,因此经验表明,由具有较高强度的钢制成的焊点通常对LME更敏感。为了降低LME风险,公开EP0812647公开了一种方法,其中进行了使用包含Cu的金属芯焊丝的气体保护电弧焊。然而,该方法不适合于汽车行业中薄板的接合。
JP2006035293公开了这样的电弧焊方法:使用不锈钢焊丝来产生包含大于25%的铁素体的焊点并且实现焊点的抗拉强度小于母材的抗拉强度的1.8倍。然而,除该方法不适合于汽车行业的要求的事实之外,在焊点中实现低强度也是不期望的。
文献JP2004211158还公开了用于管的电阻焊(Electro-Resistance Welding,ERW)的方法,其中在钢组成中存在3ppm至40ppm的硼。然而,该文献的结论与ERW方法的具体条件有关并且无法简单地转用于电阻点焊工艺。此外,B的添加在各个高强度钢种中是不期望的。
文献JP2005002415提出在涂层与钢基材之间***基于镍的层,以使锌的扩散最小化,从而抑制热影响区中LME裂纹的产生。然而,钢板的制造更复杂且昂贵。
文献EP2682495公开了经锌-铝-镁涂覆的钢板,其中钢组成包括一些限制(特别是在C、Mn和Si方面),以获得电弧焊焊缝的高耐LME开裂性。然而,该文献涉及弧焊,而不涉及电阻点焊。此外,最近开发的钢通常包含更高的C、Mn和Si的含量,以实现更高的抗拉强度。因此,不可能将EP2682495中的组成限制与钢板的更高强度水平的需要简单地调和。
因此,期望具有将调和以下两个相矛盾的要求的能够通过经锌涂覆的板的电阻点焊来接合的经锌涂覆的高度可成形钢板:
-一方面,为了实现母材金属板的高于900MPa的抗拉强度TS,这需要一些量的合金元素。
-另一方面,为了能够制造具有高耐LME性的电阻点焊焊点,当母材强度和合金化水平较低时,该事件不太可能发生。
更特别地,期望获得具有少数目的LME深裂纹的焊点,以便不降低焊点的机械性能。特别地,期望的是,当焊接强度不大于Imax(对应于点焊中的喷溅出现)时,深度大于100微米的LME裂纹的平均数目/焊点小于2,并且当焊接强度为Imax至Imax+10%时其不大于2。
考虑到解决这样的问题,本发明涉及用于生产用于制造电阻点焊焊点的具有高于900MPa的抗拉强度的经锌或锌合金涂覆的钢板的方法,所述电阻点焊焊点包含平均不多于两个深度为100μm或更大的液态金属脆裂纹/焊点,所述方法包括以下顺序步骤:
-提供冷轧钢板,以重量百分比计,冷轧钢板的标称组成包含:0.07%≤C≤0.5%,0.3%≤Mn≤5%,0.010%≤Al≤1%,0.010%≤Si≤2.45%,其中0.35%≤(Si+Al)≤2.5%,0.001%≤Cr≤1.0%,0.001%≤Mo≤0.5%,以及任选地,0.005%≤Nb≤0.1%,0.005%≤V≤0.2%,0.005%≤Ti≤0.1%,0.0001%≤B≤0.004%,0.001%≤Cu≤0.5%,0.001%≤Ni≤1.0%,剩余部分为铁和来自熔炼的不可避免的杂质,所述不可避免的杂质的含量为例如:S<0.003%,P<0.02%,N<0.008%;然后
-将冷轧钢板在具有气氛(A1)的炉区中加热至550℃至Ac1+50℃的温度T1,以使铁不被氧化,所述气氛(A1)包含按体积计2%至15%的氢气,余量为氮气和不可避免的杂质;然后
-在温度T≥T1下在高于(0.07%/小时×α)的注射流量Q下向炉气氛中添加选自水蒸气或氧气中的至少一种要素,以获得露点DP2为-15℃至铁/铁氧化物平衡露点的温度Te的气氛(A2),如果所述要素为水蒸气,则α等于1,或者如果所述要素为氧气,则α等于0.52;
-将板在氮的气氛(A2)下的炉区中从温度T1加热至720℃至1000℃的温度T2,氮的气氛(A2)包含按体积计2%至15%的氢气和大于0.1%的CO,其中氧气分压高于10-21atm.,其中板从温度T1直至温度T2下的均热结束的所述加热的持续时间tD为100秒至500秒;
-将板在T2下均热;然后
–将板以10℃/秒至400℃/秒的速率冷却;然后
-用锌或锌合金涂料涂覆板。
优选地,露点DP2为-10℃至+20℃。
根据一个实施方案,气氛(A2)包含按体积计大于0.2%的CO。
根据一个实施方案,温度T2为750℃至900℃,气氛(A2)包含按体积计3%至5%的H2。
根据一个实施方案,在均热之后,将钢板冷却至Ms至Ms+150℃的温度T3,并保持在T3下至少40秒,以获得无碳化物贝氏体钢板。
根据一个实施方案,温度T3为Ms+10℃至Ms+150℃。
根据另一个实施方案,在冷却之后,将钢板冷却至Ms-5℃至Ms-170℃的温度QT,任选地保持在QT下2秒至8秒的持续时间,然后再加热至350℃至550℃的温度T4,以获得配分马氏体。优选地,温度T4为350℃至490℃。
优选地,钢显微组织包含量不大于20%的残余奥氏体。
根据一个实施方案,涂覆通过热浸镀来进行。
根据另一个实施方案,涂覆通过电镀来进行。
根据另一个实施方案,涂覆通过气相沉积技术来进行。
本发明还涉及具有高于900MPa的抗拉强度的经锌或锌合金涂覆的钢板,所述钢板用于制造包含平均不多于两个深度为100μm或更大的液态金属脆裂纹/焊点的电阻点焊焊点,所述钢板包含:钢基材,以重量百分比计,所述钢基材的标称组成包含:0.07%≤C≤0.5%,0.3%≤Mn≤5%,0.010%≤Al≤1%,0.010%≤Si≤2.45%,其中0.35%≤(Si+Al)≤2.5%,0.001%≤Cr≤1.0%,0.001%≤Mo≤0.5%,以及任选地,0.005%≤Nb≤0.1%,0.005%≤V≤0.2%,0.005%≤Ti≤0.1%,0.0001%≤B≤0.004%,0.001%≤Cu≤0.5%,0.001%≤Ni≤1.0%,剩余部分为铁和来自熔炼的不可避免的杂质,所述不可避免的杂质的含量为例如:S<0.003%,P<0.02%,N<0.008%;以及紧邻在锌或锌合金涂层下方0微米至100微米的区域D100,其中在区域D100中平均碳含量Cav(100)满足:Cav(100)/Cnom<0.6,Cav(100)为区域D100中的C的平均含量,Cnom为钢的标称C含量,以及:Cav(100)+(Siav(100))/32<021%,Cav(100)和Siav(100)分别为区域D100中的C和Si的平均含量,以重量%表示。
优选地,钢板是这样的:Cav(100)+(Siav(100)/32)+(Mnav(100)/14)<030%,Cav(100)、Siav(100)和Mnav(100)分别为区域D100中的C、Si和Mn的平均含量,以重量%表示。
优选地,钢板是这样的:Cav(100)+(Siav(100)/32)+(Mnav(100)/14)-(Alav(100)/48)+(Crav(100)/11)<0.34%,Cav(100)、Siav(100)、Mnav(100)、Alav(100)、Crav(100)分别为区域D100中的C、Si、Mn、Al、Cr的平均含量,以重量%表示。
根据一个实施方案,在区域D100中Mn含量不是恒定的,以及:dMnmin>1μm,dMnmin为Mn含量等于区域D100中的最小值Mnmin时在D100中的深度,以及:dMnmin/(Mnmin/Mnnom)>8,Mnnom为钢的标称Mn含量。
根据一个实施方案,在区域D100中Si含量不是恒定的,以及:dSimin>1μm,dSimin为Si含量等于区域D100中的最小值Simin时在D100中的深度,以及:dSimin/(Simin/Sinom)>4,Sinom为钢的标称Si含量。
本发明还涉及电阻点焊焊点的制造,所述电阻点焊焊点包含不多于两个深度为100μm或更大的液态金属脆裂纹,所述制造包括以下顺序步骤:
-提供至少两个如上所述的经锌或锌合金涂覆的钢板,所述钢板的厚度为0.5mm至2.5mm;然后
-至少部分地叠置经锌或锌涂覆的钢板;然后
-通过放置成垂直于叠置的板并在叠置的板的外侧上的电极施加350daN至500daN的力;然后
-以Imin至1.10Imax的强度I焊接钢板,Imin是最小强度,高于该最小强度,当使电阻点焊焊点经受剪切拉伸试验时观察到拔拉破坏,Imax是在电阻点焊中开始观察到液态金属的喷溅时的强度。
本发明还涉及用于制造包含不多于两个深度为100μm或更大的液态金属脆裂纹的电阻点焊焊点的方法,所述方法包括以下顺序步骤:
-提供至少两个具有TS>900MPa的经锌或锌合金涂覆的钢(1)的板,所述钢(1)的板的厚度为0.5mm至2.5mm;
-测量C1av(100)、Si1av(100)、Mn1av(100)、Al1av(100)、Cr1av(100),这些量分别表示在锌或锌合金涂层下方0微米至100微米的钢基材的区域D100中的C、Si、Mn、Al、Cr的平均含量;然后
-计算钢(1)的因数CSI1:
CSI1=C1av(100)+(Si1av(100)/32)+(Mn1av(100)/14)-(Al1av(100)/48)+(Cr1av(100)/11);
-然后以Imin至1.1Imax的强度I1对至少10个焊点进行电阻点焊,Imin是最小强度,高于该最小强度,当使电阻点焊焊点经受剪切拉伸试验时观察到拔拉破坏,Imax是在电阻点焊中开始观察到液态金属的喷溅时的强度;然后
-由所述至少10个焊点测量深度为100μm或更大的液态金属脆裂纹的平均数目Crack1av,然后,如果Crack1av高于2;
-提供第二具有TS>900MPa的经锌或锌合金涂覆的钢板(2),钢板(2)的厚度与钢(1)的厚度相同,钢(2)的组成选择成使得:CSI2<CSI1-((Crack1av-2)/20),其中:
CSI2=C2av(100)+(Si2av(100)/32)+(Mn2av(100)/14)-(Al2av(100)/48)+(Cr2av(100)/11),C2av(100)、Si2av(100)、Mn2av(100)、Al2av(100)、Cr2av(100)分别表示在锌或锌合金涂层下方0微米至100微米的钢(2)基材的区域D100中的C、Si、Mn、Al、Cr的平均含量;然后
-以强度I1对钢板(2)进行电阻点焊。
本发明的目的还在于如上所述的钢板或如上所述制造的钢板用于制造机动车辆的结构部件的用途。
现在将详细地描述本发明并且通过实施例举例说明本发明而不引入限制。
首先,提供厚度为0.5mm至2.5mm的冷轧钢板,该厚度是汽车行业中使用的典型厚度范围。本发明中实施的钢板通过这样的方法来制造:其顺序地包括铸造、热轧、卷取、任选的中间退火、酸洗、冷轧、连续退火和涂覆的步骤。以重量%计,钢的组成包含以下元素:
-碳:0.07%至0.5%。如果碳含量低于0.07%,则抗拉强度可能不足,即低于900MPa。此外,如果钢显微组织包含残余奥氏体,则可能无法获得对于实现足够的延伸率所必需的其稳定性。高于0.4%的C,可焊接性降低,因为在点焊焊点的热影响区中或在熔化区中产生低韧性显微组织。在一个优选的实施方案中,碳含量在0.18%至0.4%的范围内,这使得可以实现高于1180MPa的抗拉强度。当经锌涂覆的钢板被加热时,钢基材中的低碳含量会削减钢与液态Zn或Zn合金之间的相互作用。因此,不太可能发生LME。
-锰是有助于获得高于900MPa的抗拉强度的固溶硬化元素。当Mn含量为至少0.3重量%时,获得这样的效果。然而,高于5%,Mn的添加有助于形成具有可能不利地影响焊点机械特性的过度显著的偏析区的组织。优选地,锰含量在1.5%至3%的范围内以实现这些效果。这使得可以获得令人满意的机械强度,而不增加钢的工业制造难度并且不增加焊点的淬透性。在特定的退火条件下,Mn与Si和O反应,从而降低钢中的表面下区域中的Si的量。因此,如果保持Mn在Zn涂层下低于特定量,结合C、Si、Al和Cr,则耐LME性增加。
-硅必须为0.010%至2.45%,以实现所需的机械特性和可焊接性的组合:由于硅在渗碳体中的溶解度低以及由于该元素增加奥氏体中的碳的活性的事实,硅在板的冷轧之后的退火期间使碳化物析出减少。因此,奥氏体的碳富集导致其在室温下的稳定化,并且导致出现相变诱导塑性(“TRIP”)行为,这意味着在成形期间施加应力例如将导致该奥氏体转变成马氏体。当Si高于2.45%时,在热浸镀之前的退火期间可能形成牢固地粘附的氧化物,这可能导致涂层中的表面缺陷。就C而言,减少Si促进电阻点焊期间的LME。通过控制退火条件,可以改变涂层下的硅的量。露点控制退火炉内氧气的分压。氧气在钢内部扩散并与Si反应而产生SiO2。结果,降低了钢表面下区域中的Si的量。因此,如果保持Si在Zn涂层下低于特定量,则耐LME性增加。
-铝必须为0.010%至1%。对于残余奥氏体的稳定化,铝具有与硅的影响相对相似的影响。然而,铝含量高于1重量%将增加Ac3温度(即在退火步骤期间钢中完全转变成奥氏体的温度),并因此将使工业工艺更加昂贵。因此,将Al含量限制为1%。
由于高度可成形性钢在室温下包含残余奥氏体,因此必须通过以例如(Si+Al)≥0.35%的量在钢组成中添加硅和/或铝来提供足够的奥氏体稳定化。如果(Si+Al)<0.35%,则残留奥氏体的分数可能小于5%,因此冷成形中的延性特性和应***化特性可能不足。然而,如果(Si+Al)>2.5%,则可涂覆性和可焊接性劣化。
-铬使得可以在退火周期期间在保持在最高温度下之后的冷却步骤期间延迟先共析铁素体的形成,使得可以实现更高的强度水平。因此,出于成本的原因以及为了防止过度硬化,铬含量高于0.001%且低于1.0%。Cr还影响钢的耐LME性:在特定的退火条件下,在下表面区域中,Cr与Mn和O反应。因此,如果保持Cr在Zn涂层下低于特定量,结合C、Si、Al和Cr,则可以提高耐LME性。
-量为0.001%至0.5%的钼对于提高淬透性并使残余奥氏体稳定是有效的,因为该元素使奥氏体的分解延迟。
-钢可以任选地包含能够以碳化物、氮化物或碳氮化物的形式析出从而实现沉淀硬化的元素。为了这个目的,钢可以包含铌、钛或钒:Nb和Ti各自的量为0.005%至0.1%,V的量为0.005%至0.2%。
-钢可以任选地包含量为0.001%至1.0%的镍以改善韧性。
-钢还可以任选地包含量为0.001%至0.5%的铜以提供另外的硬化。
-钢还可以任选地包含量为0.0001%至0.005%,优选0.0001%至0.004%的硼。通过在晶界处偏析,B降低晶界能并因此有益于增加耐液态金属致脆性。
-组成中的余量为铁和由炼钢产生的残留元素。在这方面,S、P和N至少被认为是残留元素或不可避免的杂质。因此,它们的含量为S小于0.003%、P小于0.02%、以及N小于0.008%。
上述组成应理解为标称组成,即不考虑位于紧邻在钢板的两个主表面下方的位置的两个100微米厚度的区域,钢板的存在于以板的中间厚度为中心的区域中的组成。如下面将解释的,在本发明中,该标称组成与紧邻在Zn涂层下方的钢基材表面处存在的局部组成不同。
在冷轧之后,钢显微组织高度各向异性并且延性特性劣化。因此,进行退火以实现晶粒再结晶以及获得奥氏体转变,这使得可以产生最终期望的显微组织。退火通过钢带在分成数个区的炉中的连续移位来进行。
根据本发明,将冷轧钢板在辐射管式炉、或电阻炉、或感应炉、或组合这些方法中的至少任两者的炉中连续退火至550℃至Ac1+50℃的温度T1,其中Ac1表示当将钢在炉区中加热时奥氏体转变开始的温度,所述炉区中的气氛(A1)包含按体积计2%至15%的氢气,优选按体积计3%至5%的氢气,余量为氮气和不可避免的杂质,并且其具有例如铁不被氧化的露点DP1。该值可以例如根据出版物D.Huin,P.Flauder,J.B.Leblond,“Numericalsimulation of internal oxidation of steels during annealing treatments”.Oxidation of Metals 2005;64;1:131-67来确定。然后将板从温度T1加热至720℃至1000℃的温度T2,同时选自水蒸气或氧气中的至少一种要素在温度T1下开始注入炉中。
在水蒸气的情况下,水蒸气的温度为90℃至150℃,注射流量Q必须高于每小时0.07%,以获得将在下面详细说明的钢板表面的改性,使得可以获得高耐LME性。注射流量Q通过每小时注射的蒸气体积除以炉区的在水蒸气的注射位置与在均热温度T2下加热的炉段的末端之间的体积来评估,如下面将述面的。
在氧气注射的情况下,注射流量Q必须高于0.036%/小时,以获得增加耐LME性所必需的钢表面的改性。注射流量Q通过每小时氧气的注射体积除以炉的在氧气的注射位置与在均热温度T2下加热的炉段的末端之间的体积来评估。
因此,无论进行何种注射类型(水蒸气或氧气),用于获得增加的耐LME性的最小注射流量Q为(0.07%/小时×α),如果注射的要素为水蒸气,则α等于1;或者如果注射的要素为氧气,则α等于0.52。
在温度T1与温度T2之间的炉段中,气氛(A2)的露点DP2必须为-15℃至铁/铁氧化物平衡露点的温度Te,优选为-10℃至+20℃。气氛(A2)包含氮和按体积计2%至15%的氢气,优选按体积计3%至5%的氢气。温度Te可以例如根据以下出版物来确定:JANAFThermomechanical Tables,第3版,Part II,Journal of Physical and ChemicalReference Data,第14卷,1985,副刊n°1,由American Chemical Society和the AmericanInstitute of Physics for the National Bureau of Standards出版。
由于特定的流量Q,气氛(A2)包含按体积计大于0.1%的CO,优选按体积计大于0.2%的CO,并且气氛(A2)中的氧气分压高于10-21atm.。这使得可以获得在钢板的位于0微米至100微米的表面下区域中的C、Mn、Si、Al、Cr的改性。
T1至T2下的均热结束之间的持续时间tD为100秒至500秒。如果持续时间tD小于100秒,则位于0微米至100微米的表面下区域中的钢组成的改性不足而无法显著改善耐LME性。如果时间tD大于500秒,则存在钢板的机械特性变得不足的风险。
然后将板在上述气氛(A2)下在T2至T2+50℃的温度下均热。
在温度T2下均热可以为30秒至400秒的持续时间之后,将钢板冷却以获得兼具高可成形性和高于900MPa的抗拉强度的显微组织。冷却可以通过使用具有5%至70%氢气的氮气或水淬火来进行,以获得10℃/秒至400℃/秒的冷却速率。
根据一个实施方案,为了获得无碳化物贝氏体(“carbides free bainite,CFB”)显微组织,将钢板冷却至Ms至Ms+150℃、或Ms+10℃至Ms+150℃的温度T3。之后,将钢板保持在温度T3下至少40秒,以获得显微组织转变。最终的显微组织通常包含10%至20%的残余奥氏体和大于50%的贝氏体,该贝氏体实际上不含粗碳化物,即,是这样的:尺寸大于0.1μm的板条间碳化物的每单位面积数目不大于50000/mm2。
根据另一个实施方案,为了获得经淬火和配分(“Q-P”)的显微组织,将钢板冷却至低于马氏体起始温度(Ms),即Ms-5℃至Ms-170℃的温度QT,任选地保持在QT下2秒至8秒的持续时间,然后在气氛(A3)中再加热至350℃至550℃,优选350℃至490℃的温度T4并均热30秒至500秒,使得不发生表面铁的再氧化。优选地,该气氛包含按体积计2%至15%的氢气,并且更优选按体积计3%至5%的氢气。
最终的显微组织通常包含3%至20%的残余奥氏体、大于25%的配分马氏体,即具有比钢的标称C含量更低的C含量的回火马氏体。
此后,在保持在温度Tbm的基于Zn的液体金属浴中对钢板进行热浸涂。在这方面,温度为Tbm-10℃至Tbm+50℃的钢连续地通过液体金属浴以被涂覆。所述板为经锌或锌合金涂覆的板,后面的表述表示其中Zn含量高于50重量%的涂层。特别地,涂覆可以如下进行:通过热浸镀锌(“GI”),或者通过在紧接着热浸镀锌之后在约475℃至570℃下进行热处理,以引起铁在涂层中扩散并且获得包含约7%至14%的Fe的“镀锌扩散退火的”或“GA”涂层。其还可以为通过电镀工艺或者通过气相沉积工艺获得的锌或锌合金涂层。Zn合金也可以为Zn-Mg-Al涂层,例如Zn-3%Mg-3.7%Al或Zn-1.2%Al-1.2%Mg涂层。
在用于生产镀锌涂覆钢板(GI)的一个优选实施方案中,在T3或T4下均热(根据期望的显微组织,CFB或Q-P钢)之后,将钢板加热至465℃±20℃,并且在保持在460℃±20℃的包含0.15重量%至0.40重量%铝的液体锌浴中进行热浸镀锌。镀锌持续时间为2秒至10秒。
在用于生产镀锌扩散退火涂层(GA)的另一个优选实施方案中,在保持在460℃±20℃的包含0.10重量%至0.17重量%铝的液体锌浴中进行镀锌,然后在475℃至570℃下进行后涂层热处理。
锌涂层还可以通过电镀法施加在钢板上。在此方法中,在T3或T4温度下均热之后,将钢板冷却至室温。然后将该钢板浸入保持在50℃至100℃的包含锌的基于氯化物或硫酸盐的盐的溶液的电镀锌浴中。在此方法中,电流流过两个阳极,而钢板充当阴极。
锌涂层还可以通过本身已知的气相沉积法施加在钢板上。
以令人惊讶的方式,本发明人已证明,当钢板标称组成对应于上述特征时并且当位于紧邻在Zn或Zn合金涂层下面0μm至100μm的位置的区域D100的组成表现出特定特征时,可以获得高抗拉强度和高耐LME开裂性的组合。应理解,该区域D100存在于钢板上的两个主表面的每一者上。该区域中的特定特征是在退火过程中获得的,即通过特定温度、注射流量、炉气氛、持续时间和露点范围获得的,这使得可以在施加Zn或Zn合金涂层之前改变钢表面的组成。因此,获得了具有改变的组成(即在碳、锰、硅、铝和铬方面)的区域。该区域的平均组成以及该区域内的Mn和Si的梯度通过标称钢组成、温度T1和T2、流量Q、T1至T2下的均热结束的持续时间tD和炉气氛来控制。特别地,T1与T2之间的露点DP2和氧气分压对区域的性质和深度具有强烈影响。
在Zn或Zn合金涂层下方的区域D100中,钢的组成与钢标称组成相比不同。该特定区域改善了点焊中的耐LME开裂性。与紧接着在Zn浴中进行热浸镀之前的钢板相比,经验表明,约一微米的钢板表面与液体锌合金浴反应或溶解在液体锌合金浴中。
区域D100中的诸如C、Mn、Si、Cr、Al的元素的含量分布及其在该区域中的平均含量(各自为:Cav(100)、Siav(100)、Mnav(100)、Alav(100)、Crav(100))可以通过本身已知的技术例如辉光放电发射光谱法(Glow-Discharge Optical Emission Spectroscopy,GDOES)来测量。
因此可以将Cav(100)与钢板的标称C含量Cnom相比较。本发明人已证明,为了改善耐LME开裂性,在D100中必须存在一定量的脱碳,即,Cav(100)/Cnom必须低于0.6。进一步为了产生在钢板的表面处的该C梯度,本发明人证明,当D100中的C和Si使得:Cav(100)+Siav(100)/32<0.21%时,有效地获得耐LME性。
此外,将耐LME开裂性(通过深于100μm的裂纹的平均数目/焊点所测量的)与D100中存在的元素相关联,本发明人已证明,通过考虑D100中的C、Si和Mn以在该区域中限定如下条件来获得更好的相关系数:Cav(100)+(Siav(100)/32)+(Mnav(100)/14)<0.30%。
在最苛刻的焊接条件下,即在与高约束相关的几何形状的情况下和在高焊接强度的情况下,已发现,必须将C、Mn、Si、Al、Cr全部考虑在内以获得最佳的耐LME性,即这些元素必须在区域D100中满足如下条件:
Cav(100)+(Siav(100)/32)+(Mnav(100)/14)-(Alav(100)/48)+(Crav(100)/11)<0.34%
此外,退火条件在区域D100中产生Mn的梯度和Si的梯度,因此这些元素的浓度在该区域中改变:在Zn涂层下方一定距离处(分别为dSimin和dMnmin)经历Si含量和Mn含量的最小值(分别为Simin和Mnmin)。
本发明人已证明,当:dSimin>1μm,并且当:dSimin/(Simin/Sinom)>4时,获得高的耐LME开裂性,Sinom表示钢的标称Si含量。
关于Mn,以类似方式,当:dMnmin>1μm,并且当:dMnmin/(Mnmin/Mnnom)>8时,观察到高的耐LME性,Mnnom表示钢的标称Mn含量。
此外,基于本发明人的很多观察和发现,他们导出了用于制造包含不多于两个深度为100μm或更大的液态金属脆裂纹的电阻点焊焊点的方法。在当前情况下,当经历LME裂纹时,进行了改变标称钢组成或涂层的试验。
然而,由于这些变性而引起的最终改善可能没有通用特性:例如,改善对于焊接条件1可以是显著的,而对于具有不同强度的焊接条件2是不太显著的。
本发明人已经对于在Imax(该Imax是在电阻点焊中开始观察到液态金属的喷溅时的强度)左右的不同焊接强度值建立了耐LME性(通过深于100μm的裂纹的平均数目所测量的)与参数CSI=Cav(100)+(Siav(100)/32)+(Mnav(100)/14)-(Alav(100)/48)+(Crav(100)/11)之间的相互关系。他们观察到裂纹的数目是CSI的线性函数,并且无论在Imax左右的范围内强度如何,该相互关系的斜率都大约相同。基于该发现,本发明人构思了以下用于更容易地改善LME问题的方法:作为第一步,提供具有TS>900MPa的经锌或锌合金涂覆的钢(1)的板,其中厚度为0.5mm至2.5mm。这些钢板待通过电阻点焊来接合。
然后,测量C1av(100)、Si1av(100)、Mn1av(100)、Al1av(100)、Cr1av(100),这些量分别表示在锌或锌合金涂层下方0微米至100微米的钢基材的区域D100中的C、Si、Mn、Al、Cr的平均含量。钢(1)的因数CSI1通过以下来计算:CSl1=C1av(100)+(Si1av(100)/32)+(Mn1av(100)/14)-(Al1av(100)/48)+(Cr1av(100)/11)。
此后以Imin至1.1Imax的强度I1对至少10个焊点进行电阻点焊,Imin是最小强度,高于该最小强度,当使电阻点焊焊点经受剪切拉伸试验时观察到拔拉破坏,Imax是在电阻点焊中开始观察到液态金属的喷溅时的强度。
然后,由该至少10个焊点测量深度为100μm或更大的LME裂纹的平均数目Crack1av。如果结果不令人满意,即如果Crack1av高于2,则本发明人已得出用于快速提供可以满足以下要求的钢板的方法:
提供具有TS>900MPa且具有与钢(1)的厚度相同的厚度的第二经锌或锌合金涂覆的钢板(2),该钢(2)的组成选择成使得满足:CSl2<CSl1-((Crack1av-2)/20,其中:CSI2=C2av(100)+(Si2av(100)/32)+(Mn2av(100)/14)-(Al2av(100)/48)+(Cr2av(100)/11),C2av(100)、Si2av(100)、Mn2av(100)、Al2av(100)、Cr2av(100)分别表示在锌或锌合金涂层下方0微米至100微米的钢(2)基材的区域D100中C、Si、Mn、Al、Cr的平均含量,以重量%计。然后,以相同的强度I1焊接钢(2)。这种方法确保了由此由钢(2)制造的点焊焊点将是令人满意的,并且节省了昂贵且耗时的试验和误差测试。
现将通过以下实施例举例说明本发明,所述实施例决不是限制性的。
实施例1:
提供厚度范围为1.4mm至1.6mm的冷轧钢板,标记为A至F的标称组成报告在表1中。组成的剩余部分为铁和由熔炼产生的不可避免的杂质。特别地,以重量%计,S、P和N是这样的:S<0.003%,P<0.02%,N<0.008%。
分别对应于在加热时开始转变成奥氏体和对应于在冷却时开始马氏体转变的Ac1和Ms温度也报告在表1中。
表1.钢组成(重量%)
使这些钢板经受不同的退火周期。表2报告了这些不同条件中的气氛、温度、流量、露点以及在温度T1和T2下的持续时间。因此,板D3表示例如已经经受退火条件3的具有组成D的冷轧钢。
在条件2至5中,已进行向温度T1下的炉中注射温度为110℃的蒸汽水。
在A1中不发生铁氧化。
在退火条件1中,钢板表面未经充分改性,因此不存在使得可以实现高耐LME性的特定表面特征,如从下面表4和表5中的试验B1c、E1a、E1b可以看出的。
在退火条件2中,进行蒸气注射,然而以0.05%/小时的不足的蒸气流量进行。气氛A2中的CO百分比和氧气分压也不足以实现高耐LME性,如从表4和表5中的试验A2c和C2d可以看出的。
在退火条件3至5中,根据本发明的条件进行水蒸气注射。
在T2下均热之后,将钢板A至D以10℃/秒至400℃/秒的冷却速率冷却,直到温度T3对于钢A等于Ms+45℃,对于钢B等于Ms+90℃,对于钢C和D等于Ms+40℃。在T2下保持的持续时间对于钢A、B和C至D分别为300秒、40秒和360秒。
将钢E冷却至225℃的温度QT,然后再加热至410℃的温度T4,持续90秒的持续时间。
将钢F冷却至150℃的温度QT,然后再加热至465℃的温度T4,持续120秒的持续时间。
用纯锌对钢板A和C至F进行电镀(EG),而在包含0.3%Al和0.4%Fe的Zn浴中对钢B进行热浸镀锌(GI)。所有施加的涂层具有7μm的相似厚度。
通过辉光放电发射光谱法(GDOES)测量区域D100中的C、Mn、Si、Cr、Al的含量变化和该区域中的这些元素的平均值(分别为:Cav(100)、Siav(100)、Mnav(100)、Alav(100)、Crav(100))。
由钢A至D获得的板的显微组织包含12%的残余奥氏体和大于50%的贝氏体,所述贝氏体的尺寸大于0.1μm的板条间碳化物的每单位面积数目不大于50000/mm2。由钢E至F获得的钢的显微组织包含3%至20%的残余奥氏体,和大于25%的配分马氏体。
表2.退火条件
加下划线的值:未根据本发明
在根据表3的不同条件下在50HZ或60HZ的交流电和450daN至500daN的电极力下对钢板进行电阻点焊。将电极放置成垂直于钢板。D3d表示例如由根据条件d焊接的在标记为n°3的条件下退火的钢D制成的焊点。
-通过施加不同值的强度,可以确定由Imin和Imax限定的适当的焊接范围,Imin是最小强度,高于该最小强度,当使电阻点焊焊点经受剪切拉伸试验时观察到拔拉破坏,Imax是在电阻点焊中开始观察到液态金属的喷溅时的强度。在工业条件下强度的选择常常在该最后的值左右进行,因为它对应于大的焊点熔核直径,其使得可以获得高焊点抗拉特性。在目前情况下,焊接在Imax和在喷溅范围内略高于Imax(即Imax+10%)下进行。尽管以Imax至Imax+10%的强度焊接增加了LME敏感性,但是这种情况可能在工业实践中的某些情况下遇到。
-表3还报告了焊接顺序:例如12-2-12表示焊接顺序由以下组成:12个20毫秒的电流流动的周期(“热周期”),接着是两个20毫秒的电流不流动的周期(“冷周期”),和最后12个电流流动的周期。
-通过将两个或三个板焊接在一起并产生层叠体构造,对LME开裂的敏感性随着层叠体厚度的增加而提高。进行异质焊接,另一钢板为具有包含以下的组成的软钢:0.032%C、0.008%Si、0.222%Mn、0.052%Al、0.039%Cr和0.012%N。选择软钢的原因是,其点焊需要比拉伸应力高于900MPa的钢更高的电流水平来获得合适的焊点。这种高电流水平引起高的热输入,并且因此在高电阻钢的焊接期间引起更多的LME裂纹。因此,提高了焊接条件的严苛性。表3报告了层叠体的总厚度。在这些层叠体中,焊接以抗拉强度高于900MPa的钢板的一个表面与焊接电极接触的方式进行。最终的裂纹更容易出现在由焊接电极在板表面处产生的压痕区域中。
表3.电阻点焊条件
在以下条件下对由LME引起的裂纹进行观察和量化:在对10个至20个焊点进行半横切和精抛光之后,通过光学显微镜以10至1000的放大倍率观察焊点截面。对于每个焊点测量深度超过100微米的裂纹的数目,并且对于该系列的20个焊点计算每点焊焊点深于100μm的LME裂纹的平均数目。
在以I=Imax焊接的情况下,当裂纹的平均数目小于2时,获得高耐LME开裂性;或者在以Imax+10%焊接的情况下,当裂纹的平均数目小于或等于2时,获得高耐LME开裂性。
表4和表5示出了与如根据GDOES测量的在Zn涂层下方的区域D100中的钢组成的一些特定特征有关的在Imax或Imax+10%的焊接条件下确定的平均LME裂纹数目。此外,表4报告了对母材测量的最小抗拉强度。
表4:Zn涂层下方的区域D100的特征-LME开裂的发生-基材抗拉强度
(I)=Cav(100)+Siav(100)/32
(II)=Cav(100)+(Siav(100)/32)+(Mnav(100)/14)
(III)=Cav(100)+(Siav(100)/32)+(Mnav(100)/14)-(Alav(100)/48)+(Crav(100)/11)
加下划线的值:未根据本发明。
n.a.:未评估。
表5:Zn涂层下方的区域D100中的Mn和Si特征-LME开裂的发生加下划线的值:未根据本发明。
n.a.:未评估。
如表4显示的,在所有情况下,该组成和退火条件使得可以制造具有高可成形性并且具有至少900MPa的抗拉强度的经Zn或Zn合金涂覆的钢板。然而,这些板不具有相同的耐LME开裂性:钢板D3、F4、E5根据本发明的条件来制造。因此,区域D100中的C、Mn、Si和Cr的平均含量降低至这样的程度:即使在Imax+10%下焊接的条件下也不太可能发生LME开裂。
退火条件产生了具有Mn梯度和Si梯度的区域D100。表5还示出,关于这些钢,Mn和Si分布显示,在Zn涂层下方Si含量和Mn含量的最小值的位置大于1μm,并且使得dSimin/(Simin/Sinom)>4和dMnmin/(Mnmin/Mnnom)>8。位于距Zn涂层足够距离处的充分削减Si和Mn的该区域的产生,使得可以提高耐LME性。
相比之下,板B1、E1、A2、C2的退火条件不符合本发明。因此,脱碳和在Si、Mn、Cr和Al方面的组成改变不足以获得足够的耐LME性。
因此,由于它们的高机械特性和在电阻点焊中的高耐LME开裂性,根据本发明制造的高强度钢板可以有利地用于制造用于机动车辆的结构部件。
Claims (18)
1.一种用于生产具有高于900MPa的抗拉强度的经锌或锌合金涂覆的钢板的方法,所述钢板用于制造包含平均不多于两个深度为100μm或更大的液态金属脆裂纹/焊点的电阻点焊焊点,所述方法包括以下顺序步骤:
-提供冷轧钢板,以重量百分比计,所述冷轧钢板的标称组成包含:
0.07%≤C≤0.5%
0.3%≤Mn≤5%
0.010%≤Al≤1%
0.010%≤Si≤2.45%
其中0.35%≤(Si+Al)≤2.5%,
0.001%≤Cr≤1.0%
0.001%≤Mo≤0.5%
以及任选地
0.005%≤Nb≤0.1%
0.005%≤V≤0.2%
0.005%≤Ti≤0.1%
0.0001%≤B≤0.004%
0.001%≤Cu≤0.5%
0.001%≤Ni≤1.0%,
剩余部分为铁和来自熔炼的不可避免的杂质,所述不可避免的杂质的含量为例如:
S<0.003%
P<0.02%
N<0.008%;
-将所述冷轧钢板在具有气氛(A1)的炉区中加热至550℃至Ac1+50℃的温度T1,以使所述铁不被氧化,所述气氛(A1)包含按体积计2%至15%的氢气,余量为氮气和不可避免的杂质;然后
-在温度T≥T1下在高于(0.07%/小时×α)的注射流量Q下向炉气氛中添加选自水蒸气或氧气中的至少一种要素,以获得露点DP2为-15℃至铁/铁氧化物平衡露点的温度Te的气氛(A2),如果所述要素为水蒸气,则α等于1,或者如果所述要素为氧气,则α等于0.52;
-将所述板在氮的气氛(A2)下的炉区中从所述温度T1加热至720℃至1000℃的温度T2,所述氮的气氛(A2)包含按体积计2%至15%的氢气、大于0.1%的CO,其中氧气分压高于10-21atm.,其中所述板从温度T1直至温度T2下的均热结束的所述加热的持续时间tD为100秒至500秒;
-将所述板在T2下均热;然后
-将所述板以10℃/秒至400℃/秒的速率冷却;然后
-用锌或锌合金涂料涂覆所述板。
2.根据权利要求1所述的方法,其中所述露点DP2为-10℃至+20℃。
3.根据权利要求1或2中任一项所述的方法,其中所述气氛(A2)包含按体积计大于0.2%的CO。
4.根据权利要求1至3中任一项所述的方法,其中所述温度T2为750℃至900℃,以及其中所述气氛(A2)包含按体积计3%至5%的H2。
5.根据权利要求1至4中任一项所述的方法,其中在所述均热之后,将所述钢板冷却至Ms至Ms+150℃的温度T3,并保持在T3下至少40秒,以获得无碳化物贝氏体钢板。
6.根据权利要求5所述的方法,其中所述温度T3为Ms+10℃至Ms+150℃。
7.根据权利要求1至5中任一项所述的方法,其中在所述冷却之后,将所述钢板冷却至Ms-5℃至Ms-170℃的温度QT,任选地保持在QT下2秒至8秒的持续时间,然后再加热至350℃至550℃,优选350℃至490℃的温度T4,以获得配分马氏体。
8.根据权利要求1至7中任一项所述的方法,其中所述钢显微组织包含量不大于20%的残余奥氏体。
9.根据权利要求1至8中任一项所述的方法,其中所述涂覆通过热浸镀来进行。
10.根据权利要求1至8中任一项所述的方法,其中所述涂覆通过电镀来进行。
11.一种具有高于900MPa的抗拉强度的经锌或锌合金涂覆的钢板,所述钢板用于制造包含平均不多于两个深度为100μm或更大的液态金属脆裂纹/焊点的电阻点焊焊点,所述钢板包含:钢基材,以重量百分比计,所述钢基材的标称组成包含:
0.07%≤C≤0.5%
0.3%≤Mn≤5%
0.010%≤Al≤1%
0.010%≤Si≤2.45%
其中0.35%≤(Si+Al)≤2.5%,
0.001%≤Cr≤1.0%
0.001%≤Mo≤0.5%
以及任选地
0.005%≤Nb≤0.1%
0.005%≤V≤0.2%
0.005%≤Ti≤0.1%
0.0001%≤B≤0.004%
0.001%≤Cu≤0.5%
0.001%≤Ni≤1.0%,
剩余部分为铁和来自熔炼的不可避免的杂质,所述不可避免的杂质的含量为例如:
S<0.003%
P<0.02%
N<0.008%;
以及紧邻在所述锌或锌合金涂层下方0微米至100微米的区域D100,其中在所述区域D100中平均碳含量Cav(100)满足:
Cav(100)/Cnom<0.6,
Cav(100)为所述区域D100中的C的平均含量,Cnom为所述钢的标称C含量,以及:
Cav(100)+(Siav(100))/32<0.21%,
Cav(100)和Siav(100)分别为所述区域D100中的C和Si的平均含量,以重量%表示。
12.根据权利要求11所述的钢板,其中:
Cav(100)+(Siav(100)/32)+(Mnav(100)/14)<0.30%,
Cav(100)、Siav(100)和Mnav(100)分别为所述区域D100中的C、Si和Mn的平均含量,以重量%表示。
13.根据权利要求11或12中任一项所述的钢板,其中:
Cav(100)+(Siav(100)/32)+(Mnav(100)/14)-(Alav(100)/48)+(Crav(100)/11)<0.34%,
Cav(100)、Siav(100)、Mnav(100)、Alav(100)、Crav(100)分别为所述区域D100中的C、Si、Mn、Al、Cr的平均含量,以重量%表示。
14.根据权利要求11至13中任一项所述的钢板,其中在所述区域D100中Mn含量不是恒定的,以及其中:
dMnmin>1μm,
dMnmin为Mn含量等于所述区域中的最小值Mnmin时在D100中的深度,以及:
dMnmin/(Mnmin/Mnnom)>8,
Mnnom为所述钢的标称Mn含量。
15.根据权利要求11至14中任一项所述的钢板,其中在所述区域D100中Si含量不是恒定的,以及其中:
dSimin>1μm,
dSimin为Si含量等于所述区域中的最小值Simin时在D100中的深度,以及:
dSimin/(Simin/Sinom)>4,
Sinom为所述钢的标称Si含量。
16.一种用于制造包含不多于两个深度为100μm或更大的液态金属脆裂纹的电阻点焊焊点的方法,所述方法包括以下顺序步骤:
-提供至少两个根据权利要求11至15中任一项所述的经锌或锌合金涂覆的钢板,所述钢板的厚度为0.5mm至2.5mm;然后
-至少部分地叠置所述经锌或锌涂覆的钢板;然后
-通过放置成垂直于叠置的板并在叠置的板的外侧上的电极施加350daN至500daN的力;然后
-以Imin至1.10Imax的强度I焊接所述钢板,Imin是最小强度,高于所述最小强度,当使所述电阻点焊焊点经受剪切拉伸试验时观察到拔拉破坏,Imax是在电阻点焊中开始观察到液态金属的喷溅时的强度。
17.一种用于制造包含不多于两个深度为100μm或更大的液态金属脆裂纹的电阻点焊焊点的方法,所述方法包括以下顺序步骤:
-提供至少两个具有TS>900MPa的经锌或锌合金涂覆的钢(1)的板,所述钢(1)的板的厚度为0.5mm至2.5mm;
-测量C1av(100)、Si1av(100)、Mn1av(100)、Al1av(100)、Cr1av(100),这些量分别表示在锌或锌合金涂层下方0微米至100微米的钢基材的区域D100中的C、Si、Mn、Al、Cr的平均含量;然后
-计算钢(1)的因数CSI1:
CSI1=C1av(100)+(Si1av(100)/32)+(Mn1av(100)/14)-(Al1av(100)/48)+(Cr1av(100)/11)
-然后;
-以Imin至1.1Imax的强度I1对至少10个焊点进行电阻点焊,Imin是最小强度,高于所述最小强度,当使所述电阻点焊焊点经受剪切拉伸试验时观察到拔拉破坏,Imax是在电阻点焊中开始观察到液态金属的喷溅时的强度;然后
-由所述至少10个焊点测量深度为100μm或更大的液态金属脆裂纹的平均数目Crack1av,然后,如果Crack1av高于2;
-则提供第二具有TS>900MPa的经锌或锌合金涂覆的钢板(2),所述钢板(2)的厚度与钢(1)的厚度相同,钢(2)的组成选择成使得:
CSI2<CSI1-((Crack1av-2)/20)
其中:
CSI2=C2av(100)+(Si2av(100)/32)+(Mn2av(100)/14)-(Al2av(100)/48)+(Cr2av(100)/11)
C2av(100)、Si2av(100)、Mn2av(100)、Al2av(100)、Cr2av(100)分别表示在所述锌或锌合金涂层下方0微米至100微米的所述钢(2)基材的区域D100中的C、Si、Mn、Al、Cr的平均含量;
-以所述强度I1对所述钢板(2)进行电阻点焊。
18.根据权利要求11至15中任一项所述的钢板或根据权利要求1至14中任一项制造的钢板用于制造机动车辆的结构部件的用途。
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
IBPCT/IB2017/000753 | 2017-06-20 | ||
PCT/IB2017/000753 WO2018234839A1 (en) | 2017-06-20 | 2017-06-20 | ZINC COATED STEEL SHEET HAVING HIGH STRENGTH POINTS WELDABILITY |
PCT/IB2018/054306 WO2018234938A1 (en) | 2017-06-20 | 2018-06-13 | ZINC COATED STEEL SHEET HAVING HIGH STRENGTH POINTS WELDABILITY |
Publications (2)
Publication Number | Publication Date |
---|---|
CN110892087A true CN110892087A (zh) | 2020-03-17 |
CN110892087B CN110892087B (zh) | 2022-03-25 |
Family
ID=59366454
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
CN201880037315.XA Active CN110892087B (zh) | 2017-06-20 | 2018-06-13 | 具有高可电阻点焊性的经锌涂覆的钢板 |
Country Status (16)
Country | Link |
---|---|
US (2) | US11649522B2 (zh) |
EP (2) | EP3892748A1 (zh) |
JP (1) | JP7142037B2 (zh) |
KR (1) | KR102306471B1 (zh) |
CN (1) | CN110892087B (zh) |
BR (2) | BR112019025057B8 (zh) |
CA (1) | CA3063835C (zh) |
ES (1) | ES2886223T3 (zh) |
HU (1) | HUE056466T2 (zh) |
MA (2) | MA49449B1 (zh) |
MX (1) | MX2019015511A (zh) |
PL (1) | PL3642379T3 (zh) |
RU (1) | RU2732714C1 (zh) |
UA (1) | UA125620C2 (zh) |
WO (2) | WO2018234839A1 (zh) |
ZA (1) | ZA201907399B (zh) |
Cited By (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN114686651A (zh) * | 2020-12-31 | 2022-07-01 | 通用汽车环球科技运作有限责任公司 | 具有降低的液态金属致脆(lme)敏感性的锌涂覆的钢 |
CN115151368A (zh) * | 2020-02-25 | 2022-10-04 | 株式会社神户制钢所 | 电阻点焊方法 |
CN115516117A (zh) * | 2020-05-07 | 2022-12-23 | 安赛乐米塔尔公司 | 钢的退火方法 |
CN116209781A (zh) * | 2020-09-30 | 2023-06-02 | 日本制铁株式会社 | 钢板 |
CN116463547A (zh) * | 2022-06-30 | 2023-07-21 | 宝山钢铁股份有限公司 | 一种120公斤级超高强度镀锌钢板及其制造方法 |
Families Citing this family (17)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2020158063A1 (ja) | 2019-01-29 | 2020-08-06 | Jfeスチール株式会社 | 高強度溶融亜鉛めっき鋼板およびその製造方法 |
JP7059979B2 (ja) * | 2019-04-25 | 2022-04-26 | Jfeスチール株式会社 | スポット溶接部材 |
JP7424932B2 (ja) * | 2020-07-22 | 2024-01-30 | 株式会社神戸製鋼所 | 抵抗スポット溶接方法 |
MX2022015391A (es) * | 2020-06-08 | 2023-01-16 | Nippon Steel Corp | Lamina de acero y metodo para producir la misma. |
MX2023005389A (es) | 2020-11-11 | 2023-05-19 | Nippon Steel Corp | Lamina de acero y metodo para producir la misma. |
EP4267776A1 (en) * | 2020-12-23 | 2023-11-01 | voestalpine Stahl GmbH | A zinc or zinc-alloy coated strip or steel with improved zinc adhesion |
CN116723908A (zh) * | 2021-01-08 | 2023-09-08 | 日本制铁株式会社 | 焊接接头及汽车部件 |
DE102021107330A1 (de) | 2021-03-24 | 2022-09-29 | Thyssenkrupp Steel Europe Ag | Beschichtetes Stahlflachprodukt und Verfahren zu seiner Herstellung |
CN113333986A (zh) * | 2021-05-31 | 2021-09-03 | 帝国理工创新有限公司 | 一种快速成形异种合金拼焊板部件的方法 |
WO2022264585A1 (ja) * | 2021-06-15 | 2022-12-22 | Jfeスチール株式会社 | 高強度亜鉛めっき鋼板および部材ならびにそれらの製造方法 |
KR20240007934A (ko) * | 2021-06-15 | 2024-01-17 | 제이에프이 스틸 가부시키가이샤 | 고강도 아연 도금 강판 및 부재 그리고 그들의 제조 방법 |
KR20220169497A (ko) * | 2021-06-18 | 2022-12-28 | 주식회사 포스코 | 굽힘 특성이 우수한 고항복비 초고강도 강판 및 그 제조방법 |
CN113414516B (zh) * | 2021-07-07 | 2022-09-09 | 北京科技大学 | 一种先进高强钢点焊焊接性的预判评价方法 |
JPWO2023054705A1 (zh) * | 2021-10-01 | 2023-04-06 | ||
JPWO2023054717A1 (zh) * | 2021-10-01 | 2023-04-06 | ||
CN115156845B (zh) * | 2022-06-16 | 2024-06-21 | 唐山钢铁集团高强汽车板有限公司 | 一种防止镀层粘辊的镀锌热成形钢生产方法 |
CN116463546B (zh) * | 2022-06-30 | 2024-01-09 | 宝山钢铁股份有限公司 | 一种100公斤级超高强度镀锌钢板及其制造方法 |
Citations (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US6558815B1 (en) * | 1999-11-08 | 2003-05-06 | Kawasaki Steel Corporation | Hot dip Galvanized steel plate excellent in balance of strength and ductility and in adhesiveness between steel and plating layer |
CN101336308A (zh) * | 2006-01-30 | 2008-12-31 | 新日本制铁株式会社 | 成形性及镀覆性优良的高强度热浸镀锌钢板和高强度合金化热浸镀锌钢板及其制造方法和制造装置 |
US20120018060A1 (en) * | 2009-03-31 | 2012-01-26 | Jfe Steel Corporation | High-strength galvanized steel sheet and method for manufacturing the same |
CN102639739A (zh) * | 2009-11-30 | 2012-08-15 | 新日本制铁株式会社 | 耐氢脆化特性优异的最大拉伸强度为900MPa以上的高强度钢板及其制造方法 |
CN103649343A (zh) * | 2011-06-07 | 2014-03-19 | 安赛乐米塔尔研发有限公司 | 涂覆有锌或锌合金的经冷轧钢板、其制造方法及所述钢板的用途 |
CN103827335A (zh) * | 2011-09-30 | 2014-05-28 | 新日铁住金株式会社 | 镀锌钢板及其制造方法 |
CN104769138A (zh) * | 2012-09-06 | 2015-07-08 | 安赛乐米塔尔研发有限公司 | 用于制造经压制硬化的涂覆钢部件的方法和能够用于制造所述部件的预涂覆钢板 |
EP2990501A1 (en) * | 2013-04-26 | 2016-03-02 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Alloyed hot-dip galvanized steel sheet for hot stamping use, and method for manufacturing steel part |
CN106661652A (zh) * | 2014-07-03 | 2017-05-10 | 安赛乐米塔尔公司 | 用于制造超高强度涂覆或未涂覆钢板的方法和获得的板 |
Family Cites Families (16)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US5857141A (en) | 1996-06-11 | 1999-01-05 | Illinois Tool Works Inc. | Metal-core weld wire for welding galvanized steels |
JP4173990B2 (ja) | 2002-12-27 | 2008-10-29 | 新日本製鐵株式会社 | 溶接用亜鉛系合金めっき鋼材およびその電縫鋼管 |
JP2005002415A (ja) | 2003-06-12 | 2005-01-06 | Nippon Steel Corp | 溶接性に優れた溶融Zn系めっき鋼材 |
JP4303655B2 (ja) | 2004-07-29 | 2009-07-29 | 新日本製鐵株式会社 | 溶接部の耐食性および耐亜鉛脆化割れ性に優れた亜鉛めっき鋼板の溶接方法 |
JP4741376B2 (ja) * | 2005-01-31 | 2011-08-03 | 新日本製鐵株式会社 | 外観が良好な高強度合金化溶融亜鉛めっき鋼板及びその製造方法と製造設備 |
JP2006265671A (ja) | 2005-03-25 | 2006-10-05 | Nisshin Steel Co Ltd | 加工性及び耐溶融金属脆化割れ性に優れた合金化溶融亜鉛めっき高張力鋼板 |
EP1832667A1 (fr) | 2006-03-07 | 2007-09-12 | ARCELOR France | Procédé de fabrication de tôles d'acier à très hautes caractéristiques de résistance, de ductilité et de tenacité, et tôles ainsi produites |
JP5223366B2 (ja) * | 2007-02-08 | 2013-06-26 | Jfeスチール株式会社 | 成形性および溶接性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法 |
EP1990431A1 (fr) * | 2007-05-11 | 2008-11-12 | ArcelorMittal France | Procédé de fabrication de tôles d'acier laminées à froid et recuites à très haute résistance, et tôles ainsi produites |
EP2009129A1 (en) | 2007-06-29 | 2008-12-31 | ArcelorMittal France | Process for manufacturing a galvannealed steel sheet by DFF regulation |
EP2009128A1 (en) | 2007-06-29 | 2008-12-31 | ArcelorMittal France | Galvanized or galvannealed silicon steel |
JP5499664B2 (ja) * | 2009-11-30 | 2014-05-21 | 新日鐵住金株式会社 | 疲労耐久性に優れた引張最大強度900MPa以上の高強度冷延鋼板及びその製造方法、並びに、高強度亜鉛めっき鋼板及びその製造方法 |
RU2470097C2 (ru) | 2010-09-07 | 2012-12-20 | Государственное образовательное учреждение высшего профессионального образования "Казанский государственный энергетический университет" (КГЭУ) | Способ изготовления фольги из чистого ферромагнитного металла и устройство для его осуществления (варианты) |
EP2644737A4 (en) | 2010-11-26 | 2016-01-06 | Jfe Steel Corp | FIRE-ADJUSTED PLATED STEEL PLATE ON AL-ZN BASE |
JP5936390B2 (ja) | 2011-02-28 | 2016-06-22 | 日新製鋼株式会社 | 溶融Zn−Al−Mg系めっき鋼板および製造方法 |
KR20150073005A (ko) * | 2013-12-20 | 2015-06-30 | 주식회사 포스코 | 용접부 균열 저항성이 우수한 오스테나이트계 아연도금강판 및 이의 제조방법 |
-
2017
- 2017-06-20 WO PCT/IB2017/000753 patent/WO2018234839A1/en active Application Filing
-
2018
- 2018-06-13 MA MA49449A patent/MA49449B1/fr unknown
- 2018-06-13 ES ES18735715T patent/ES2886223T3/es active Active
- 2018-06-13 CA CA3063835A patent/CA3063835C/en active Active
- 2018-06-13 UA UAA202000315A patent/UA125620C2/uk unknown
- 2018-06-13 MA MA054413A patent/MA54413A/fr unknown
- 2018-06-13 EP EP21177833.7A patent/EP3892748A1/en active Pending
- 2018-06-13 EP EP18735715.7A patent/EP3642379B1/en active Active
- 2018-06-13 US US16/614,734 patent/US11649522B2/en active Active
- 2018-06-13 BR BR112019025057A patent/BR112019025057B8/pt active IP Right Grant
- 2018-06-13 HU HUE18735715A patent/HUE056466T2/hu unknown
- 2018-06-13 BR BR122023007818A patent/BR122023007818B8/pt active IP Right Grant
- 2018-06-13 CN CN201880037315.XA patent/CN110892087B/zh active Active
- 2018-06-13 WO PCT/IB2018/054306 patent/WO2018234938A1/en active Application Filing
- 2018-06-13 PL PL18735715T patent/PL3642379T3/pl unknown
- 2018-06-13 RU RU2020101918A patent/RU2732714C1/ru active
- 2018-06-13 KR KR1020197036977A patent/KR102306471B1/ko active IP Right Grant
- 2018-06-13 MX MX2019015511A patent/MX2019015511A/es unknown
- 2018-06-13 JP JP2019570524A patent/JP7142037B2/ja active Active
-
2019
- 2019-11-07 ZA ZA2019/07399A patent/ZA201907399B/en unknown
-
2023
- 2023-05-10 US US18/195,578 patent/US20230272502A1/en active Pending
Patent Citations (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US6558815B1 (en) * | 1999-11-08 | 2003-05-06 | Kawasaki Steel Corporation | Hot dip Galvanized steel plate excellent in balance of strength and ductility and in adhesiveness between steel and plating layer |
CN101336308A (zh) * | 2006-01-30 | 2008-12-31 | 新日本制铁株式会社 | 成形性及镀覆性优良的高强度热浸镀锌钢板和高强度合金化热浸镀锌钢板及其制造方法和制造装置 |
US20120018060A1 (en) * | 2009-03-31 | 2012-01-26 | Jfe Steel Corporation | High-strength galvanized steel sheet and method for manufacturing the same |
CN102639739A (zh) * | 2009-11-30 | 2012-08-15 | 新日本制铁株式会社 | 耐氢脆化特性优异的最大拉伸强度为900MPa以上的高强度钢板及其制造方法 |
CN103649343A (zh) * | 2011-06-07 | 2014-03-19 | 安赛乐米塔尔研发有限公司 | 涂覆有锌或锌合金的经冷轧钢板、其制造方法及所述钢板的用途 |
CN103827335A (zh) * | 2011-09-30 | 2014-05-28 | 新日铁住金株式会社 | 镀锌钢板及其制造方法 |
CN104769138A (zh) * | 2012-09-06 | 2015-07-08 | 安赛乐米塔尔研发有限公司 | 用于制造经压制硬化的涂覆钢部件的方法和能够用于制造所述部件的预涂覆钢板 |
US20160017452A1 (en) * | 2012-09-06 | 2016-01-21 | ArcelorMittal Investigación y Desarrollo, S.L. | Process for manufacturing press-hardened coated steel parts and precoated sheets allowing these parts to be manufactured |
EP2990501A1 (en) * | 2013-04-26 | 2016-03-02 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Alloyed hot-dip galvanized steel sheet for hot stamping use, and method for manufacturing steel part |
CN106661652A (zh) * | 2014-07-03 | 2017-05-10 | 安赛乐米塔尔公司 | 用于制造超高强度涂覆或未涂覆钢板的方法和获得的板 |
Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN115151368A (zh) * | 2020-02-25 | 2022-10-04 | 株式会社神户制钢所 | 电阻点焊方法 |
CN115516117A (zh) * | 2020-05-07 | 2022-12-23 | 安赛乐米塔尔公司 | 钢的退火方法 |
CN115516117B (zh) * | 2020-05-07 | 2024-03-08 | 安赛乐米塔尔公司 | 钢的退火方法 |
CN116209781A (zh) * | 2020-09-30 | 2023-06-02 | 日本制铁株式会社 | 钢板 |
CN114686651A (zh) * | 2020-12-31 | 2022-07-01 | 通用汽车环球科技运作有限责任公司 | 具有降低的液态金属致脆(lme)敏感性的锌涂覆的钢 |
CN116463547A (zh) * | 2022-06-30 | 2023-07-21 | 宝山钢铁股份有限公司 | 一种120公斤级超高强度镀锌钢板及其制造方法 |
CN116463547B (zh) * | 2022-06-30 | 2024-01-09 | 宝山钢铁股份有限公司 | 一种120公斤级超高强度镀锌钢板及其制造方法 |
Also Published As
Publication number | Publication date |
---|---|
MA49449A (fr) | 2020-04-29 |
UA125620C2 (uk) | 2022-05-04 |
MA49449B1 (fr) | 2021-10-29 |
ZA201907399B (en) | 2021-09-29 |
CA3063835C (en) | 2022-03-01 |
BR122023007818B8 (pt) | 2023-11-07 |
RU2732714C1 (ru) | 2020-09-22 |
BR122023007818B1 (pt) | 2023-09-19 |
KR20200008142A (ko) | 2020-01-23 |
JP7142037B2 (ja) | 2022-09-26 |
MA54413A (fr) | 2021-10-13 |
KR102306471B1 (ko) | 2021-09-30 |
PL3642379T3 (pl) | 2022-01-03 |
ES2886223T3 (es) | 2021-12-16 |
EP3892748A1 (en) | 2021-10-13 |
BR112019025057A2 (pt) | 2020-06-16 |
JP2020524743A (ja) | 2020-08-20 |
WO2018234938A1 (en) | 2018-12-27 |
US11649522B2 (en) | 2023-05-16 |
US20230272502A1 (en) | 2023-08-31 |
BR112019025057B8 (pt) | 2023-11-07 |
HUE056466T2 (hu) | 2022-02-28 |
CA3063835A1 (en) | 2018-12-27 |
BR112019025057B1 (pt) | 2023-09-12 |
MX2019015511A (es) | 2020-02-24 |
WO2018234839A1 (en) | 2018-12-27 |
EP3642379B1 (en) | 2021-08-04 |
EP3642379A1 (en) | 2020-04-29 |
CN110892087B (zh) | 2022-03-25 |
US20200181729A1 (en) | 2020-06-11 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
CN110892087B (zh) | 具有高可电阻点焊性的经锌涂覆的钢板 | |
JP6388099B1 (ja) | 鋼板、溶融亜鉛めっき鋼板および合金化溶融亜鉛めっき鋼板 | |
US20160017452A1 (en) | Process for manufacturing press-hardened coated steel parts and precoated sheets allowing these parts to be manufactured | |
JP6049516B2 (ja) | 溶接構造部材用高強度めっき鋼板およびその製造法 | |
JPWO2019106894A1 (ja) | 高強度亜鉛めっき鋼板およびその製造方法 | |
CA2786381C (en) | High-strength galvanized steel sheet having excellent formability and spot weldability and method for manufacturing the same | |
JPWO2019106895A1 (ja) | 高強度亜鉛めっき鋼板およびその製造方法 | |
CN110392617B (zh) | 用于将锌涂覆钢板接合的电阻点焊法 | |
JP2019504205A (ja) | めっき性及び溶接性に優れたオーステナイト系溶融アルミニウムめっき鋼板及びその製造方法 | |
KR101630957B1 (ko) | 점용접성 및 도금성이 우수한 고망간강 합금아연도금강판 및 이의 제조방법 | |
KR20150073317A (ko) | 용접성이 우수한 아연도금강판 및 이의 제조 방법 | |
US20230257862A1 (en) | Annealing method of steel | |
KR102065230B1 (ko) | 점 용접성이 우수한 초고강도 고망간 아연도금강판 및 그의 제조방법 | |
JP4580403B2 (ja) | 深絞り用溶融めっき高強度鋼板及びその製造方法 | |
WO2022202020A1 (ja) | 鋼板及び溶接継手 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
PB01 | Publication | ||
PB01 | Publication | ||
SE01 | Entry into force of request for substantive examination | ||
SE01 | Entry into force of request for substantive examination | ||
GR01 | Patent grant | ||
GR01 | Patent grant |