EP2668302A1 - High strength multi-phase steel having excellent forming properties - Google Patents
High strength multi-phase steel having excellent forming propertiesInfo
- Publication number
- EP2668302A1 EP2668302A1 EP11822842.8A EP11822842A EP2668302A1 EP 2668302 A1 EP2668302 A1 EP 2668302A1 EP 11822842 A EP11822842 A EP 11822842A EP 2668302 A1 EP2668302 A1 EP 2668302A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- steel
- content
- temperature
- hot
- strip
- 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 134
- 239000010959 steel Substances 0.000 title claims abstract description 134
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 31
- 229910052742 iron Inorganic materials 0.000 claims abstract description 16
- 238000010276 construction Methods 0.000 claims abstract description 4
- 238000000034 method Methods 0.000 claims description 56
- 238000000137 annealing Methods 0.000 claims description 46
- 238000001816 cooling Methods 0.000 claims description 35
- 229910052719 titanium Inorganic materials 0.000 claims description 23
- 229910052796 boron Inorganic materials 0.000 claims description 19
- 229910052758 niobium Inorganic materials 0.000 claims description 17
- 238000004519 manufacturing process Methods 0.000 claims description 14
- 238000010438 heat treatment Methods 0.000 claims description 5
- 229910052750 molybdenum Inorganic materials 0.000 claims description 5
- 238000007598 dipping method Methods 0.000 claims description 4
- 238000003618 dip coating Methods 0.000 claims 1
- 230000008569 process Effects 0.000 description 48
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 35
- 239000010936 titanium Substances 0.000 description 26
- 230000000694 effects Effects 0.000 description 24
- 230000015572 biosynthetic process Effects 0.000 description 23
- 229910045601 alloy Inorganic materials 0.000 description 22
- 239000000956 alloy Substances 0.000 description 22
- 238000005275 alloying Methods 0.000 description 22
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 19
- 229910052799 carbon Inorganic materials 0.000 description 19
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 18
- 229910001566 austenite Inorganic materials 0.000 description 18
- 229910052757 nitrogen Inorganic materials 0.000 description 18
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 17
- 239000010955 niobium Substances 0.000 description 17
- 229910052760 oxygen Inorganic materials 0.000 description 17
- 239000001301 oxygen Substances 0.000 description 17
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 16
- 239000011651 chromium Substances 0.000 description 16
- 229910000734 martensite Inorganic materials 0.000 description 16
- 229910000859 α-Fe Inorganic materials 0.000 description 16
- 239000000463 material Substances 0.000 description 14
- 229910052804 chromium Inorganic materials 0.000 description 13
- 239000000203 mixture Substances 0.000 description 13
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 12
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 11
- 238000007792 addition Methods 0.000 description 11
- 229910052782 aluminium Inorganic materials 0.000 description 11
- 229910052739 hydrogen Inorganic materials 0.000 description 11
- 239000001257 hydrogen Substances 0.000 description 11
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 11
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 10
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 10
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 10
- 229910001563 bainite Inorganic materials 0.000 description 10
- 229910052710 silicon Inorganic materials 0.000 description 10
- 239000010703 silicon Substances 0.000 description 10
- 229910052720 vanadium Inorganic materials 0.000 description 10
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 9
- 150000004767 nitrides Chemical class 0.000 description 9
- 229910052698 phosphorus Inorganic materials 0.000 description 9
- 239000011574 phosphorus Substances 0.000 description 9
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 8
- -1 niobium carbides Chemical class 0.000 description 8
- 238000012545 processing Methods 0.000 description 8
- 230000002829 reductive effect Effects 0.000 description 8
- 239000011701 zinc Substances 0.000 description 8
- 229910052725 zinc Inorganic materials 0.000 description 8
- 238000006243 chemical reaction Methods 0.000 description 7
- 230000029142 excretion Effects 0.000 description 7
- 239000011572 manganese Substances 0.000 description 7
- 239000002244 precipitate Substances 0.000 description 7
- 230000009466 transformation Effects 0.000 description 7
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 6
- 239000010949 copper Substances 0.000 description 6
- 150000001247 metal acetylides Chemical class 0.000 description 6
- 238000007670 refining Methods 0.000 description 6
- 238000005096 rolling process Methods 0.000 description 6
- 229910052717 sulfur Inorganic materials 0.000 description 6
- 239000011593 sulfur Substances 0.000 description 6
- 238000012360 testing method Methods 0.000 description 6
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 5
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 5
- 229910052802 copper Inorganic materials 0.000 description 5
- 238000009792 diffusion process Methods 0.000 description 5
- 238000005098 hot rolling Methods 0.000 description 5
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 4
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 4
- 230000008901 benefit Effects 0.000 description 4
- 238000005246 galvanizing Methods 0.000 description 4
- 229910052748 manganese Inorganic materials 0.000 description 4
- 239000011159 matrix material Substances 0.000 description 4
- 239000011733 molybdenum Substances 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 238000004881 precipitation hardening Methods 0.000 description 4
- 238000001953 recrystallisation Methods 0.000 description 4
- 239000006104 solid solution Substances 0.000 description 4
- 230000007797 corrosion Effects 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 230000007547 defect Effects 0.000 description 3
- 230000003111 delayed effect Effects 0.000 description 3
- 238000010586 diagram Methods 0.000 description 3
- 238000009826 distribution Methods 0.000 description 3
- 230000009977 dual effect Effects 0.000 description 3
- 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 3
- 230000006911 nucleation Effects 0.000 description 3
- 238000010899 nucleation Methods 0.000 description 3
- 238000005204 segregation Methods 0.000 description 3
- 238000003466 welding Methods 0.000 description 3
- PXFBZOLANLWPMH-UHFFFAOYSA-N 16-Epiaffinine Natural products C1C(C2=CC=CC=C2N2)=C2C(=O)CC2C(=CC)CN(C)C1C2CO PXFBZOLANLWPMH-UHFFFAOYSA-N 0.000 description 2
- PNEYBMLMFCGWSK-UHFFFAOYSA-N Alumina Chemical class [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 2
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 2
- 238000010521 absorption reaction Methods 0.000 description 2
- 238000013459 approach Methods 0.000 description 2
- 229910001567 cementite Inorganic materials 0.000 description 2
- 239000011362 coarse particle Substances 0.000 description 2
- 239000010960 cold rolled steel Substances 0.000 description 2
- 238000005097 cold rolling Methods 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 150000002431 hydrogen Chemical class 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- VCTOKJRTAUILIH-UHFFFAOYSA-N manganese(2+);sulfide Chemical class [S-2].[Mn+2] VCTOKJRTAUILIH-UHFFFAOYSA-N 0.000 description 2
- 239000000155 melt Substances 0.000 description 2
- ZLANVVMKMCTKMT-UHFFFAOYSA-N methanidylidynevanadium(1+) Chemical class [V+]#[C-] ZLANVVMKMCTKMT-UHFFFAOYSA-N 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 229910001562 pearlite Inorganic materials 0.000 description 2
- 235000019362 perlite Nutrition 0.000 description 2
- 239000010451 perlite Substances 0.000 description 2
- 230000008092 positive effect Effects 0.000 description 2
- 238000004886 process control Methods 0.000 description 2
- 230000009467 reduction Effects 0.000 description 2
- 238000003303 reheating Methods 0.000 description 2
- 230000000717 retained effect Effects 0.000 description 2
- LIVNPJMFVYWSIS-UHFFFAOYSA-N silicon monoxide Chemical class [Si-]#[O+] LIVNPJMFVYWSIS-UHFFFAOYSA-N 0.000 description 2
- 229910052814 silicon oxide Inorganic materials 0.000 description 2
- 238000007711 solidification Methods 0.000 description 2
- 230000008023 solidification Effects 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- 238000009628 steelmaking Methods 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- 230000035882 stress Effects 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 150000004763 sulfides Chemical class 0.000 description 2
- 238000005496 tempering Methods 0.000 description 2
- 239000011573 trace mineral Substances 0.000 description 2
- 235000013619 trace mineral Nutrition 0.000 description 2
- 230000007704 transition Effects 0.000 description 2
- 238000011144 upstream manufacturing Methods 0.000 description 2
- 238000009489 vacuum treatment Methods 0.000 description 2
- 239000013585 weight reducing agent Substances 0.000 description 2
- 229910000521 B alloy Inorganic materials 0.000 description 1
- 229910052582 BN Inorganic materials 0.000 description 1
- PZNSFCLAULLKQX-UHFFFAOYSA-N Boron nitride Chemical compound N#B PZNSFCLAULLKQX-UHFFFAOYSA-N 0.000 description 1
- 229910052684 Cerium Inorganic materials 0.000 description 1
- 229910000885 Dual-phase steel Inorganic materials 0.000 description 1
- 229910000915 Free machining steel Inorganic materials 0.000 description 1
- 229910003092 TiS2 Inorganic materials 0.000 description 1
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 1
- PGTXKIZLOWULDJ-UHFFFAOYSA-N [Mg].[Zn] Chemical compound [Mg].[Zn] PGTXKIZLOWULDJ-UHFFFAOYSA-N 0.000 description 1
- 230000006978 adaptation Effects 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 230000003679 aging effect Effects 0.000 description 1
- JZQOJFLIJNRDHK-CMDGGOBGSA-N alpha-irone Chemical compound CC1CC=C(C)C(\C=C\C(C)=O)C1(C)C JZQOJFLIJNRDHK-CMDGGOBGSA-N 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 230000001174 ascending effect Effects 0.000 description 1
- 125000004429 atom Chemical group 0.000 description 1
- FFBHFFJDDLITSX-UHFFFAOYSA-N benzyl N-[2-hydroxy-4-(3-oxomorpholin-4-yl)phenyl]carbamate Chemical compound OC1=C(NC(=O)OCC2=CC=CC=C2)C=CC(=C1)N1CCOCC1=O FFBHFFJDDLITSX-UHFFFAOYSA-N 0.000 description 1
- 229910052790 beryllium Inorganic materials 0.000 description 1
- ATBAMAFKBVZNFJ-UHFFFAOYSA-N beryllium atom Chemical compound [Be] ATBAMAFKBVZNFJ-UHFFFAOYSA-N 0.000 description 1
- 238000005266 casting Methods 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
- 150000001875 compounds Chemical class 0.000 description 1
- PMHQVHHXPFUNSP-UHFFFAOYSA-M copper(1+);methylsulfanylmethane;bromide Chemical compound Br[Cu].CSC PMHQVHHXPFUNSP-UHFFFAOYSA-M 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000001934 delay Effects 0.000 description 1
- 230000001419 dependent effect Effects 0.000 description 1
- 238000006477 desulfuration reaction Methods 0.000 description 1
- 230000023556 desulfurization Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000001627 detrimental effect Effects 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 230000006355 external stress Effects 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 238000007654 immersion Methods 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 230000005764 inhibitory process Effects 0.000 description 1
- 238000007689 inspection Methods 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- AMWRITDGCCNYAT-UHFFFAOYSA-L manganese oxide Inorganic materials [Mn].O[Mn]=O.O[Mn]=O AMWRITDGCCNYAT-UHFFFAOYSA-L 0.000 description 1
- PPNAOCWZXJOHFK-UHFFFAOYSA-N manganese(2+);oxygen(2-) Chemical class [O-2].[Mn+2] PPNAOCWZXJOHFK-UHFFFAOYSA-N 0.000 description 1
- 230000010534 mechanism of action Effects 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 229910001392 phosphorus oxide Inorganic materials 0.000 description 1
- LFGREXWGYUGZLY-UHFFFAOYSA-N phosphoryl Chemical class [P]=O LFGREXWGYUGZLY-UHFFFAOYSA-N 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 230000001681 protective effect Effects 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 230000006798 recombination Effects 0.000 description 1
- 238000005215 recombination Methods 0.000 description 1
- 239000002893 slag Substances 0.000 description 1
- 230000003068 static effect Effects 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- CADICXFYUNYKGD-UHFFFAOYSA-N sulfanylidenemanganese Chemical compound [Mn]=S CADICXFYUNYKGD-UHFFFAOYSA-N 0.000 description 1
- 230000000930 thermomechanical effect Effects 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Classifications
-
- 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
- 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
- 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
- C21D1/185—Hardening; Quenching with or without subsequent tempering from an intercritical temperature
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
-
- 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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/28—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
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
-
- 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
Definitions
- the invention relates to a high-strength multiphase steel with dual, bainite or
- dual phase steels which consist of a ferritic basic structure into which a martensitic second phase and
- Hot or cold rolled complex-phase steels are steels which contain small amounts of martensite, retained austenite and / or pearlite in a ferritic / bainitic matrix, whereby extreme grain refinement is caused by retarded recrystallization or precipitation of micro-alloying elements.
- Hot-rolled ferritic-bainitic steels are steels that contain bainite or solidified bainite in a matrix of ferrite and / or solidified ferrite.
- the solidification of the matrix is effected by a high dislocation density, by grain refining and the excretion of micro-alloying elements.
- Hot rolled or cold rolled bainitic steels are steels characterized by a very high yield strength and tensile strength at a sufficiently high elongation for cold forming processes. Due to the chemical composition a good weldability is given.
- the microstructure typically consists of bainite. Occasionally, small amounts of other phases, such as. As martensite and ferrite.
- Hot rolled martensitic steels are steels produced by
- thermomechanical rolling containing small amounts of ferrite and / or bainite in a matrix of martensite.
- the steel grade is characterized by a very high yield strength and tensile strength at a sufficiently high elongation for cold forming processes.
- the martensitic steels have the highest
- TRB ® s with multi-phase structure is currently known alloys and continuous annealing lines available for widely varying thicknesses, however, not without limitations such. B. for the heat treatment before cold rolling, possible. In areas of different sheet thickness can be due to one of the common
- Temperaturpreheat occurring process windows are not a homogeneous multi-phase structure in cold- as well as hot-rolled steel strips can be adjusted.
- Process parameters such as throughput speed, annealing temperatures and
- Cooling speed adjusted according to the required mechanical and technological properties with the necessary structure.
- the hot or cold strip is heated in a continuous annealing furnace to a temperature such that the required microstructure formation occurs during cooling.
- a continuous annealing furnace to a temperature such that the required microstructure formation occurs during cooling.
- the annealing treatment is usually carried out in a continuous annealing furnace upstream of the galvanizing bath.
- the required microstructure of the hot strip may also be adjusted in the continuous furnace during the annealing treatment, in order to achieve the required mechanical properties.
- a narrow process window means that, depending on the cross section of the strip to be annealed, the process parameters have to be adjusted in order to achieve a homogenous process
- a homogeneous temperature distribution is just at different thicknesses in the
- Transition range from one band to another difficult to achieve can lead to alloy compositions with too small process windows in the continuous annealing that z. B. the thinner strip is either driven too slowly through the oven and thereby productivity is lowered, or that the thicker strip is driven too fast through the oven and the required annealing temperature and thus the required structure is not achieved. The consequences are increased rejects or even customer complaints.
- the decisive process parameter is thus the setting of the speed in the continuous annealing, since the phase transformation is temperature- and time-controlled.
- a method for producing a steel strip with different thickness over the strip length is z. B. in DE 100 37 867 A1.
- the goal of achieving the final mechanical-technological properties in a narrow range over bandwidth and strip length by the controlled adjustment of the volume fractions of the structural phases has the highest priority and is therefore only possible through an enlarged process window.
- the known alloy concepts for honed steels are characterized by too narrow a process window and are therefore unsuitable for solving the present problem, in particular in flexibly rolled strips. At present, only steels of a strength class are defined with the known alloy concepts
- Cross-sectional areas representable, so that for different strength classes and or cross-sectional areas altered alloy concepts are necessary,
- the invention is therefore based on the object to provide a different alloy concept for a high-strength Mehrphasenstahi with different microstructural compositions, with which the process window for the continuous annealing of hot or
- Cross sections and steel bands with over tape length and possibly bandwidth varying thickness can be produced with the most homogeneous mechanical and technological properties. Furthermore, an alloy concept is to be specified, with which different strength classes can be served. In addition, a method for producing a strip made from this steel is to be specified.
- this object is achieved by a steel with the following contents in% by weight:
- Nb 2 0.005 to ⁇ 0.050
- the steel according to the invention offers the advantage of a significantly enlarged process window in comparison to the known steels. This results in an increased process reliability in the continuous annealing of cold and hot strip with multi-phase structure. Thus, homogenized mechanical-technological properties in the strip can be ensured for pass-annealed hot or cold strips even with different cross sections and otherwise identical process parameters.
- the material produced can be used as a cold as well as a hot strip over a
- Hot dip galvanizing line or a pure continuous annealing system are produced in the dressed and undressed and also in the heat treated state ⁇ intermediate annealing).
- the steel strips produced with the alloy composition according to the invention are distinguished in the production of an honed or bainitic steel by a significantly wider process window in terms of temperature and in comparison
- phase structure be uniform over the belt length. This has a particularly advantageous effect in the annealing of flexibly rolled strips or in the successive annealing of strips of different cross sections, so that very uniform material properties are thereby achieved.
- the basis for achieving a broad process window is the inventive combination of the micro-alloying elements titanium, niobium and boron with optional addition of molybdenum.
- Fine titanium precipitates work in the same way as niobium carbides and together enhance the effect. Titanium binds off the nitrogen, which is therefore no longer available for the formation of boron nitride, whereby the boron alloy can act. In this case, the addition of boron, which is free, causes an increase in the hardenability.
- Boron is one of the elements that is characterized not only by a high degree of hardening but also by a high hardening effect.
- the microstructure becomes more isotropic, because differences in the cooling rates caused by the process control or the geometry of the strip have less influence, which also leads to a larger process window.
- the free boron is capable of a relatively homogeneous microstructure (same
- Microstructural components over the sheet thickness. The same applies to the less pronounced influence of temperature gradients that occur over the length of the strip or in relation to its width.
- Carbon equivalent can be reduced, thereby improving the weldability and to avoid excessive hardening during welding. In resistance spot welding, moreover, the electrode life can be significantly increased.
- vanadium is the high solubility in austenite and the large volume fraction of fine precipitates caused by the low precipitation temperature.
- the effect of the elements in the alloy according to the invention is described in more detail below.
- the multiphase steels are typically chemically designed to combine alloying elements with and without micro-alloying elements. Accompanying elements complete the analysis concept.
- Hydrogen (H) can be the only element that can diffuse through the iron lattice without creating lattice strains. As a result, the hydrogen in the iron grid is relatively mobile and can be absorbed relatively easily during production. Hydrogen can only be taken up in atomic (ionic) form in the iron lattice.
- Hydrogen has a strong embrittlement and preferably diffuses to energy-favorable sites (defects, grain boundaries, etc.). In this case, defects act as hydrogen traps and can significantly increase the residence time of the hydrogen in the material.
- the hydrogen content in the steel should be as low as possible.
- Oxygen (OY) In the molten state, the steel has a relatively high absorption capacity for gases, but at room temperature, oxygen is only soluble in very small quantities.On the same way as hydrogen, oxygen can only diffuse into the material in an atomic form due to the strongly embrittling effect and the Negative effects on aging resistance are attempted as much as possible during the manufacturing process to reduce the oxygen content.
- the oxygen content in the steel should be as low as possible.
- Nitrogen (N) is also a companion element of steelmaking. Steels with free nitrogen tend to have a strong aging effect. The nitrogen already diffuses at low temperatures at dislocations and blocks them. It causes an increase in strength combined with a rapid loss of toughness. Nitrogen bonding in the form of nitrides is possible by alloying aluminum or titanium.
- the nitrogen content is limited to ⁇ 0.0100%, advantageously to ⁇ 0.0090% or optimally to 0.0070% or to unavoidable steel-accompanying amounts.
- sulfur is bound as a trace element in iron ore. It is undesirable in steel (except free-cutting steels), as it tends to segregate severely and has a strong embrittlement. It is therefore attempted to achieve the lowest possible amounts of sulfur in the melt (for example, by a deep vacuum treatment). Furthermore, the existing sulfur is converted by adding manganese into the relatively harmless compound manganese sulfide (MnS).
- the manganese sulfides are often rolled in rows during the rolling process and act as nucleation sites for the transformation. This leads to a line-shaped structure, especially in the case of diffusion-controlled transformation, and can lead to impaired mechanical properties in the case of pronounced bristleness (for example pronounced Martensitzeilen instead of distributed Martensitinseln, no isotropic Maschinenstoffverhaiten, reduced Brüchausdehnung).
- the sulfur content is limited to 0.0100% or unavoidable steel-accompanying quantities.
- Phosphorus (P) is a trace element from iron ore and is found in iron lattice as
- phosphorus is also used in part as a strength carrier.
- the phosphorus content is limited to ⁇ 0.025% or unavoidable, steel-accompanying amounts.
- Alloying elements are usually added to the steel in order to specifically influence certain properties.
- An alloying element in different steels can influence different properties. The effect generally depends strongly on the amount and the solution state in the material.
- chromium in dissolved form can significantly increase the hardenability of steel even in small quantities.
- chromium carbides he can by a
- the hardenability is reduced.
- Carbon (Q is considered to be the most important alloying element in steel, because of its presence the iron is first reduced to steel.) Despite this fact, the carbon content is drastically reduced during steelmaking In dual phase steels for a continuous hot dip refinement, its proportion according to DIN EN 10346 is maximum depending on quality 0.23%, a minimum value is not specified.
- the minimum C content is set to 0.060% and the maximum C content to 0.115%.
- Silicon (Si) binds oxygen during casting, thus reducing segregation and impurities in the steel.
- silicon increases the strength and the yield strength ratio of the ferrite with solid solution hardening with only a slightly decreasing elongation at break.
- Another important effect is that silicon shifts the formation of ferrite to shorter times, thus allowing the formation of sufficient ferrite before quenching.
- the ferrite formation enriches the austenite with carbon and stabilizes it.
- silicon stabilizes austenite in the lower temperature range, especially in the area of bainite formation, by preventing carbidation (no depletion of carbon).
- silicon can diffuse to the surface during annealing and lead to silicon oxides there.
- silicon oxides can interfere with the formation of a closed adhesion layer between steel and zinc (inhibiting layer). This manifests itself in a poor zinc adhesion and undigested places.
- the minimum Si content is set to 0, 100% and the maximum Si content is set to 0.500%.
- Manganese (Mn) is added to almost all steels for desulfurization to convert the harmful sulfur into manganese sulphides. In addition, manganese increases by
- Solid solution solidifies the strength of the ferrite and shifts the a / ß conversion to lower temperatures.
- One main reason for adding manganese into dual-phase steels is the significant improvement in hardenability. Due to the diffusion hindrance, the pearlite and bainite transformation is shifted to longer times and the martensite start temperature is lowered.
- Manganese similar to silicon, can be added at high surface concentrations
- the Mn content is therefore set at 1, 300 to 2,500%.
- Chromium is also a carbide former. If chromium is in carbide form, the
- the Cr content is therefore set at values of 0.280 to 0.480%.
- Molybdenum (Mo) The addition of molybdenum is similar to chromium to improve hardenability. The perlite and bainite transformation is pushed to longer times and the martensite start temperature is lowered.
- Molybdenum also increases the tempering resistance considerably, so that in the zinc bath no
- the Mo content is optionally added depending on the size, the equipment configuration and the microstructure setting, in which case the minimum addition should be 0.050% in order to have an effect. For cost reasons, the Mo content is limited to max. 0.150% set.
- Copper (Cu) The addition of copper can increase the tensile strength as well as the hardenability. In combination with nickel, chromium and phosphorus, copper can form a protective oxide layer on the surface, which can significantly reduce the corrosion rate.
- copper When combined with oxygen, copper can form harmful oxides at the grain boundaries, which can be detrimental to hot working processes in particular.
- the content of copper is therefore limited to unavoidable steel-accompanying quantities.
- Ni nickel
- Sn tin
- Microalloying elements are usually added only in very small amounts ( ⁇ 0.1%). They act in contrast to the alloying elements mainly by excretion formation but can also affect the properties in a dissolved state. Despite the small quantity additions, micro-alloying elements strongly influence the production conditions as well as the processing and final properties.
- micro-alloying elements carbide and nitride formers which are generally soluble in the iron lattice are used. A formation of carbonitrides is due to the complete solubility "nitrides and carbides vori each other also possible. The tendency to form oxides and sulfides is most pronounced in the micro-alloying elements in general.
- This property can be used positively by binding the generally harmful elements sulfur and oxygen.
- the setting can also have negative effects, if not enough
- Microalloying elements are available for the formation of carbides.
- Typical micro-alloying elements are aluminum, vanadium, titanium, niobium and boron. These elements can be dissolved in the iron lattice and form carbides or nitrides with carbon and nitrogen because of a decrease in the free enthalpy.
- Aluminum (AI) is usually added to the steel to bind the dissolved oxygen in the iron and nitrogen.
- the oxygen and nitrogen is thus converted into aluminum oxides and aluminum nitrides. These excretions may be due to an increase in
- Seed points cause a grain refining and so the toughness properties as well
- Titanium nitrides have a lower formation enthalpy and are therefore formed at higher temperatures.
- the AI content is therefore limited to 0.020 to a maximum of 0.060%.
- Titanium (Ti) forms very stable nitrides (Ti ' N) and sulfides (TiS2) even at high temperatures. These dissolve depending on the nitrogen content in part only in the melt. If the resulting precipitates are not removed with the slag, they form very coarse particles in the material due to the high formation temperature and are generally not conducive to the mechanical properties.
- a positive effect on the toughness results from the setting of the free nitrogen and oxygen.
- titanium protects other micro-alloying elements, such as niobium, from binding with nitrogen. These can then develop their effect optimally.
- Nitrides "caused by the lowering of the oxygen and nitrogen content only at lower temperatures can also cause an effective obstacle to the austenite grain.
- Unbonded titanium forms titanium carbides at temperatures above 1150 ° C and can thus cause grain refinement (inhibition of austenite grain growth, grain refinement through delayed recrystallization and / or increase in the number of nuclei during ⁇ / ⁇ transformation) and precipitation hardening.
- the Ti content therefore has values of more than 0.005 and less than 0.050%.
- Ti is limited to contents of ⁇ 0.045 or 0.040%.
- Niobium (Nb) causes a strong grain refining as it is most effective of all
- Niobium carbides form from about 1200 ° C. In combination with titanium, which sets the nitrogen as already described, niobium can be formed by carbide formation in the lower part
- niobium Another effect of niobium is the retardation of the ⁇ / ß conversion and the
- Precipitation hardening can thus become effective especially for steels with a low C content (greater supersaturation possible) and during hot forming processes (deformation-induced precipitation).
- the Nb content is therefore limited to values between 0.005 and 0.050%, with the maximum contents being advantageously restricted to ⁇ 0.045 or 0.040%.
- Vanadium (V) The carbide as well as the nitride formation of vanadium first settles
- Austenite grain growth is not inhibited by the late release of vanadium carbides.
- vanadium is its high solubility in austenite and its low solubility
- vanadium content is limited to unavoidable steel accompanying amounts.
- Nitrogen is in ascending order more affine to beryllium, aluminum, cerium, titanium and zirconium. Especially titanium can guarantee the setting of the entire nitrogen. Aluminum is less suitable.
- boron in the dissolved state in very small amounts leads to a significant improvement in hardenability.
- the mechanism of action of boron can be described as boron atoms preferentially attach to the grain boundaries and there, by the
- Hardenability as boron carbides act as seeds on the grain boundaries.
- Boron has a very high affinity for oxygen, which can lead to a lowering of the boron content in areas near the surface (up to 0.5 mm).
- annealing at over 1000 ° C is not recommended. This is also recommended because boron temperatures above 1000 ° C can cause coarse grain formation.
- the B-phase is limited to values of 0.0005 to 0.0060%. However, these values are advantageously below 0.0050 or 0.0040%.
- the annealing temperatures are between 700 and 950 ° C. for the steel according to the invention, so that a partially austenitic (two-phase area) or a fully austenitic structure (austenite area) is achieved, depending on the structure to be achieved (complex phase structure).
- the hot-dip coated material can be produced both as a hot strip, as a cold rolled hot strip or cold strip in the dressed (cold rolled) or stretch bent state (undressed).
- Steel strips in the present case as hot strip, cold rolled hot strip or cold strip made from the alloy composition according to the invention, are furthermore distinguished by the
- the hot strip according to the invention with final rolling temperatures in the austenitic region above A C 3 and reel temperatures above
- FIG. 1 shows schematically the process chain for the production of the steels according to the invention
- FIG. 2 shows the results of the hole widening test
- FIG. 3 Examples of analytical differences of the steel according to the invention
- Figure 5 schematically shows the time-temperature curve of the process steps hot rolling
- FIG. 6 ZTU diagram for a steel according to the invention
- FIG. 7 mechanical characteristic values with variation of the rolling degrees
- Figure 8 Overview of the adjustable with the inventive alloy concept
- FIG. 1 shows schematically the process chain for the production of the steels according to the invention. Shown are the different process routes relating to the invention. Up to position 5 (pickling), the process route is the same for all steels according to the invention, after which the corresponding processing takes place according to the desired results.
- the pickled hot strip can be galvanized or cold rolled and galvanized. Or it can be annealed cold-rolled and galvanized.
- FIG. 2 shows results of the hole expansion test (relative values in comparison). Shown are the results of the hole widening tests for a steel according to the invention compared to the standard grades. All materials have a sheet thickness of 2.00mm.
- the left panel shows the results for the test ISO TS 16630, right the results for the KWI test (Kaiser Wilhelm Institut). It can be seen that the steels according to the invention, regardless of the type of processing the best
- Process 1 here corresponds to annealing, for example, on a hot-dip galvanizing with a combined directly fired furnace and radiant tube furnace.
- Process 2 corresponds, for example, to process control in a continuous annealing plant.
- a reheating of the steel can optionally be achieved directly in front of the zinc bath by means of an induction furnace. Due to the different sensed temperature guides within the specified range, different characteristic values or even different ones result
- FIG. 3 shows the relevant alloying elements of the steel according to the invention in comparison with steels of the same quality which correspond to the prior art.
- the main difference lies in the Carbon content that is in the overperature range.
- steels that are individually micro-alloyed with Nb, Ti and B, but not in this combination are individually micro-alloyed with Nb, Ti and B, but not in this combination.
- Figure 4 shows the mechanical characteristics of the steel according to the invention in comparison with those of the prior art. All characteristic values correspond to the normative specification.
- FIG. 5 schematically shows the time-temperature profile of the process steps of hot rolling and continuous annealing of strips of the alloy composition according to the invention. Shown is the time- and temperature-dependent conversion for the hot rolling process as well as for a heat treatment after cold rolling. Of particular interest here is the shift of the ferrite nose at later times. This opens up the potential for complex-phase steels and bainitic steels.
- FIG. 6 shows a ZTU diagram for a steel according to the invention.
- the determined ZTU diagram with the corresponding chemical composition and the Ad and A C 3 temperature is shown.
- FIG. 7 shows the mechanical characteristic values with the same parameters of continuously annealed strips with variation of the rolling degrees or different workpiece thickness. Shown are the characteristics of tensile strength, yield strength and elongation at break depending on selected degrees of reduction. Only the tensile strength increases slightly with increasing Abwalzgrad. All values are in the range of the standard for a HCT780XD and show that even with different sheet thicknesses after the continuous annealing practically identical mechanical properties are present.
- FIG. 8 shows an overview of the strength classes which can be set using the alloy concept according to the invention.
- the alloy composition used corresponds to that shown in FIG. Shown are the differently processed steel strips with their characteristic values and Gefugezusammen deren. This clearly indicates the wide range of adjustable strength classes for hot and cold strip with the resulting microstructure levels depending on the process steps carried out and the set process parameters.
- Figure 9 shows schematically the temperature-time courses in the annealing
- Variation 1 shows the annealing and cooling of the cold-rolled or hot-rolled steel strip produced in a continuous annealing plant.
- the annealed steel strip is then s cooled from the annealing temperature at a cooling rate between 15 and 100 ° C / up to an intermediate temperature of 200 to 250 D C.
- the steel strip is cooled at a cooling rate of 2 and 30 ° C / s until it reaches room temperature in air or the cooling at a cooling rate between 15 and 100 ° C / s is maintained up to room temperature, ie the
- Variant 2 shows the process according to variant 1, but the cooling of the steel strip for the purpose of hot dip finishing is briefly interrupted when the hot dipping vessel is run through, in order to subsequently cool it with a
- Cooling rate between 15 and 100 ° C / s to an intermediate temperature of 200 to 250 a C continue. Subsequently, the steel strip is cooled at a cooling rate of 2 and 30 ° C / s until it reaches room temperature in air.
- Variant 3 (FIG. 9 c) likewise shows the process according to variant 1 in a
- Hot dip finishing however, the cooling of the steel strip is interrupted by a brief pause (i to 20 s) at an intermediate temperature of 200 to 250 ° C and reheated (to about 420-470 ° C) to the temperature necessary for hot dipping , Subsequently, the steel strip is cooled to an intermediate temperature of 200 to 250 ° C. At a cooling rate of 2 and 30 ° C / s, the final cooling of the steel strip takes place until air reaches the room temperature.
Abstract
Description
Claims
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE102011010256 | 2011-01-26 | ||
DE102011117572A DE102011117572A1 (en) | 2011-01-26 | 2011-10-25 | High-strength multiphase steel with excellent forming properties |
PCT/DE2011/002094 WO2012100762A1 (en) | 2011-01-26 | 2011-11-30 | High strength multi-phase steel having excellent forming properties |
Publications (2)
Publication Number | Publication Date |
---|---|
EP2668302A1 true EP2668302A1 (en) | 2013-12-04 |
EP2668302B1 EP2668302B1 (en) | 2018-06-06 |
Family
ID=46579740
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP11822842.8A Active EP2668302B1 (en) | 2011-01-26 | 2011-11-30 | Method for manufacturing a strip from a high strength multi-phase steel having excellent forming properties |
Country Status (6)
Country | Link |
---|---|
US (1) | US20140034196A1 (en) |
EP (1) | EP2668302B1 (en) |
KR (1) | KR101845321B1 (en) |
DE (1) | DE102011117572A1 (en) |
RU (1) | RU2581940C2 (en) |
WO (1) | WO2012100762A1 (en) |
Families Citing this family (13)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE102012006017A1 (en) | 2012-03-20 | 2013-09-26 | Salzgitter Flachstahl Gmbh | High strength multiphase steel and method of making a strip of this steel |
DE102014017273A1 (en) | 2014-11-18 | 2016-05-19 | Salzgitter Flachstahl Gmbh | High strength air hardening multiphase steel with excellent processing properties and method of making a strip of this steel |
DE102014017274A1 (en) * | 2014-11-18 | 2016-05-19 | Salzgitter Flachstahl Gmbh | Highest strength air hardening multiphase steel with excellent processing properties and method of making a strip from this steel |
DE102015111177A1 (en) * | 2015-07-10 | 2017-01-12 | Salzgitter Flachstahl Gmbh | High strength multi-phase steel and method of making a cold rolled steel strip therefrom |
DE202015104790U1 (en) | 2015-07-17 | 2015-12-04 | Salzgitter Flachstahl Gmbh | Hot strip of a bainitic multi-phase steel with a Zn-Mg-Al coating |
EP3325684B1 (en) * | 2015-07-17 | 2020-03-04 | Salzgitter Flachstahl GmbH | Method for manufacturing a hot-rolled bainitic multiphase steel sheet having a zn-mg-al-coating and a corresponding hot-rolled steel sheet |
CN110283972B (en) * | 2019-07-02 | 2021-06-25 | 天津市琨泰机械制造有限公司 | Steel strip hot galvanizing and multi-strip-iron hot galvanizing comprehensive continuous production line |
CN110527795B (en) * | 2019-07-02 | 2021-06-25 | 天津市琨泰机械制造有限公司 | Many band irons hot-galvanize continuous production line |
EP3816319B1 (en) | 2019-10-29 | 2022-09-14 | Salzgitter Flachstahl GmbH | Method for producing a high strength steel strip with improved adhesion of zinc-based hot dip coatings |
CN111218614B (en) * | 2020-02-11 | 2022-03-18 | 山东钢铁股份有限公司 | Free-cutting steel for connecting rod and manufacturing method thereof |
DE102020203564A1 (en) | 2020-03-19 | 2021-09-23 | Sms Group Gmbh | Process for producing a rolled multiphase steel strip with special properties |
DE102020110319A1 (en) | 2020-04-15 | 2021-10-21 | Salzgitter Flachstahl Gmbh | Process for the production of a steel strip with a multiphase structure and steel strip added |
KR20230045648A (en) * | 2021-09-27 | 2023-04-05 | 주식회사 포스코 | High-strength and high-thickness steel sheet having excellent hole expandability and ductility and mathod for manufacturing thereof |
Family Cites Families (18)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
GB1344460A (en) * | 1969-12-30 | 1974-01-23 | Nippon Steel Corp | Method of and apparatus for producing low-carbon cold steel sheet |
AU530384B2 (en) * | 1979-06-28 | 1983-07-14 | Nippon Kokan Kabushiki Kaisha | Controlled cooling of steel strip to effect continuous annealing |
JPS60174852A (en) | 1984-02-18 | 1985-09-09 | Kawasaki Steel Corp | Cold rolled steel sheet having composite structure and superior deep drawability |
JP3365632B2 (en) | 1991-03-15 | 2003-01-14 | 新日本製鐵株式会社 | High-strength cold-rolled steel sheet and hot-dip galvanized high-strength cold-rolled steel sheet having good formability and methods for producing them |
US5356494A (en) | 1991-04-26 | 1994-10-18 | Kawasaki Steel Corporation | High strength cold rolled steel sheet having excellent non-aging property at room temperature and suitable for drawing and method of producing the same |
DE19520541C2 (en) * | 1995-06-03 | 1999-01-14 | Bwg Bergwerk Walzwerk | Method and device for correcting a rolled metal strip which is bent horizontally in the strip plane, in particular a metal strip with a strip thickness of 0.5 mm to 2.0 mm |
US6228183B1 (en) * | 1997-07-28 | 2001-05-08 | Exxonmobil Upstream Research Company | Ultra-high strength, weldable, boron-containing steels with superior toughness |
DE19936151A1 (en) * | 1999-07-31 | 2001-02-08 | Thyssenkrupp Stahl Ag | High-strength steel strip or sheet and process for its manufacture |
DE10037867A1 (en) | 1999-08-06 | 2001-06-07 | Muhr & Bender Kg | Flexible rolling process, for metal strip, involves work roll bending line control during or immediately after each roll gap adjustment to obtain flat strip |
JP2001140022A (en) * | 1999-08-27 | 2001-05-22 | Nippon Steel Corp | Method of manufacturing high strength galvanized steel sheet excellent in press-formability |
NL1015184C2 (en) * | 2000-05-12 | 2001-11-13 | Corus Staal Bv | Multi-phase steel and method for its manufacture. |
EP1288322A1 (en) * | 2001-08-29 | 2003-03-05 | Sidmar N.V. | An ultra high strength steel composition, the process of production of an ultra high strength steel product and the product obtained |
RU2256707C1 (en) * | 2004-07-15 | 2005-07-20 | Липецкий государственный технический университет | Method of production of the steel with homogeneous properties |
CN100473741C (en) * | 2005-06-29 | 2009-04-01 | 宝山钢铁股份有限公司 | Soft tin-plate and making process thereof |
DE502006003835D1 (en) * | 2006-10-30 | 2009-07-09 | Thyssenkrupp Steel Ag | Method of producing steel flat products from boron microalloyed multiphase steel |
ES2683010T3 (en) | 2007-02-23 | 2018-09-24 | Tata Steel Ijmuiden Bv | Strip of high strength steel cold rolled and continuously annealed, and method for producing said steel |
KR100928788B1 (en) * | 2007-12-28 | 2009-11-25 | 주식회사 포스코 | High strength steel sheet with excellent weldability and manufacturing method |
JP4924730B2 (en) * | 2009-04-28 | 2012-04-25 | Jfeスチール株式会社 | High-strength hot-dip galvanized steel sheet excellent in workability, weldability and fatigue characteristics and method for producing the same |
-
2011
- 2011-10-25 DE DE102011117572A patent/DE102011117572A1/en not_active Withdrawn
- 2011-11-30 WO PCT/DE2011/002094 patent/WO2012100762A1/en active Application Filing
- 2011-11-30 RU RU2013139431/02A patent/RU2581940C2/en active
- 2011-11-30 KR KR1020137022081A patent/KR101845321B1/en active IP Right Grant
- 2011-11-30 US US13/981,870 patent/US20140034196A1/en not_active Abandoned
- 2011-11-30 EP EP11822842.8A patent/EP2668302B1/en active Active
Also Published As
Publication number | Publication date |
---|---|
WO2012100762A1 (en) | 2012-08-02 |
US20140034196A1 (en) | 2014-02-06 |
KR101845321B1 (en) | 2018-04-04 |
EP2668302B1 (en) | 2018-06-06 |
RU2013139431A (en) | 2015-03-10 |
RU2581940C2 (en) | 2016-04-20 |
DE102011117572A1 (en) | 2012-08-16 |
KR20140014140A (en) | 2014-02-05 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
EP2809819B1 (en) | Ultrahigh-strength multiphase steel having improved properties during production and processing | |
EP2668302B1 (en) | Method for manufacturing a strip from a high strength multi-phase steel having excellent forming properties | |
EP2836614B1 (en) | High-strength multi-phase steel, and method for producing a strip from said steel | |
EP2864517B1 (en) | High-strength multiphase steel and method for producing a strip made from this steel with a minimum tensile strength of 580 mpa | |
EP3027784B1 (en) | Micro-alloyed high-strength multi-phase steel containing silicon and having a minimum tensile strength of 750 mpa and improved properties and method for producing a strip from said steel | |
EP3221484B1 (en) | Method for manufacturing a high-strength air-hardening multiphase steel strip having excellent processing properties | |
EP3221483B1 (en) | High strength air hardenable multi phase steel with excellent workability and sheet manufacturing process thereof | |
EP3221478B1 (en) | Hot or cold rolled strip of a high-strength air-hardening multi-phase steel comprising outstanding processing properties and method for the production a hot or cold rolled strip from said air-hardening multi-phase steel | |
EP3320120A1 (en) | Ultrahigh strength multiphase steel and method for producing a cold-rolled steel strip therefrom | |
WO2009021897A1 (en) | Dual-phase steel, flat product made of such dual-phase steel and method for producing a flat product | |
EP3692178B1 (en) | Method for producing a steel strip from an ultrahigh strength multiphase steel | |
WO2024068957A1 (en) | Method for producing a steel strip from a high-strength multiphase steel, and the corresponding steel strip | |
WO2022207913A1 (en) | Steel strip made of a high-strength multiphase steel and process for producing such a steel strip | |
EP4136265A1 (en) | Method for producing a steel strip with a multiphase structure, and related steel strip |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
|
17P | Request for examination filed |
Effective date: 20130716 |
|
AK | Designated contracting states |
Kind code of ref document: A1 Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR |
|
RIN1 | Information on inventor provided before grant (corrected) |
Inventor name: SCHULZ, THOMAS Inventor name: SCHLEGEL, CHRISTIAN Inventor name: WUELLNER, PHILIPP Inventor name: WEDEMEIER, ANDREAS Inventor name: POHL, MICHAEL Inventor name: HEINECKE, JOERG |
|
DAX | Request for extension of the european patent (deleted) | ||
17Q | First examination report despatched |
Effective date: 20161108 |
|
GRAP | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOSNIGR1 |
|
RIC1 | Information provided on ipc code assigned before grant |
Ipc: C22C 38/04 20060101ALI20180108BHEP Ipc: C22C 38/32 20060101ALI20180108BHEP Ipc: C22C 38/26 20060101ALI20180108BHEP Ipc: C21D 8/02 20060101ALI20180108BHEP Ipc: C22C 38/06 20060101ALI20180108BHEP Ipc: C22C 38/02 20060101ALI20180108BHEP Ipc: C22C 38/28 20060101ALI20180108BHEP Ipc: C21D 1/18 20060101AFI20180108BHEP |
|
INTG | Intention to grant announced |
Effective date: 20180131 |
|
GRAS | Grant fee paid |
Free format text: ORIGINAL CODE: EPIDOSNIGR3 |
|
GRAA | (expected) grant |
Free format text: ORIGINAL CODE: 0009210 |
|
AK | Designated contracting states |
Kind code of ref document: B1 Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: FG4D Free format text: NOT ENGLISH |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: EP Ref country code: AT Ref legal event code: REF Ref document number: 1006147 Country of ref document: AT Kind code of ref document: T Effective date: 20180615 |
|
REG | Reference to a national code |
Ref country code: IE Ref legal event code: FG4D Free format text: LANGUAGE OF EP DOCUMENT: GERMAN |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R096 Ref document number: 502011014307 Country of ref document: DE |
|
REG | Reference to a national code |
Ref country code: NL Ref legal event code: MP Effective date: 20180606 |
|
REG | Reference to a national code |
Ref country code: LT Ref legal event code: MG4D |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: BG Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180906 Ref country code: FI Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180606 Ref country code: LT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180606 Ref country code: CY Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180606 Ref country code: SE Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180606 Ref country code: ES Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180606 Ref country code: NO Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180906 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: RS Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180606 Ref country code: LV Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180606 Ref country code: GR Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180907 Ref country code: HR Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180606 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: NL Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180606 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: SK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180606 Ref country code: RO Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180606 Ref country code: PL Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180606 Ref country code: CZ Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180606 Ref country code: EE Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180606 Ref country code: IS Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20181006 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: IT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180606 Ref country code: SM Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180606 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R097 Ref document number: 502011014307 Country of ref document: DE |
|
PLBE | No opposition filed within time limit |
Free format text: ORIGINAL CODE: 0009261 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT |
|
26N | No opposition filed |
Effective date: 20190307 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: DK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180606 Ref country code: SI Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180606 |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: PL |
|
GBPC | Gb: european patent ceased through non-payment of renewal fee |
Effective date: 20181130 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: LU Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20181130 Ref country code: MC Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180606 |
|
REG | Reference to a national code |
Ref country code: BE Ref legal event code: MM Effective date: 20181130 |
|
REG | Reference to a national code |
Ref country code: IE Ref legal event code: MM4A |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: CH Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20181130 Ref country code: LI Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20181130 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: IE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20181130 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: AL Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180606 Ref country code: BE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20181130 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: GB Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20181130 |
|
REG | Reference to a national code |
Ref country code: AT Ref legal event code: MM01 Ref document number: 1006147 Country of ref document: AT Kind code of ref document: T Effective date: 20181130 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: AT Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20181130 Ref country code: MT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180606 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: TR Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180606 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: PT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180606 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: MK Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20180606 Ref country code: HU Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO Effective date: 20111130 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: FR Payment date: 20231120 Year of fee payment: 13 Ref country code: DE Payment date: 20231121 Year of fee payment: 13 |