EP2767601A1 - Cold rolled steel flat product for deep drawing applications and method for its production - Google Patents
Cold rolled steel flat product for deep drawing applications and method for its production Download PDFInfo
- Publication number
- EP2767601A1 EP2767601A1 EP13155225.9A EP13155225A EP2767601A1 EP 2767601 A1 EP2767601 A1 EP 2767601A1 EP 13155225 A EP13155225 A EP 13155225A EP 2767601 A1 EP2767601 A1 EP 2767601A1
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- EP
- European Patent Office
- Prior art keywords
- cold
- annealing
- content
- steel
- flat steel
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- Granted
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- 238000000034 method Methods 0.000 title claims abstract description 14
- 239000010960 cold rolled steel Substances 0.000 title claims description 15
- 238000004519 manufacturing process Methods 0.000 title description 10
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 103
- 239000010959 steel Substances 0.000 claims abstract description 103
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 24
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 23
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 15
- 229910052761 rare earth metal Inorganic materials 0.000 claims abstract description 15
- 150000002910 rare earth metals Chemical class 0.000 claims abstract description 14
- 238000005096 rolling process Methods 0.000 claims abstract description 10
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 10
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 10
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 10
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 8
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 8
- 229910052796 boron Inorganic materials 0.000 claims abstract description 7
- 229910052791 calcium Inorganic materials 0.000 claims abstract description 7
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 7
- 229910052802 copper Inorganic materials 0.000 claims abstract description 7
- 239000012535 impurity Substances 0.000 claims abstract description 7
- 229910052742 iron Inorganic materials 0.000 claims abstract description 7
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 7
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 7
- 238000000137 annealing Methods 0.000 claims description 59
- 238000005097 cold rolling Methods 0.000 claims description 38
- 238000005098 hot rolling Methods 0.000 claims description 12
- 239000002243 precursor Substances 0.000 claims description 12
- 238000005266 casting Methods 0.000 claims description 9
- 238000002844 melting Methods 0.000 claims description 5
- 230000008018 melting Effects 0.000 claims description 5
- 229910052748 manganese Inorganic materials 0.000 claims description 4
- 238000003856 thermoforming Methods 0.000 claims description 3
- 238000005554 pickling Methods 0.000 claims description 2
- 238000003303 reheating Methods 0.000 claims 1
- 239000010936 titanium Substances 0.000 abstract description 22
- 239000010955 niobium Substances 0.000 abstract description 21
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 abstract description 12
- 229910052799 carbon Inorganic materials 0.000 abstract description 10
- 150000001247 metal acetylides Chemical class 0.000 abstract description 10
- 239000010949 copper Substances 0.000 abstract description 7
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 abstract description 5
- 229910052782 aluminium Inorganic materials 0.000 abstract description 5
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 abstract description 5
- 229910052717 sulfur Inorganic materials 0.000 abstract description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 abstract description 4
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 abstract description 4
- 229910052698 phosphorus Inorganic materials 0.000 abstract description 4
- 239000011593 sulfur Substances 0.000 abstract description 4
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 abstract description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 abstract description 3
- 239000011574 phosphorus Substances 0.000 abstract description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 abstract 4
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 abstract 2
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 abstract 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 abstract 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 abstract 2
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 abstract 2
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 abstract 2
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 abstract 2
- 239000011575 calcium Substances 0.000 abstract 2
- 239000011651 chromium Substances 0.000 abstract 2
- 229910017052 cobalt Inorganic materials 0.000 abstract 2
- 239000010941 cobalt Substances 0.000 abstract 2
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 abstract 2
- 239000011733 molybdenum Substances 0.000 abstract 2
- 239000010703 silicon Substances 0.000 abstract 2
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 abstract 2
- 239000010937 tungsten Substances 0.000 abstract 2
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 abstract 2
- 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 abstract 1
- -1 manganese, rare earth metal Chemical class 0.000 abstract 1
- 239000000047 product Substances 0.000 description 37
- 230000015572 biosynthetic process Effects 0.000 description 10
- 239000000835 fiber Substances 0.000 description 9
- 238000005275 alloying Methods 0.000 description 7
- 230000007797 corrosion Effects 0.000 description 7
- 238000005260 corrosion Methods 0.000 description 7
- 230000000694 effects Effects 0.000 description 6
- 239000000463 material Substances 0.000 description 4
- 239000000956 alloy Substances 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 3
- 239000002131 composite material Substances 0.000 description 3
- 230000003647 oxidation Effects 0.000 description 3
- 238000007254 oxidation reaction Methods 0.000 description 3
- 229910000859 α-Fe Inorganic materials 0.000 description 3
- 238000010276 construction Methods 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 230000002349 favourable effect Effects 0.000 description 2
- 239000000155 melt Substances 0.000 description 2
- 229910052684 Cerium Inorganic materials 0.000 description 1
- 229910017372 Fe3Al Inorganic materials 0.000 description 1
- KCZFLPPCFOHPNI-UHFFFAOYSA-N alumane;iron Chemical compound [AlH3].[Fe] KCZFLPPCFOHPNI-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000033228 biological regulation Effects 0.000 description 1
- 230000000903 blocking effect Effects 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000010924 continuous production Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000001419 dependent effect Effects 0.000 description 1
- 230000003009 desulfurizing effect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 229910052746 lanthanum Inorganic materials 0.000 description 1
- 239000010410 layer Substances 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000010327 methods by industry Methods 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 230000008092 positive effect Effects 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 239000011241 protective layer Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 239000007858 starting material Substances 0.000 description 1
- 239000013589 supplement Substances 0.000 description 1
- 238000009966 trimming Methods 0.000 description 1
Classifications
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- 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
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0405—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
-
- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
- C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
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- 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
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- 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
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
-
- 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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—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
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- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/004—Dispersions; Precipitations
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—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
Definitions
- the invention relates to a cold-rolled steel flat product for thermoforming applications, which has a reduced weight as a result of a density reduction with optimized mechanical properties and an optimized deformability. Likewise, the invention relates to a method for producing such a flat steel product.
- Al-containing deep-drawing steels may contain a maximum of 6.5% by weight of A1 (cf. U. Brüx "Thermoformable iron-aluminum lightweight steels", construction April 4, 2002 ).
- the object of the invention was to provide a flat steel product which, with a significant reduction in weight, has optimized deformation suitability and likewise optimized mechanical properties.
- this object is achieved with regard to the cold-rolled flat steel product by providing a product having the features specified in claim 1.
- a cold-rolled flat steel product according to the invention for deep-drawing applications consists of a steel which, in addition to iron and unavoidable impurities (in% by weight) C: 0.008-0.1%, Al: 6.5-12%, Nb: 0.1-0, 2%, Ti: 0.15-0.5%, P: up to 0.1%, S: up to 0.03%, N: up to 0.1%, and optionally one or more elements from the group " Mn, Si, rare earth metals, Mo, Cr, Zr, V, W, Co, Ni, B, Cu, Ca, N "with the proviso contains, Mn: up to 1%, rare earth metals: up to 0.2%, Si : up to 2%, Zr: up to 1%, V: up to 1%, W: up to 1%, Mo: up to 1%, Cr: up to 3%, Co: up to 1%, Ni: up to 2%, B: up to 0 , 1%, Cu: up to 3%, Ca: up to 0.015%.
- the cold-rolled steel strip according to the invention is distinguished by r values of at least 1.3, with flat steel products according to the invention regularly achieving r values of greater than 1.3.
- the high r-value stands for a good deep drawability of the cold-rolled steel flat product according to the invention, since with increasing r-value the tendency to thinning during deep-drawing is reduced and consequently stronger deep-drawing degrees are made possible. Otherwise there would be a risk of component failure at the thinned area.
- a cold-rolled flat steel product according to the invention not only has high r values, but also reaches an elongation A50 of more than 18% on a regular basis. Steel flat products produced under optimum processing conditions have elongations A50 of 25% or more.
- the ⁇ -carbide content of a flat steel product according to the invention is from 0% by volume (completely ⁇ -carbide-free state) to at most 0.1% by volume. Due to the minimized ⁇ -carbide content, the processability of the flat steel product according to the invention is reliably ensured.
- a composite steel flat product according to the invention is further distinguished by the fact that the grains are globulitically pronounced in their microstructure.
- the ratio of the grain length in the rolling direction to the grain width in the transverse direction of the band is generally less than 1.5, in particular less than 1.2. That is, the length of the grains is at most 50%, in particular at most 20%, greater than their width.
- the steel according to the invention may contain a large number of further alloying elements in order to set certain properties.
- the relevant elements are summarized in the group "Mn, Si, rare earth metal, Mo, Cr, Zr, V, W, Co, Ni, B, Cu, Ca, N".
- Each of these optionally added alloying elements may be present in the steel according to the invention or completely absent, the respective element is also considered “not present” when it is present in the flat steel product according to the invention in an amount in which it is ineffective and therefore the production unavoidable impurities attributable to.
- Aluminum is present in the steel of the present invention at levels of 6.5-12 wt%, with Al contents greater than 6.8 wt% being advantageous in view of the desired density reduction.
- Typical Al contents of flat steel products according to the invention are in the range from 6.5 to 10% by weight, in particular from 6.8 to 9% by weight.
- the presence of high Al contents reduces the density of the steel and significantly improves its corrosion and oxidation resistance.
- A1 increases the tensile strength in these contents. Excessive contents of A1, however, can lead to a deterioration of the forming behavior, which is expressed in a decrease in the r value.
- the Al content is limited to a maximum of 12 wt .-%.
- An optimally balanced ratio of reduced density and processability arises when 6.5 to 10% by weight of Al, in particular at least 6.8% by weight of Al, are present in the steel according to the invention.
- the C content is limited to at most 0.1% by weight in steel according to the invention, with C contents of 0.015-0.05% by weight, in particular 0.008-0.05% by weight, being particularly favorable.
- C contents above 0.1 wt.% Can cause the formation of undesirable brittle kappa carbides ("K carbides”) at the grain boundaries and consequent reduction in hot and cold workability.
- ⁇ -carbides Fe-Al-C compounds
- ⁇ -carbides are formed in the Processing of generic steels early during hot processing at high temperatures on the grain boundaries and cause embrittlement of the material.
- carbide-forming alloying elements in accordance with the invention, the lowest possible free C content is set, thus largely preventing the formation of ⁇ carbides.
- 0.15-0.5% by weight of Ti and 0.1-0.2% by weight of Nb are present in the first place for this purpose.
- the effect of titanium can then be used particularly reliably if the Ti content is 0.15-0.3% by weight.
- niobium when Nb is present in amounts of 0.1-0.15% by weight in the steel according to the invention.
- the respective contents of Ti and Nb must be adjusted in such a way that they fulfill the condition prescribed according to the invention for the ratio of these contents.
- Ti and Nb contents which fulfill these requirements cause the formation of finely dispersed Ti and Nb carbides in the steel according to the invention, which promote the formation of a fine structure which supports the deformability of the flat steel product.
- V, Zr and W are also effective carbide formers and In amounts of up to 1% by weight each can supplement the effect of the Nb and Ti required contents provided according to the invention.
- the effect of V, Zr and W can be used particularly purposefully if their content is limited to in each case up to 0.5% by weight, in particular 0.3% by weight.
- Mn By adding Mn in amounts of up to 1% by weight, in particular up to 0.5% by weight, the hot workability and weldability of the steel according to the invention can be improved.
- Mn aids in deoxidation during melting and contributes to increasing the strength of the steel.
- Mo can be present in amounts of up to 1% by weight in the steel according to the invention. Mo also forms carbides and contributes to increasing the tensile strength, creep resistance and fatigue strength of a flat steel product of the present invention.
- the carbides formed by Mo with C are particularly fine and thus improve the fineness of the structure of the flat steel product according to the invention. High levels of Mo, however, degrade the hot and cold workability. In order to avoid this particularly reliably, the optionally present Mo content of a steel according to the invention can be limited to 0.5% by weight.
- the S content to a maximum of 0.03 wt .-%, preferably at most 0.01 wt .-%, and the P content to a maximum 0.1 wt .-%, preferably at most 0.05 wt .-%, limited.
- the N content of the flat steel product according to the invention is limited to at most 0.1% by weight, in particular at most 0.02% by weight, preferably at most 0.001% by weight, in order to avoid the formation of relatively large amounts of Al nitrides. These would degrade the mechanical properties.
- the presence of rare earth metals in amounts of up to 0.2% by weight contributes to improved resistance to oxidation and increased strength of a flat steel product of the present invention.
- contents of rare earth metals are desulfurizing and deoxidizing.
- the oxides formed by the respective rare earth metals also have a fine grain and promote positive texture selection for improved technological properties.
- Particularly suitable rare earth metals are Ce and La.
- the positive influences of rare earth metals in the steel according to the invention can be used particularly purposefully if the contents of rare earth metals are in the range of up to 0.05% by weight.
- the carbides formed by the presence of one or more of the elements Ti, Nb, V, Zr, W, Mo contribute to increasing the strength of the steel of the present invention.
- Si in amounts of up to 2 wt .-%, in particular up to 0.5 wt .-%, supported in the melting also the deoxidation and increases the strength and corrosion resistance of the steel according to the invention. Too high levels are due to the presence of Si however, reduces the ductility of the steel and its weldability.
- Typical Si contents of steels according to the invention are in the range of 0.1-0.5% by weight, in particular 0.1-0.2% by weight.
- the Co content of the steel according to the invention is limited to max. 1 wt .-%, in particular max. 0.5% by weight, preferably max. 0.3% by weight, limited.
- Ni improves the corrosion resistance and reduces the proportion of primary ferrite in the structure of the steel according to the invention.
- Ni can be used in the steel according to the invention at levels of up to 0.5% by weight in a particularly practical manner.
- the addition of B can also lead to the formation of a fine, the deformability of the steel according to the invention favoring structure. Too high levels of B, however, the cold workability and the Impair oxidation resistance. Therefore, the B content of the steel according to the invention is limited to 0.1% by weight, in particular up to 0.01% by weight, preferably 0.005% by weight.
- Cu in amounts of up to 3% by weight improves corrosion resistance in the steel of the present invention, but at higher levels may also deteriorate hot workability and weldability. If present, therefore, the Cu content in a practical embodiment of the invention to at most 1 wt .-%, in particular 0.5 wt .-%, limited.
- a waiting time of at least about 15 minutes should elapse between the last addition of alloy and the casting, in order to ensure thorough mixing of the molten steel.
- Typical effluent temperatures are in the range of about 1590 ° C.
- the hot strip is cold rolled to a degree of cold rolling of at least 65%, or a cold rolling degree of at least 65% is also achieved in the two- and multi-stage cold rolling after the intermediate annealing.
- the two-stage cold rolling can be carried out in such a way that the degree of cold rolling in the first stage is at least 40% and the last stage at least 65%, in particular more than 70%, for example at least 80%.
- the molten steels E1 and E2 have been cast into precursors in the form of blocks.
- the blocks were then heated through a preheating of two hours in each case to a preheat temperature VWT and vorgeblockt to slabs.
- the reheated slabs are hot rolled at a hot rolling end temperature WET to a hot strip and the resulting hot strip was wound at a reel temperature HT each to form a coil.
- a cast strip was produced as a precursor via a two-roll strip caster, which was then also hot-rolled into a hot strip with a hot rolling end temperature WET.
- the processing to the hot strip was carried out in a continuous process sequence without interruption following the strip casting, so that the precursor already had a temperature lying in the range of inventively predetermined preheating temperatures when entering the hot rolling device and the preheating could be omitted.
- the hot strip produced from the steel E3 has been coiled after hot rolling at a reel temperature HT to form a coil.
- the so annealed hot strips were cold rolled in one or two stages with cold rolling degrees KWG1 (cold rolling degree of the first cold rolling stage) and KWG2 (cold rolling degree of the respective second cold rolling stage) each to a cold rolled steel strip. If two-stage cold rolling has been used, an intermediate annealing at an intermediate annealing temperature ZGT is in each case between the cold rolling stages Have been carried out. After cold rolling, the cold-rolled steel flat products have undergone a final annealing at an annealing temperature SGT. The intermediate annealing and the final annealing have each been completed in continuous operation.
- the respective preheat temperature VWT, hot rolling end temperature WET, coiler temperature HT, annealing temperature GT, the respective cold rolling degree KWG1, KWG2, and the respective intermediate annealing temperature ZGT and final annealing temperature SGT, are given in Table 2.
- the cold-rolled steel strips produced from the steels E1 and E2 produced according to the invention in accordance with the invention have yield strengths which are regularly greater than 300 MPa, in particular greater than 320 MPa and thereby reach values of 380 MPa and more, and tensile strengths which are regularly greater 460 MPa, in particular greater than 480 MPa, while achieving values of 530 MPa and more, and having elongation values A50 of at least 18%, which regularly exceed 21%, in particular greater than 25%, and always have r values of 1 , 3 or greater.
- Cold-rolled steel strips not assembled according to the invention do not achieve such r-values even if these steel strips have been produced taking into account production parameters that are closely related to the parameters set in the production of the cold-rolled steel flat products according to the invention. Also according to the invention composite, but not according to the invention processed flat steel products do not reach the properties of steel flat products produced according to the invention or can not even be cold-rolled.
- the steel strips produced according to the invention have, despite their high Al contents, a superior deep-drawing capability, without the need for expensive alloying or process-engineering measures.
- a flat steel product with optimum deformation properties (r ⁇ 2, n ⁇ 0.2, A50 ⁇ 30%) is achieved by a combination of alloy according to the invention, high degree of cold deformation and low hot rolling temperature (about 850 ° C).
- the cold-rolled steel strips produced from the steels according to the invention in accordance with the invention contain, in addition to a Fe (Al) mixed-crystal matrix, locally occurring hardening precursor phase.
- a Fe (Al) mixed-crystal matrix in standard hot rolling parameters, rolling is carried out in the full-ferrite phase region and hot strip with typical three-layer structure is obtained, which in turn is characterized by recrystallized globulitic margins and the only recovered core area with stem crystals is marked.
- the hot strip annealing performed according to the invention reduces the dislocation density in the recovered area and facilitates subsequent cold rolling processing. Without the hot strip annealing, the alpha fiber texture component is strong but weak with hot strip annealing.
- a low maximum cold rolling degree of up to 50% results in weak gamma fiber texture components
- one-stage cold rolling with a high cold rolling degree of at least 65%, especially at least 80%, or two-stage cold rolling with correspondingly high deformation in the last rolling stage results in one strong gamma fiber component.
- These dependencies are more pronounced at lower hot rolling end temperatures, which are in the range of 830-960 ° C, especially 840-880 ° C.
- the deformation behavior of the resulting cold-rolled steel flat product is significantly influenced by the texture.
- High r and n values as well as a high elongation at break A50 are particularly noticeable when the gamma fast texture component dominates over the alpha fiber texture component.
- the inventively predetermined hot strip annealing and the inventively provided parameters of cold rolling ensure that this goal is achieved.
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Abstract
Description
Die Erfindung betrifft ein kaltgewalztes Stahlflachprodukt für Tiefziehanwendungen, das ein in Folge einer Dichtereduzierung vermindertes Gewicht bei optimierten mechanischen Eigenschaften und einer optimierten Verformbarkeit besitzt. Ebenso betrifft die Erfindung ein Verfahren zur Herstellung eines solchen Stahlflachprodukts.The invention relates to a cold-rolled steel flat product for thermoforming applications, which has a reduced weight as a result of a density reduction with optimized mechanical properties and an optimized deformability. Likewise, the invention relates to a method for producing such a flat steel product.
Wenn hier von Stahlflachprodukten die Rede ist, so sind damit durch Walzprozesse gewonnene Stahlbänder, Stahlbleche und daraus gewonnene Platinen, Zuschnitte und desgleichen bezeichnet.When it comes to flat-rolled steel products, it refers to steel strips obtained by rolling processes, steel sheets and blanks, blanks and the like obtained therefrom.
Sofern hier im Zusammenhang mit einer Legierungsvorschrift Angaben zum Gehalt eines Legierungselements gemacht werden, beziehen sich diese auf das Gewicht, sofern nicht ausdrücklich etwas anderes angegeben ist.If information about the content of an alloying element is given in connection with an alloying regulation, these relate to the weight, unless expressly stated otherwise.
Insbesondere bei im Bereich des Fahrzeugbaus eingesetzten Stahlflachprodukten sind neben dem Verhältnis von Festigkeit zu Umformbarkeit physikalische Eigenschaften wie Steifigkeit und Dichte im Hinblick auf die allgemein angestrebte Gewichtseinsparung und Verbesserung der Eigenfrequenzen des jeweiligen Fahrzeugs von besonderer Bedeutung. Eine deutliche Minimierung der Dichte und damit einhergehend des Gewichts kann bei Stählen durch Zulegieren größerer Gehalte an leichtem A1 erreicht werden. Bei hinreichend hohen Al-Gehalten tritt zudem Vorordnungsphase (K-Zustand) oder Ordnungsphase Fe3Al (D03) auf, die teilchenhärtend, festigkeitssteigernd und duktilitätsmindernd wirken.Particularly in the case of flat steel products used in the field of vehicle construction, in addition to the ratio of strength to formability, physical properties such as stiffness and density are of particular importance with regard to the generally desired weight saving and improvement of the natural frequencies of the respective vehicle. A significant minimization of the density and thus As a result of the weight, steels can be obtained by alloying larger contents of light A1. Moreover, at sufficiently high Al contents, the precursor phase (K-state) or the order phase Fe3Al (D03) occurs, which is particle-hardening, strength-increasing and reduces ductility.
Den anwendungsbezogenen Vorteilen von ferritischen Fe-Al-Stählen mit hohen Al-Gehalten der hier in Rede stehenden Art stehen Schwierigkeiten bei der Erzeugung und Verarbeitung gegenüber. So zeigen praktische Erfahrungen, dass ein nicht rekristallisierter Bandkernbereich am aus solchen Stählen erzeugten Warmband reduziert werden muss, da andernfalls Schwierigkeiten beim Besäumen und beim Kaltwalzen des Warmbands auftreten können. Darüber hinaus müssen im Stand der Technik aufwändige Prozesse durchlaufen werden, um anisotrope Kaltbandeigenschaften aufgrund einer ungeeigneten Kaltbandtextur zu vermeiden. Solche Anisotropien sind durch niedrige r- und n-Werte gekennzeichnet und bringen eine niedrige Bruchdehnung mit sich. Daraus resultiert ein problematisches Umform- und Bearbeitungsverhalten von aus Fe-Al-Stählen mit hohen Al-Gehalten erzeugten kaltgewalzten Stahlflachprodukten.The application-related advantages of high Al ferritic Fe-Al steels of the type in question are faced with difficulties in production and processing. Thus, practical experience shows that a non-recrystallized strip core area must be reduced on the hot strip produced from such steels, otherwise difficulties in trimming and cold rolling of the hot strip may occur. In addition, in the prior art, elaborate processes must be run to avoid anisotropic cold-rolled properties due to inadequate cold-rolled texture. Such anisotropies are characterized by low r and n values and entail a low elongation at break. This results in a problematic forming and processing behavior of cold-rolled flat steel products produced from Fe-Al steels with high Al contents.
Die voranstehend zusammengefassten Probleme nehmen mit ansteigendem Al-Gehalt zu und begrenzen daher die bisher erreichbare Dichtereduktion. So gilt in der Praxis, dass Al-haltige tiefziehfähige Stähle maximal 6,5 Gew.-% A1 enthalten dürfen (s.
Vor dem Hintergrund des voranstehend erläuterten Standes der Technik bestand die Aufgabe der Erfindung darin, ein Stahlflachprodukt zu schaffen, das bei einer deutlichen Gewichtsreduzierung optimierte Verformungseignung und ebenso optimierte mechanische Eigenschaften aufweist.Against the background of the above-mentioned state The object of the invention was to provide a flat steel product which, with a significant reduction in weight, has optimized deformation suitability and likewise optimized mechanical properties.
Darüber hinaus sollte ein Verfahren zur Herstellung eines solchen Stahlflachprodukts angegeben werden.In addition, a method for producing such a flat steel product should be specified.
Erfindungsgemäß wird diese Aufgabe im Hinblick auf das kaltgewalzte Stahlflachprodukt dadurch gelöst, dass ein Produkt mit den in Anspruch 1 angegebenen Merkmalen bereitgestellt wird.According to the invention, this object is achieved with regard to the cold-rolled flat steel product by providing a product having the features specified in claim 1.
Die erfindungsgemäße Lösung der oben genannten Aufgabe in Bezug auf das Verfahren besteht darin, dass bei der Herstellung von erfindungsgemäßen Stahlflachprodukten die in Anspruch 10 angegebenen Arbeitsschritte absolviert werden.The inventive solution of the above-mentioned object with respect to the method is that in the production of flat steel products according to the invention the steps specified in claim 10 are completed.
Vorteilhafte Ausgestaltungen der Erfindung sind in den abhängigen Ansprüchen angegeben und werden nachfolgend wie der allgemeine Erfindungsgedanke im Einzelnen erläutert.Advantageous embodiments of the invention are specified in the dependent claims and are explained below as the general inventive concept in detail.
Ein erfindungsgemäßes kaltgewalztes Stahlflachprodukt für Tiefziehanwendungen besteht aus einem Stahl, der neben Eisen und unvermeidbaren Verunreinigungen (in Gew.-%) C: 0,008 - 0,1 %, Al: 6,5 - 12 %, Nb: 0,1 - 0,2 %, Ti: 0,15 - 0,5 %, P: bis zu 0,1 %, S: bis zu 0,03 %, N: bis zu 0,1 % sowie optional eines oder mehrere Elemente aus der Gruppe "Mn, Si, Seltenerdmetalle, Mo, Cr, Zr, V, W, Co, Ni, B, Cu, Ca, N" mit der Maßgabe enthält, Mn: bis zu 1 %, Seltenerdmetalle: bis zu 0,2 %, Si: bis zu 2 %, Zr: bis zu 1 %, V: bis zu 1 %, W: bis zu 1 %, Mo: bis zu 1 %, Cr: bis zu 3 %, Co: bis zu 1 %, Ni: bis zu 2 %, B: bis zu 0,1 %, Cu: bis zu 3 %, Ca: bis zu 0,015 %. Dabei gilt für das Verhältnis %Ti/%Nb des Ti-Gehalts %Ti und des Nb-Gehalts %Nb
2,5 ≥ %Ti/%Nb ≥ 1,5,
insbesondere
2,2 ≥ %Ti/%Nb ≥ 1,8.A cold-rolled flat steel product according to the invention for deep-drawing applications consists of a steel which, in addition to iron and unavoidable impurities (in% by weight) C: 0.008-0.1%, Al: 6.5-12%, Nb: 0.1-0, 2%, Ti: 0.15-0.5%, P: up to 0.1%, S: up to 0.03%, N: up to 0.1%, and optionally one or more elements from the group " Mn, Si, rare earth metals, Mo, Cr, Zr, V, W, Co, Ni, B, Cu, Ca, N "with the proviso contains, Mn: up to 1%, rare earth metals: up to 0.2%, Si : up to 2%, Zr: up to 1%, V: up to 1%, W: up to 1%, Mo: up to 1%, Cr: up to 3%, Co: up to 1%, Ni: up to 2%, B: up to 0 , 1%, Cu: up to 3%, Ca: up to 0.015%. In this case, the ratio% Ti /% Nb of the Ti content% Ti and the Nb content% Nb
2.5 ≥% Ti /% Nb ≥ 1.5,
especially
2.2 ≥% Ti /% Nb ≥ 1.8.
In der für ein erfindungsgemäßes Stahlflachprodukt erfindungsgemäß vorgesehenen Legierungsvorschrift sind außer Eisen nur A1 und Titan und Niob Pflichtbestandteile.In the alloy rule provided according to the invention for a flat steel product according to the invention, only A1 and titanium and niobium are compulsory constituents apart from iron.
Das erfindungsgemäße kaltgewalzte Stahlband zeichnet sich durch r-Werte von mindestens 1,3 aus, wobei erfindungsgemäße Stahlflachprodukte regelmäßig r-Werte größer 1,3 erreichen. Der hohe r-Wert steht für eine gute Tiefziehfähigkeit des erfindungsgemäßen kaltgewalzten Stahlflachprodukts, da mit steigendem r-Wert die Neigung zum Ausdünnen beim Tiefziehen verringert wird und damit einhergehend stärkere Tiefziehgrade ermöglicht werden. Es bestände sonst die Gefahr von Bauteilversagen an der ausgedünnten Stelle.The cold-rolled steel strip according to the invention is distinguished by r values of at least 1.3, with flat steel products according to the invention regularly achieving r values of greater than 1.3. The high r-value stands for a good deep drawability of the cold-rolled steel flat product according to the invention, since with increasing r-value the tendency to thinning during deep-drawing is reduced and consequently stronger deep-drawing degrees are made possible. Otherwise there would be a risk of component failure at the thinned area.
Ein erfindungsgemäßes kaltgewalztes Stahlflachprodukt weist dabei nicht nur hohe r-Werte auf, sondern erreicht auch eine Dehnung A50 von regelmäßig mehr als 18 %. Unter optimalen Verarbeitungsbedingungen erzeugte erfindungsgemäße Stahlflachprodukte weisen Dehnungen A50 von 25 % und mehr auf.A cold-rolled flat steel product according to the invention not only has high r values, but also reaches an elongation A50 of more than 18% on a regular basis. Steel flat products produced under optimum processing conditions have elongations A50 of 25% or more.
Gleichzeitig ist charakteristisch für das Gefüge eines erfindungsgemäßen Stahlflachprodukts, dass es vollständig ferritisch und weitestgehend frei von κ-Karbiden (Fe-Al-C-Karbide) ist. Dementsprechend liegt der κ-Karbid-Gehalt eines erfindungsgemäße Stahlflachprodukts bei 0 Vol.-% (vollständig κ-Karbid-freier Zustand) bis höchstens 0,1 Vol.-%. Durch den minimierten κ-Karbid-Gehalt ist die Prozessierbarkeit des erfindungsgemäßen Stahlflachprodukts sicher gewährleistet.At the same time, it is characteristic of the structure of a flat steel product according to the invention that it is completely ferritic and largely free from κ-carbides (Fe-Al-C-carbides). Accordingly, the κ-carbide content of a flat steel product according to the invention is from 0% by volume (completely κ-carbide-free state) to at most 0.1% by volume. Due to the minimized κ-carbide content, the processability of the flat steel product according to the invention is reliably ensured.
Ein erfindungsgemäß zusammengesetztes Stahlflachprodukt zeichnet sich des Weiteren dadurch aus, dass in seinem Gefüge die Körner globulitisch ausgeprägt sind. Dabei beträgt das Verhältnis der Kornlänge in Walzrichtung zur Kornbreite in Querrichtung des Bands in der Regel weniger als 1,5, insbesondere weniger als 1,2. D.h., die Länge der Körner ist um maximal 50 %, insbesondere um höchstens 20 %, größer als ihre Breite.A composite steel flat product according to the invention is further distinguished by the fact that the grains are globulitically pronounced in their microstructure. The ratio of the grain length in the rolling direction to the grain width in the transverse direction of the band is generally less than 1.5, in particular less than 1.2. That is, the length of the grains is at most 50%, in particular at most 20%, greater than their width.
Neben den Pflichtbestandteilen kann der erfindungsgemäße Stahl eine Vielzahl von weiteren Legierungselementen enthalten, um bestimmte Eigenschaften einzustellen. Die hierzu in Frage kommenden Elemente sind in der Gruppe "Mn, Si, Seltenerdmetall, Mo, Cr, Zr, V, W, Co, Ni, B, Cu, Ca, N" zusammengefasst. Jedes dieser jeweils wahlweise zugegebenen Legierungselemente kann im erfindungsgemäßen Stahl vorhanden sein oder vollständig fehlen, wobei das jeweilige Element auch dann als "nicht vorhanden" anzusehen ist, wenn es im erfindungsgemäßen Stahlflachprodukt in einer Menge präsent ist, in der es unwirksam ist und daher den herstellungsbedingt unvermeidbaren Verunreinigungen zuzurechnen ist.In addition to the mandatory components, the steel according to the invention may contain a large number of further alloying elements in order to set certain properties. The relevant elements are summarized in the group "Mn, Si, rare earth metal, Mo, Cr, Zr, V, W, Co, Ni, B, Cu, Ca, N". Each of these optionally added alloying elements may be present in the steel according to the invention or completely absent, the respective element is also considered "not present" when it is present in the flat steel product according to the invention in an amount in which it is ineffective and therefore the production unavoidable impurities attributable to.
Aluminium ist im erfindungsgemäßen Stahl in Gehalten von 6,5 - 12 Gew.-% vorhanden, wobei Al-Gehalte von mehr als 6,8 Gew.-% im Hinblick auf die angestrebte Dichtereduktion vorteilhaft sind. Typische Al-Gehalte erfindungsgemäßer Stahlflachprodukte liegen im Bereich von 6,5 - 10 Gew.-%, insbesondere 6,8 - 9 Gew.-%. Durch die Anwesenheit hoher Al-Gehalte ist die Dichte des Stahls verringert und seine Korrosions- und Oxidationsbeständigkeit deutlich verbessert. Gleichzeitig erhöht A1 in diesen Gehalten die Zugfestigkeit. Zu hohe Gehalte an A1 können jedoch zu einer Verschlechterung des Umformverhaltens führen, die sich in einer Abnahme des r-Wertes ausdrückt. Um die negativen Auswirkungen von A1 zu minimieren, ist daher der Al-Gehalt auf maximal 12 Gew.-% beschränkt. Ein optimal ausgewogenes Verhältnis von verminderter Dichte und Verarbeitbarkeit stellt sich ein, wenn im erfindungsgemäßen Stahl 6,5 - 10 Gew.-% Al, insbesondere mindestens 6,8 Gew.-% Al, vorhanden sind.Aluminum is present in the steel of the present invention at levels of 6.5-12 wt%, with Al contents greater than 6.8 wt% being advantageous in view of the desired density reduction. Typical Al contents of flat steel products according to the invention are in the range from 6.5 to 10% by weight, in particular from 6.8 to 9% by weight. The presence of high Al contents reduces the density of the steel and significantly improves its corrosion and oxidation resistance. At the same time A1 increases the tensile strength in these contents. Excessive contents of A1, however, can lead to a deterioration of the forming behavior, which is expressed in a decrease in the r value. In order to minimize the negative effects of A1, therefore, the Al content is limited to a maximum of 12 wt .-%. An optimally balanced ratio of reduced density and processability arises when 6.5 to 10% by weight of Al, in particular at least 6.8% by weight of Al, are present in the steel according to the invention.
Der C-Gehalt ist in erfindungsgemäßem Stahl auf höchstens 0,1 Gew.-% beschränkt, wobei C-Gehalte von 0,015 - 0,05 Gew.-%, insbesondere 0,008 - 0,05 Gew.-%, besonders günstig sind. Oberhalb von 0,1 Gew.-% liegende C-Gehalte können die Bildung von unerwünschten spröden Kappa-Karbiden ("κ-Karbiden") an den Korngrenzen und eine dadurch bedingte Verminderung der Warm- und Kaltumformbarkeit verursachen.The C content is limited to at most 0.1% by weight in steel according to the invention, with C contents of 0.015-0.05% by weight, in particular 0.008-0.05% by weight, being particularly favorable. C contents above 0.1 wt.% Can cause the formation of undesirable brittle kappa carbides ("K carbides") at the grain boundaries and consequent reduction in hot and cold workability.
Der Vermeidung der Entstehung von κ-Karbiden (Fe-Al-C-Verbindungen) kommt beim erfindungsgemäßen Stahl eine besondere Bedeutung zu. κ-Karbide bilden sich bei der Verarbeitung von gattungsgemäßen Stählen frühzeitig während der Warmverarbeitung bei hohen Temperaturen auf den Korngrenzen und bewirken eine Versprödung des Materials. Durch die im Rahmen der erfindungsgemäßen Vorgaben erfolgende Zugabe karbidbildender Legierungselemente wird ein möglichst geringer freier C-Gehalt eingestellt und so die Entstehung von κ-Karbiden weitgehend unterbunden.The avoidance of the formation of κ-carbides (Fe-Al-C compounds) is of particular importance in the steel according to the invention. κ-carbides are formed in the Processing of generic steels early during hot processing at high temperatures on the grain boundaries and cause embrittlement of the material. As a result of the addition of carbide-forming alloying elements in accordance with the invention, the lowest possible free C content is set, thus largely preventing the formation of κ carbides.
Im erfindungsgemäßen Stahl sind zu diesem Zweck an erster Stelle 0,15 - 0,5 Gew.-% Ti und 0,1 - 0,2 Gew.-% Nb vorhanden. Dabei lässt sich die Wirkung von Titan dann besonders betriebssicher nutzen, wenn der Ti-Gehalt 0,15 - 0,3 Gew.-% beträgt. Entsprechendes gilt für Niob, wenn Nb in Gehalten von 0,1 - 0,15 Gew.-% im erfindungsgemäßen Stahl vorhanden ist. Gleichzeitig müssen die jeweiligen Ti- und Nb-Gehalte so eingestellt sein, dass sie die erfindungsgemäß für das Verhältnis dieser Gehalte vorgegebene Bedingung erfüllen. Ti- und Nb-Gehalte, die diese Vorgaben erfüllen, bewirken im erfindungsgemäßen Stahl die Bildung von feindispers verteilten Ti- und Nb-Karbiden, die die Ausbildung eines feinen, die Verformbarkeit des Stahlflachprodukts unterstützenden Gefüges fördern. Gleichzeitig wird freier Kohlenstoff gebunden, der andernfalls zur Entstehung von die Verformbarkeit behindernden, die Gefahr von Versprödung mit sich bringenden Fe-Al-C-Karbiden führen könnte. Bei zu hohen Gehalten an Ti und Nb können sich allerdings unerwünschte Ausscheidungen dieser Elemente im Stahl bilden, die eine Abnahme der Zähigkeit und Verformbarkeit bewirken könnten.In the steel according to the invention, 0.15-0.5% by weight of Ti and 0.1-0.2% by weight of Nb are present in the first place for this purpose. The effect of titanium can then be used particularly reliably if the Ti content is 0.15-0.3% by weight. The same applies to niobium when Nb is present in amounts of 0.1-0.15% by weight in the steel according to the invention. At the same time, the respective contents of Ti and Nb must be adjusted in such a way that they fulfill the condition prescribed according to the invention for the ratio of these contents. Ti and Nb contents which fulfill these requirements cause the formation of finely dispersed Ti and Nb carbides in the steel according to the invention, which promote the formation of a fine structure which supports the deformability of the flat steel product. At the same time free carbon is bound, which could otherwise lead to the formation of deformability hindering the risk of embrittlement bring Fe-Al-C-carbides. Too high levels of Ti and Nb, however, may form undesirable precipitates of these elements in the steel, which could cause a decrease in toughness and ductility.
V, Zr und W sind ebenfalls effektive Karbidbildner und können in Gehalten von jeweils bis zu 1 Gew.-% die Wirkung der erfindungsgemäß vorgesehenen Pflichtgehalte an Nb und Ti ergänzen. Besonders zielgerichtet lässt sich die Wirkung von V, Zr und W dann nutzen, wenn ihr Gehalt jeweils auf bis zu 0,5 Gew.-%, insbesondere 0,3 Gew.-%, beschränkt ist.V, Zr and W are also effective carbide formers and In amounts of up to 1% by weight each can supplement the effect of the Nb and Ti required contents provided according to the invention. The effect of V, Zr and W can be used particularly purposefully if their content is limited to in each case up to 0.5% by weight, in particular 0.3% by weight.
Durch die Zugabe von Mn in Gehalten von bis zu 1 Gew.-%, insbesondere bis zu 0,5 Gew.-%, kann die Warmformbarkeit und Schweißbarkeit des erfindungsgemäßen Stahls verbessert werden. Darüber hinaus unterstützt Mn bei der Erschmelzung die Desoxidation und trägt zu einer Erhöhung der Festigkeit des Stahls bei. Diese positiven Wirkungen von Mn können besonders effektiv genutzt werden, wenn der Mn-Gehalt 0,05 - 0,5 Gew.-% beträgt.By adding Mn in amounts of up to 1% by weight, in particular up to 0.5% by weight, the hot workability and weldability of the steel according to the invention can be improved. In addition, Mn aids in deoxidation during melting and contributes to increasing the strength of the steel. These positive effects of Mn can be used particularly effectively when the Mn content is 0.05-0.5 wt%.
Mo kann in Gehalten von jeweils bis zu 1 Gew.-% im erfindungsgemäßen Stahl enthalten sein. Mo bildet ebenfalls Karbide und trägt zur Erhöhung der Zugfestigkeit, Kriechbeständigkeit und Ermüdungsfestigkeit eines erfindungsgemäßen Stahlflachprodukts bei. Die von Mo mit C gebildeten Karbide sind besonders fein und verbessern so die Feinheit des Gefüges des erfindungsgemäßen Stahlflachprodukts. Hohe Gehalte an Mo verschlechtern jedoch die Warm- und Kaltumformbarkeit. Um dies besonders sicher zu vermeiden, kann der optional vorhandene Mo-Gehalt eines erfindungsgemäßen Stahls auf 0,5 Gew.-% beschränkt werden.Mo can be present in amounts of up to 1% by weight in the steel according to the invention. Mo also forms carbides and contributes to increasing the tensile strength, creep resistance and fatigue strength of a flat steel product of the present invention. The carbides formed by Mo with C are particularly fine and thus improve the fineness of the structure of the flat steel product according to the invention. High levels of Mo, however, degrade the hot and cold workability. In order to avoid this particularly reliably, the optionally present Mo content of a steel according to the invention can be limited to 0.5% by weight.
Um negative Einflüsse von Schwefel und Phosphor auf die Eigenschaften des erfindungsgemäß verarbeiteten Stahls zu vermeiden, sind der S-Gehalt auf maximal 0,03 Gew.-%, bevorzugt maximal 0,01 Gew.-%, und der P-Gehalt auf maximal 0,1 Gew.-%, bevorzugt maximal 0,05 Gew.-%, beschränkt.To avoid negative effects of sulfur and phosphorus on the properties of the steel processed according to the invention, the S content to a maximum of 0.03 wt .-%, preferably at most 0.01 wt .-%, and the P content to a maximum 0.1 wt .-%, preferably at most 0.05 wt .-%, limited.
Der N-Gehalt des erfindungsgemäßen Stahlflachprodukts ist auf höchstens 0,1 Gew.-%, insbesondere höchstens 0,02 Gew.-%, bevorzugt höchstens 0,001 Gew.-%, beschränkt, um die Bildung größerer Mengen von Al-Nitriden zu vermeiden. Diese würden die mechanischen Eigenschaften verschlechtern.The N content of the flat steel product according to the invention is limited to at most 0.1% by weight, in particular at most 0.02% by weight, preferably at most 0.001% by weight, in order to avoid the formation of relatively large amounts of Al nitrides. These would degrade the mechanical properties.
Die Anwesenheit von Seltenerdmetallen in Gehalten von bis zu 0,2 Gew.-% trägt zu einer verbesserten Beständigkeit gegen Oxidation und zu einer erhöhten Festigkeit eines erfindungsgemäßen Stahlflachprodukts bei. Gleichzeitig wirken Gehalte an Seltenerdmetallen entschwefelnd sowie desoxidierend. Die vom jeweiligen Seltenerdmetall gebildeten Oxide wirken zudem kornfeinend und fördern eine positive Texturauslese für verbesserte technologische Eigenschaften. Als Seltenerdmetalle eignen sich besonders Ce und La. Besonders zielgerichtet lassen sich die positiven Einflüsse von Seltenerdmetallen im erfindungsgemäßen Stahl nutzen, wenn die Gehalte an Seltenerdmetallen im Bereich von bis zu 0,05 Gew.-% liegen.The presence of rare earth metals in amounts of up to 0.2% by weight contributes to improved resistance to oxidation and increased strength of a flat steel product of the present invention. At the same time, contents of rare earth metals are desulfurizing and deoxidizing. The oxides formed by the respective rare earth metals also have a fine grain and promote positive texture selection for improved technological properties. Particularly suitable rare earth metals are Ce and La. The positive influences of rare earth metals in the steel according to the invention can be used particularly purposefully if the contents of rare earth metals are in the range of up to 0.05% by weight.
Grundsätzlich tragen die durch die Anwesenheit von einem oder mehreren der Elemente Ti, Nb, V, Zr, W, Mo jeweils gebildeten Karbide zur Steigerung der Festigkeit des erfindungsgemäßen Stahls bei.Basically, the carbides formed by the presence of one or more of the elements Ti, Nb, V, Zr, W, Mo contribute to increasing the strength of the steel of the present invention.
Si in Gehalten von bis zu 2 Gew.-%, insbesondere bis zu 0,5 Gew.-%, unterstützt bei der Erschmelzung ebenfalls die Desoxidation und erhöht die Festigkeit und Korrosionsbeständigkeit des erfindungsgemäßen Stahls. Bei zu hohen Gehalten werden durch die Anwesenheit von Si allerdings die Duktilität des Stahls und seine Schweißeignung verringert. Typische Si-Gehalte erfindungsgemäßer Stähle liegen im Bereich von 0,1 - 0,5 Gew.-%, insbesondere 0,1 - 0,2 Gew.-%.Si in amounts of up to 2 wt .-%, in particular up to 0.5 wt .-%, supported in the melting also the deoxidation and increases the strength and corrosion resistance of the steel according to the invention. Too high levels are due to the presence of Si however, reduces the ductility of the steel and its weldability. Typical Si contents of steels according to the invention are in the range of 0.1-0.5% by weight, in particular 0.1-0.2% by weight.
Auch durch die Zugabe von Cr in Gehalten von bis zu 3 Gew.-% kann in erfindungsgemäßem Stahl vorhandener Kohlenstoff zu Karbiden abgebunden werden. Gleichzeitig erhöht die Anwesenheit von Cr die Korrosionsbeständigkeit. Besonders zielsicher werden die vorteilhaften Eigenschaften von Cr im erfindungsgemäßen Stahl dann erreicht, wenn Cr in Gehalten von bis zu 1 Gew.-%, insbesondere bis zu 0,5 Gew.-%, vorhanden ist.Also by the addition of Cr in amounts of up to 3 wt .-% existing carbon in the invention steel can be bonded to carbides. At the same time, the presence of Cr increases the corrosion resistance. The advantageous properties of Cr in the steel according to the invention are achieved with particular accuracy when Cr is present in amounts of up to 1% by weight, in particular up to 0.5% by weight.
Um eine Erhöhung der Rekristallisationstemperatur zu vermeiden, ist der Co-Gehalt des erfindungsgemäßen Stahls auf max. 1 Gew.-%, insbesondere max. 0,5 Gew.-%, bevorzugt max. 0,3 Gew.-%, beschränkt.In order to avoid an increase in the recrystallization temperature, the Co content of the steel according to the invention is limited to max. 1 wt .-%, in particular max. 0.5% by weight, preferably max. 0.3% by weight, limited.
Nickel in Gehalten von bis zu 2 Gew.-%, insbesondere 1 Gew.-%, trägt in erfindungsgemäßem Stahl ebenfalls zur Erhöhung der Festigkeit und Zähigkeit bei. Darüber hinaus verbessert Ni die Korrosionsbeständigkeit und verringert den Anteil an primärem Ferrit im Gefüge des erfindungsgemäßen Stahls. Besonders praxisgerecht lässt sich Ni im erfindungsgemäßen Stahl bei Gehalten von bis zu 0,5 Gew.-% nutzen.Nickel in amounts of up to 2 wt .-%, in particular 1 wt .-%, also contributes in the inventive steel to increase the strength and toughness. In addition, Ni improves the corrosion resistance and reduces the proportion of primary ferrite in the structure of the steel according to the invention. Ni can be used in the steel according to the invention at levels of up to 0.5% by weight in a particularly practical manner.
Die Zugabe von B kann ebenfalls zur Ausbildung eines feinen, die Verformbarkeit des erfindungsgemäßen Stahls begünstigenden Gefüges führen. Zu hohe Gehalte an B können jedoch die Kaltumformbarkeit und die Oxidationsbeständigkeit beeinträchtigen. Daher ist der B-Gehalt des erfindungsgemäßen Stahls auf 0,1 Gew.-%, insbesondere bis zu 0,01 Gew.-%, bevorzugt 0,005 Gew.-%, beschränkt.The addition of B can also lead to the formation of a fine, the deformability of the steel according to the invention favoring structure. Too high levels of B, however, the cold workability and the Impair oxidation resistance. Therefore, the B content of the steel according to the invention is limited to 0.1% by weight, in particular up to 0.01% by weight, preferably 0.005% by weight.
Cu in Gehalten von bis zu 3 Gew.-% verbessert im erfindungsgemäßen Stahl die Korrosionsbeständigkeit, kann aber bei höheren Gehalten auch die Warmumformbarkeit und Schweißbarkeit verschlechtern. Sofern vorhanden, ist daher der Cu-Gehalt bei einer praxisgerechten Ausgestaltung der Erfindung auf höchstens 1 Gew.-%, insbesondere 0,5 Gew.-%, beschränkt.Cu in amounts of up to 3% by weight improves corrosion resistance in the steel of the present invention, but at higher levels may also deteriorate hot workability and weldability. If present, therefore, the Cu content in a practical embodiment of the invention to at most 1 wt .-%, in particular 0.5 wt .-%, limited.
Ca in Gehalten von bis zu 0,015 Gew.-%, insbesondere 0,005 Gew.-% oder 0,003 Gew.-%, bindet im erfindungsgemäßen Stahl Schwefel, welcher die Korrosionsbeständigkeit vermindern könnte.Ca in amounts of up to 0.015 wt .-%, in particular 0.005 wt .-% or 0.003 wt .-%, binds sulfur in the steel according to the invention, which could reduce the corrosion resistance.
Bei der Erzeugung eines erfindungsgemäßen kaltgewalzten Stahlflachprodukts werden erfindungsgemäß folgende Arbeitsschritte durchlaufen:
- Erschmelzen einer entsprechend den voranstehend erläuterten Maßgaben erfindungsgemäß zusammengesetzten Stahlschmelze.
- Vergießen der Stahlschmelze zu einem Vorprodukt, wie einem Block, einer Bramme, einer Dünnbramme oder einem gegossenen Band. Hier hat sich insbesondere das Vergießen zu einem endabmessungsnah gegossenen Band als vorteilhaft herausgestellt. Das endabmessungsnahe Gießen kann dabei durch Einsatz von an sich zu diesem Zweck bekannten konventionellen Gießeinrichtungen erfolgen. Hierzu zählt z. B. die "Zwei-Rollen-Bandgießmaschine". Da dieses Verfahren mit einer mitlaufenden Kokille operiert, besteht keine Relativbewegung zwischen Kokille und erstarrender Bandschale. Auf diese Weise können diese Verfahren ohne Gießpulver arbeiten und sind daher grundsätzlich gut geeignet, das Vormaterial für die Herstellung von erfindungsgemäßen Stahlflachprodukten zu erzeugen. Beim Bandgießen ebenfalls positiv wirkt sich aus, dass das gegossene Band bis zu seiner Abkühlung allenfalls geringen mechanischen Spannungen ausgesetzt ist, so dass die Gefahr der Entstehung von Rissen im Hochtemperaturbereich minimiert ist.
- Melting a according to the above-explained provisos according to the invention composite molten steel.
- Casting the molten steel into a precursor such as a block, a slab, a thin slab or a cast strip. In particular, the casting to a near-net cast tape has been found to be beneficial. The close to the final casting can by using known per se for this purpose Conventional pouring done. This includes z. As the "two-roll strip casting machine". Since this method operates with a co-rotating mold, there is no relative movement between mold and solidifying band shell. In this way, these methods can work without casting powder and therefore are generally well suited to produce the starting material for the production of flat steel products according to the invention. Another positive aspect of strip casting is the fact that the cast strip is exposed to at most low mechanical stresses until it cools, so that the risk of cracking in the high-temperature region is minimized.
Beim Erschmelzen der erfindungsgemäß vergossenen Stahlschmelze sollte zwischen der letzten Legierungszugabe und dem Abguss jeweils eine Wartezeit von mindestens etwa 15 Minuten vergehen, um eine gute Durchmischung der Stahlschmelze zu gewährleisten. Typische Abgusstemperaturen liegen im Bereich von etwa 1590 °C.When melting the molten steel poured according to the invention, a waiting time of at least about 15 minutes should elapse between the last addition of alloy and the casting, in order to ensure thorough mixing of the molten steel. Typical effluent temperatures are in the range of about 1590 ° C.
Anhand praktischer Versuche konnte gezeigt werden, dass sich erfindungsgemäße Stähle auch zu Blöcken vergießen lassen, die dann durch Vorblocken zu Brammen ausgewalzt werden.
- Das Vorprodukt wird erforderlichenfalls auf eine 1000 - 1300 °C betragende Vorwärmtemperatur gebracht oder in diesem Temperaturbereich gehalten, wobei sich hier Vorwärmtemperaturen von 1200 - 1300 °C, insbesondere 1200 - 1280 °C, als besonders praxisgerecht erwiesen haben. Im Fall, dass das Vorprodukt eine Bramme ist, beträgt die Dauer, über die diese Vorerwärmung abläuft, beispielsweise 120 - 240 Minuten.
- Das Vorprodukt wird, gegebenenfalls nach der optional durchgeführten Erwärmung auf die Vorwärmtemperatur, zu einem Warmband warmgewalzt, wobei die Walzendtemperatur mehr als 820 °C, insbesondere mehr als 850 °C, betragen soll und in der Praxis Warmwalzendtemperaturen von 830 - 960 °C eingestellt werden. Bei praktischen Versuchen haben sich im Bereich von 840 - 880 °C liegende Warmwalzendtemperaturen als besonders günstig herausgestellt.
- Das erhaltene Warmband wird zu einem Coil gehaspelt, wobei die Haspeltemperatur bis zu 750 °C, insbesondere bis zu 650 °C, betragen kann. In der Praxis werden typischerweise Haspeltemperaturen von 450 - 750 °C, insbesondere 500 °C +/- 20 °C, eingestellt. Das so erhaltene Warmband hat eine mittlere Ferritkornlänge im Bandkern, die in Bandrichtung gemessen größer 100 µm ist.
- Nach dem Haspeln wird das Warmband geglüht. Diese Glühung ist von besonderer Bedeutung für die Eigenschaften des erfindungsgemäß erzeugten Stahlflachprodukts. Die Warmbandglühung wird bei einer oberhalb von 650 °C liegenden, bis 1200 °C reichenden, insbesondere 700 - 900 °C betragenden Glühtemperatur durchgeführt. Glühtemperaturen von etwa 850 °C, insbesondere 850 °C +/-20 °C, haben sich dabei als besonders praxisgerecht erwiesen. Die hierfür vorgesehenen Glühzeiten betragen bei dieser üblicherweise als Haubenglühung durchgeführten Glühung typischerweise 1 - 50 h.
- If necessary, the precursor is brought to a preheating temperature of 1000-1300 ° C. or kept within this temperature range, with preheating temperatures of 1200-1300 ° C., in particular 1200-1280 ° C., proving to be particularly practical to have. In the case where the precursor is a slab, the duration over which this preheating takes place is, for example, 120-240 minutes.
- The precursor is, if appropriate after the optionally performed heating to the preheating temperature, hot rolled into a hot strip, the rolling end temperature should be more than 820 ° C, in particular more than 850 ° C, and be set in practice Heißwalzendtemperaturen 830-960 ° C. , In practical experiments, hot rolling temperatures in the range of 840-880 ° C have proven to be particularly favorable.
- The resulting hot strip is coiled into a coil, wherein the coiler temperature can be up to 750 ° C, in particular up to 650 ° C. In practice, reel temperatures of 450-750 ° C., in particular 500 ° C. +/- 20 ° C., are typically set. The hot strip thus obtained has an average ferrite grain length in the strip core which, measured in the strip direction, is greater than 100 μm.
- After reeling, the hot strip is annealed. This annealing is of particular importance for the properties of the steel flat product produced according to the invention. The hot strip annealing is carried out at a temperature above 650 ° C, reaching up to 1200 ° C, in particular 700 - 900 ° C amount annealing temperature. Annealing temperatures of about 850 ° C, in particular 850 ° C +/- 20 ° C, have proven to be particularly practical. The intended annealing times are usually carried out as a bell annealing at this Annealing typically 1 - 50 h.
In Folge der in dem erfindungsgemäß vorgegebenen Temperaturbereich durchgeführten Glühung lässt sich das Warmband trotz seiner hohen Al-Gehalte kaltwalzen, ohne dass starke Kantenrisse oder gar Bandrisse auftreten. Die Warmbandglühung dient dabei der Erzeugung eines ausreichend erholten Bandkernbereichs, der Absenkung des Kaltwalzwiderstands und der Erhöhung des maximal erreichbaren Kaltwalzgrades. Eine durch die Warmbandglühung bewirkte Texturauslese und ein hoher Kaltverformungsgrad fördern die Ausbildung einer geeigneten Kaltbandtextur mit dem gewünschten Eigenschaftsprofil. Für die Warmbandglühung ist dabei insbesondere der Haubenglühprozess mit nach Maßgabe der voranstehend erläuterten Varianten eingestellten Spitzentemperaturen oberhalb von 650 °C geeignet.
- Erforderlichenfalls kann nach dem Glühen ein Beizen des Warmbands durchgeführt werden, um auf dem Warmband haftende Rückstände zu entfernen.
- Das geglühte und optional gebeizte Warmband wird dann zu einem kaltgewalzten Stahlflachprodukt kaltgewalzt. Das Kaltwalzen kann in einer Stufe oder zweistufig erfolgen. Beim zweistufigen Kaltwalzen kann in an sich bekannter Weise zwischen den Kaltwalzstufen eine Zwischenglühung durchgeführt werden. Durch zweistufiges Kaltwalzen mit Zwischenglühung wird eine positive Texturauslese gefördert.
- If necessary, pickling of the hot strip may be performed after annealing to remove any residue left on the hot strip.
- The annealed and optionally pickled hot strip is then cold rolled to a cold rolled flat steel product. Cold rolling can be done in one stage or two stages. In the two-stage cold rolling an intermediate annealing can be carried out in a conventional manner between the cold rolling stages. Two-stage cold rolling with intermediate annealing promotes positive texture selection.
In jedem Fall wird beim Kaltwalzen die vor dem Ende des Kaltwalzens absolvierte Walzstufe mit einem möglichst hohen Kaltverformungsgrad durchgeführt. Im Fall eines einstufigen Kaltwalzens bedeutet dies, dass das Warmband mit einem Kaltwalzgrad von mindestens 65 % kaltgewalzt wird, bzw. beim zwei- und mehrstufigen Kaltwalzen nach der Zwischenglühung ein Kaltwalzgrad von ebenfalls mindestens 65 % erreicht wird. Um optimale Walzergebnisse zu erhalten, kann dabei das zweistufige Kaltwalzen so durchgeführt werden, dass der Kaltwalzgrad in der ersten Stufe mindestens 40 % und der letzten Stufe mindestens 65 %, insbesondere mehr als 70 %, beispielsweise mindestens 80 %, beträgt.In any case, when cold rolling before the end of the Cold rolling completed rolling stage with the highest possible degree of cold deformation. In the case of single-stage cold rolling, this means that the hot strip is cold rolled to a degree of cold rolling of at least 65%, or a cold rolling degree of at least 65% is also achieved in the two- and multi-stage cold rolling after the intermediate annealing. In order to obtain optimum rolling results, the two-stage cold rolling can be carried out in such a way that the degree of cold rolling in the first stage is at least 40% and the last stage at least 65%, in particular more than 70%, for example at least 80%.
Der hohe Kaltwalzgrad von mindestens 65 % in der jeweils letzten Kaltwalzstufe fördert die Ausbildung einer geeigneten Kaltbandtextur. Der Effekt ist bei den in erfindungsgemäßer Weise legierten Ti/Nb-legierten Materialien besonders ausgeprägt.
- Nach dem Kaltwalzen wird das erhaltene Kaltband einer Glühung unterzogen, die im kontinuierlichen Glühprozess oder batchweise als Haubenglühung ausgeführt wird. Sowohl die Schlussglühung als auch die optional beim Kaltwalzen durchgeführten Zwischenglühungen können in konventioneller Weise bei Temperaturen und Glühdauern durchgeführt werden, die an sich bekannt sind. Bei der abschließenden Schlussglühung des Kaltbandes bildet sich ein Material mit rekristallisierter Mikrostruktur und vorteilhafter Textur aus. Die erhaltene Textur ist gekennzeichnet durch eine geringe Belegung der α-Fasern von weniger als 4 und einer starken Belegung der γ-Fasern von mehr als 4, was zu r-Werten größer 1,3 führt. Die jeweilige Glühung des kaltgewaltzen Bandes kann in im kontinuierlichen Durchlauf durchlaufenen Glühanlagen mit Glühtemperaturen von 750 - 850 °C über eine typische Dauer von 1 - 20 min erfolgen, wobei sich Glühtemperaturen von mehr als 780 °C, insbesondere 800 - 850 °C, und eine Glühdauer von 2 - 5 min als besonders praxisgerecht erwiesen haben. Alternativ kann die jeweilige Glühung auch in einer Haubenglühanlage durchgeführt werden, bei der die Glühtemperatur mehr als 650 °C, insbesondere 650 - 850 °C, und die Glühdauer 1 - 50 h beträgt. In der Praxis haben sich für das Haubenglühen Glühtemperaturen von 700 - 800 °C und eine Glühdauer von 1 - 30 h besonders bewährt.
- Optional kann das erhaltene Kaltband beispielsweise zur Verbesserung seiner Korrosionsbeständigkeit mit einer metallischen Schutzschicht belegt werden, die beispielsweise auf A1 oder Zn basiert. Hierzu eignen sich die an sich bekannten Beschichtungsverfahren.
- After cold rolling, the cold strip obtained is subjected to an annealing, which is carried out in a continuous annealing process or batchwise as a bell annealing. Both the final annealing and the optional intermediate anneals carried out during cold rolling can be carried out in a conventional manner at temperatures and annealing times which are known per se. In the final annealing of the cold strip, a material with a recrystallized microstructure and an advantageous texture is formed. The obtained texture is characterized by a low occupancy of the α-fibers of less than 4 and a strong occupancy of the γ-fibers of more than 4, which leads to r-values greater than 1.3. The respective annealing of the cold-rolled strip can be carried out in continuously continuous annealing plants with annealing temperatures of 750 - 850 ° C over a typical period of 1 - 20 min, with annealing temperatures of more than 780 ° C, in particular 800 - 850 ° C, and An annealing time of 2 - 5 min have proven to be particularly practical. Alternatively, the respective annealing can also be carried out in a bell annealing plant in which the annealing temperature is more than 650 ° C., in particular 650-850 ° C., and the annealing time is 1-50 h. In practice, annealing temperatures of 700 ° to 800 ° C. and an annealing time of 1 to 30 h have proven particularly suitable for bell annealing.
- Optionally, the cold strip obtained, for example, to improve its corrosion resistance can be covered with a metallic protective layer, which is based for example on A1 or Zn. For this purpose, the coating methods known per se are suitable.
Zur Erprobung der Erfindung sind drei erfindungsgemäße Schmelzen E1,E2,E3 und zwei Vergleichsschmelzen V1,V2 erschmolzen worden, deren Zusammensetzungen in Tabelle 1 angegeben sind.To test the invention, three inventive melts E1, E2, E3 and two comparative melts V1, V2 have been melted, whose compositions are given in Table 1.
Die Stahlschmelzen E1 und E2 sind zu Vorprodukten in Form von Blöcken vergossen worden. Die Blöcke sind dann über eine Vorwärmdauer von jeweils zwei Stunden auf eine Vorwärmtemperatur VWT durcherwärmt und zu Brammen vorgeblockt worden.The molten steels E1 and E2 have been cast into precursors in the form of blocks. The blocks were then heated through a preheating of two hours in each case to a preheat temperature VWT and vorgeblockt to slabs.
Anschließend sind die durcherwärmten Brammen bei einer Warmwalzendtemperatur WET zu einem Warmband warmgewalzt und das erhaltene Warmband bei einer Haspeltemperatur HT jeweils zu einem Coil gewickelt worden.Subsequently, the reheated slabs are hot rolled at a hot rolling end temperature WET to a hot strip and the resulting hot strip was wound at a reel temperature HT each to form a coil.
Aus der Stahlschmelze E3 ist über eine Zwei-Rollen-Bandgießanlage als Vorprodukt ein gegossenes Band erzeugt worden, das anschließend ebenfalls zu einem Warmband mit einer Warmwalzendtemperatur WET warmgewalzt worden ist. Die Verarbeitung zum Warmband erfolgte in einer kontinuierlichen Prozessfolge unterbrechungsfrei im Anschluss an das Bandgießen, so dass das Vorprodukt bei Eintritt in die Warmwalzeinrichtung bereits eine im Bereich der erfindungsgemäß vorgegebenen Vorwärmtemperaturen liegende Temperatur aufwies und die Vorerwärmung entfallen konnte. Auch das aus dem Stahl E3 erzeugte Warmband ist nach dem Warmwalzen bei einer Haspeltemperatur HT zu einem Coil gehaspelt worden.From the molten steel E3, a cast strip was produced as a precursor via a two-roll strip caster, which was then also hot-rolled into a hot strip with a hot rolling end temperature WET. The processing to the hot strip was carried out in a continuous process sequence without interruption following the strip casting, so that the precursor already had a temperature lying in the range of inventively predetermined preheating temperatures when entering the hot rolling device and the preheating could be omitted. Also, the hot strip produced from the steel E3 has been coiled after hot rolling at a reel temperature HT to form a coil.
Nach dem Haspeln sind die jeweils erzeugten Warmbänder, soweit in Tabelle 2 nicht anders angegeben, bei einer Glühtemperatur GT über eine Glühdauer von jeweils acht Stunden einer Glühung in einer Haubenglühanlage unterzogen worden.After coiling, the hot strips produced in each case, unless otherwise indicated in Table 2, have been subjected to annealing in a bell annealing system at an annealing temperature GT over an annealing time of eight hours each time.
Die so geglühten Warmbänder sind in einer oder in zwei Stufen mit Kaltwalzgraden KWG1 (Kaltwalzgrad der ersten Kaltwalzstufe) und KWG2 (Kaltwalzgrad der jeweiligen zweiten Kaltwalzstufe) jeweils zu einem kaltgewalzten Stahlband kaltgewalzt worden. Sofern zweistufig kaltgewalzt worden ist, ist zwischen den Kaltwalzstufen jeweils eine Zwischenglühung bei einer Zwischenglühtemperatur ZGT durchgeführt worden. Nach dem Kaltwalzen haben die kaltgewalzten Stahlflachprodukte eine Schlussglühung bei einer Glühtemperatur SGT durchlaufen. Die Zwischenglühung und die Schlussglühung sind jeweils im kontinuierlichen Durchlauf absolviert worden.The so annealed hot strips were cold rolled in one or two stages with cold rolling degrees KWG1 (cold rolling degree of the first cold rolling stage) and KWG2 (cold rolling degree of the respective second cold rolling stage) each to a cold rolled steel strip. If two-stage cold rolling has been used, an intermediate annealing at an intermediate annealing temperature ZGT is in each case between the cold rolling stages Have been carried out. After cold rolling, the cold-rolled steel flat products have undergone a final annealing at an annealing temperature SGT. The intermediate annealing and the final annealing have each been completed in continuous operation.
Die jeweilige Vorwärmtemperatur VWT, Warmwalzendtemperatur WET, Haspeltemperatur HT, Glühtemperatur GT, der jeweilige Kaltwalzgrad KWG1, KWG2, sowie die jeweilige Zwischenglühtemperatur ZGT und Schlussglühtemperatur SGT, sind in Tabelle 2 angegeben.The respective preheat temperature VWT, hot rolling end temperature WET, coiler temperature HT, annealing temperature GT, the respective cold rolling degree KWG1, KWG2, and the respective intermediate annealing temperature ZGT and final annealing temperature SGT, are given in Table 2.
Die an den so erzeugten kaltgewalzten Stahlbändern ermittelten mechanischen Eigenschaften "Streckgrenze Rp0,2", "Zugfestigkeit Rm", "Dehnung A50", "r-Wert r" und "n-Wert n" sind in Tabelle 3 angegeben. Alle mechanischtechnologischen Kennwerte wurden in Querrichtung ermittelt. Zusätzlich sind in Tabelle 3die Maximalwerte der Belegung der α- und γ-Fasern angegeben.The mechanical properties "yield strength Rp0.2", "tensile strength Rm", "elongation A50", "r value r" and "n value n" determined on the cold-rolled steel strips thus produced are given in Table 3. All mechanical technological parameters were determined in the transverse direction. In addition, Table 3 shows the maximum values of the occupancy of the α and γ fibers.
Es zeigt sich, dass die aus den erfindungsgemäß zusammengesetzten Stählen E1 und E2 in erfindungsgemäßer Weise erzeugten kaltgewalzten Stahlbänder Streckgrenzen, die regelmäßig größer 300 MPa, insbesondere größer 320 MPa sind, und dabei Werte von 380 MPa und mehr erreichen, und Zugfestigkeiten, die regelmäßig größer 460 MPa, insbesondere größer 480 MPa sind, und dabei Werte von 530 MPa und mehr erreichen, sowie Dehnungswerte A50 von mindestens 18 % aufweisen, die regelmäßig mehr als 21 % erreichen, insbesondere größer 25 % sind, und dabei stets r-Werte von 1,3 oder größer besitzen.It can be seen that the cold-rolled steel strips produced from the steels E1 and E2 produced according to the invention in accordance with the invention have yield strengths which are regularly greater than 300 MPa, in particular greater than 320 MPa and thereby reach values of 380 MPa and more, and tensile strengths which are regularly greater 460 MPa, in particular greater than 480 MPa, while achieving values of 530 MPa and more, and having elongation values A50 of at least 18%, which regularly exceed 21%, in particular greater than 25%, and always have r values of 1 , 3 or greater.
Nicht erfindungsgemäß zusammengesetzte kaltgewalzte Stahlbänder erreichen solche r-Werte selbst dann nicht, wenn diese Stahlbänder unter Berücksichtigung von Herstellparametern erzeugt worden sind, die eng angelehnt sind an die Parameter, die bei der Erzeugung der erfindungsgemäßen kaltgewalzten Stahlflachprodukte eingestellt worden sind. Auch erfindungsgemäß zusammengesetzte, jedoch nicht erfindungsgemäß verarbeitete Stahlflachprodukte erreichen die Eigenschaften von erfindungsgemäß hergestellten Stahlflachprodukten nicht oder lassen sich nicht einmal kaltwalzen.Cold-rolled steel strips not assembled according to the invention do not achieve such r-values even if these steel strips have been produced taking into account production parameters that are closely related to the parameters set in the production of the cold-rolled steel flat products according to the invention. Also according to the invention composite, but not according to the invention processed flat steel products do not reach the properties of steel flat products produced according to the invention or can not even be cold-rolled.
Die erfindungsgemäß erzeugten Stahlbänder weisen dementsprechend trotz ihrer hohen Al-Gehalte eine überlegene Tiefzieheignung auf, ohne dass dazu aufwendige legierungs- oder verfahrenstechnische Maßnahmen erforderlich sind.Accordingly, the steel strips produced according to the invention have, despite their high Al contents, a superior deep-drawing capability, without the need for expensive alloying or process-engineering measures.
Ein Stahlflachprodukt mit optimalen Verformungseigenschaften (r ≈ 2, n ≈ 0,2, A50 ≈ 30 %) wird durch eine Kombination aus erfindungsgemäßer Legierung, hohem Kaltverformungsgrad und niedriger Warmwalztemperatur (ca. 850 °C) erreicht.A flat steel product with optimum deformation properties (r ≈ 2, n ≈ 0.2, A50 ≈ 30%) is achieved by a combination of alloy according to the invention, high degree of cold deformation and low hot rolling temperature (about 850 ° C).
Die aus den erfindungsgemäßen Stählen in erfindungsgemäßer Weise erzeugten kaltgewalzten Stahlbänder enthalten neben einer Fe(Al)-Mischkristallmatrix lokal auftretende härtende Vorordnungsphase. Bei gängigen Warmwalzparametern wird im vollferritischen Phasengebiet gewalzt und man erhält Warmband mit typischen dreischichtigen Gefügeaufbau, der wiederum durch rekristallisierte globulitische Randbereiche und den nur erholten Kernbereich mit Stengelkristallen gekennzeichnet ist. Die erfindungsgemäß durchgeführte Warmbandglühung baut die Versetzungsdichte im erholten Bereich ab und erleichtert ein nachfolgendes Kaltwalzprozessing. Ohne die Warmbandglühung ist die Alpha-Faserntexturkomponente stark, mit Warmbandglühung dagegen schwach ausgeprägt. Ein niedriger maximaler Kaltwalzgrad von bis zu 50 % führt zu schwachen Gamma-Fasertexturkomponenten, ein einstufiges Kaltwalzen mit einem hohen Kaltwalzgrad von mindestens 65 %, insbesondere mindestens 80 %, oder ein zweistufig durchgeführtes Kaltwalzen mit entsprechend hoher Verformung in der letzten Walzstufe führen dagegen zu einer starken Gamma-Faserkomponente. Diese Abhängigkeiten sind stärker ausgeprägt bei niedrigeren Warmwalzendtemperaturen, die im Bereich von 830 - 960 °C, insbesondere 840 - 880 °C, liegen.The cold-rolled steel strips produced from the steels according to the invention in accordance with the invention contain, in addition to a Fe (Al) mixed-crystal matrix, locally occurring hardening precursor phase. In standard hot rolling parameters, rolling is carried out in the full-ferrite phase region and hot strip with typical three-layer structure is obtained, which in turn is characterized by recrystallized globulitic margins and the only recovered core area with stem crystals is marked. The hot strip annealing performed according to the invention reduces the dislocation density in the recovered area and facilitates subsequent cold rolling processing. Without the hot strip annealing, the alpha fiber texture component is strong but weak with hot strip annealing. A low maximum cold rolling degree of up to 50% results in weak gamma fiber texture components, one-stage cold rolling with a high cold rolling degree of at least 65%, especially at least 80%, or two-stage cold rolling with correspondingly high deformation in the last rolling stage results in one strong gamma fiber component. These dependencies are more pronounced at lower hot rolling end temperatures, which are in the range of 830-960 ° C, especially 840-880 ° C.
Das Verformungsverhalten des erhaltenen kaltgewalzten Stahlflachprodukts wird von der Textur maßgeblich beeinflusst. Hohe r- und n-Werte sowie eine hohe Bruchdehnung A50 treten besonders dann auf, wenn die Gamma-Fastertexturkomponente über die Alpha-Fasertexturkomponente dominiert. Eine im erfindungsgemäßen Rahmen liegende Kombination der Nb- und Ti-Gehalte, die erfindungsgemäß vorgegebene Warmbandglühung sowie die erfindungsgemäß vorgesehenen Parameter des Kaltwalzens gewährleisten, dass dieses Ziel erreicht wird.
Claims (15)
C: 0,008 - 0,1 %,
Al: 6,5 - 12 %,
Nb: 0,1 - 0,2 %,
Ti: 0,15 - 0,5 %,
P: bis zu 0,1 %,
S: bis zu 0,03 %,
N: bis zu 0,1 %
sowie optional eines oder mehrere Elemente aus der Gruppe "Mn, Si, Seltenerdmetalle, Mo, Cr, Zr, V, W, Co, Ni, B, Cu, Ca, N" mit der Maßgabe enthält,
Mn: bis zu 1 %,
Seltenerdmetalle: bis zu 0,2 %,
Si: bis zu 2 %,
Zr: bis zu 1 %,
V: bis zu 1 %,
W: bis zu 1 %,
Mo: bis zu 1 %,
Cr: bis zu 3 %,
Co: bis zu 1 %,
Ni: bis zu 2 %,
B: bis zu 0,1 %,
Cu: bis zu 3 %,
Ca: bis zu 0,015 %,
2,5 ≥ %Ti/%Nb ≥ 1,5.
C: 0.008 - 0.1%,
Al: 6.5-12%,
Nb: 0.1-0.2%,
Ti: 0.15-0.5%,
P: up to 0.1%,
S: up to 0.03%,
N: up to 0.1%
and optionally one or more elements from the group "Mn, Si, rare earth metals, Mo, Cr, Zr, V, W, Co, Ni, B, Cu, Ca, N" with the proviso contains
Mn: up to 1%,
Rare earth metals: up to 0.2%,
Si: up to 2%,
Zr: up to 1%,
V: up to 1%,
W: up to 1%,
Mo: up to 1%,
Cr: up to 3%,
Co: up to 1%,
Ni: up to 2%,
B: up to 0.1%,
Cu: up to 3%,
Ca: up to 0.015%,
2.5 ≥% Ti /% Nb ≥ 1.5.
gekennzeichnet, dass sein Al-Gehalt mehr als 6,8 Gew.-% beträgt.Flat steel product according to one of the preceding claims, characterized
characterized in that its Al content is more than 6.8 wt .-%.
gekennzeichnet, dass sein C-Gehalt höchstens 0,05 Gew.-% beträgt.Flat steel product according to one of the preceding claims, characterized
characterized in that its C content is at most 0.05 wt .-%.
gekennzeichnet, dass sein Nb-Gehalt 0,1 - 0,15 Gew.-% beträgt.Flat steel product according to one of the preceding claims, characterized
characterized in that its Nb content is 0.1-0.15% by weight.
gekennzeichnet, dass die sein Ti-Gehalt 0,15 - 0,3 Gew.-% beträgt.Flat steel product according to one of the preceding claims, characterized
characterized in that its Ti content is 0.15-0.3% by weight.
gekennzeichnet, dass sein Gefüge 0 bis 0,1 Vol.-% κ-Karbide enthält.Flat steel product according to one of the preceding claims, characterized
characterized in that its microstructure contains 0 to 0.1 vol .-% κ-carbides.
gekennzeichnet, dass sein r-Wert mindestens 1,3 beträgt.Flat steel product according to one of the preceding claims, characterized
characterized in that its r-value is at least 1.3.
gekennzeichnet, dass in seinem Gefüge die Körner ein Verhältnis der Kornlängen in Walzrichtung zur Kornbreite in Querrichtung des Stahlflachprodukts < 1,5 aufweisen.Flat steel product according to one of the preceding claims, characterized
characterized in that in its structure, the grains have a ratio of the grain lengths in the rolling direction to the grain width in the transverse direction of the flat steel product <1.5.
Al: 6, 5 - 12 %,
Nb: 0,1 - 0,2 %,
Ti: 0,15 - 0,5 %,
P: bis zu 0,1 %,
S: bis zu 0,03 %,
N: bis zu 0,1 %
sowie optional eines oder mehrere Elemente aus der Gruppe "Mn, Si, Seltenerdmetalle, Mo, Cr, Zr, V, W, Co, Ni, B, Cu, Ca, N" mit der Maßgabe enthält,
Mn: bis zu 1 %,
Seltenerdmetalle: bis zu 0,2 %,
Si: bis zu 2 %,
Zr: bis zu 1 %,
V: bis zu 1 %,
W: bis zu 1 %,
Mo: bis zu 1 %,
Cr: bis zu 3 %,
Co: bis zu 1 %,
Ni: bis zu 2 %,
B: bis zu 0,1 %,
Cu: bis zu 3 %,
Ca: bis zu 0,015 %,
Al: 6, 5 - 12%,
Nb: 0.1-0.2%,
Ti: 0.15-0.5%,
P: up to 0.1%,
S: up to 0.03%,
N: up to 0.1%
and optionally one or more elements from the group "Mn, Si, rare earth metals, Mo, Cr, Zr, V, W, Co, Ni, B, Cu, Ca, N" with the proviso contains
Mn: up to 1%,
Rare earth metals: up to 0.2%,
Si: up to 2%,
Zr: up to 1%,
V: up to 1%,
W: up to 1%,
Mo: up to 1%,
Cr: up to 3%,
Co: up to 1%,
Ni: up to 2%,
B: up to 0.1%,
Cu: up to 3%,
Ca: up to 0.015%,
dadurch gekennzeichnet, dass die Haspeltemperatur 450 - 750 °C beträgt.Method according to one of claims 10 to 12,
characterized in that the reel temperature is 450 - 750 ° C.
dadurch gekennzeichnet, dass das Warmbandglühen als Haubenglühen durchgeführt wird.Method according to one of claims 10 to 13,
characterized in that the hot strip annealing is performed as a bell annealing.
dadurch gekennzeichnet, dass das Kaltwalzen zwei- oder mehrstufig durchgeführt wird und zwischen den Stufen des Kaltwalzens eine Zwischenglühung erfolgt.Method according to one of claims 9 to 13,
characterized in that the cold rolling is carried out in two or more stages and between the stages of cold rolling an intermediate annealing takes place.
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CN201910355506.7A CN110295317A (en) | 2013-02-14 | 2014-02-13 | Flat cold-rolled bar product and its manufacturing method for deep-draw application |
US14/767,741 US10513762B2 (en) | 2013-02-14 | 2014-02-13 | Cold-rolled flat steel product for deep drawing applications and method for production thereof |
CN201480021223.4A CN105121673A (en) | 2013-02-14 | 2014-02-13 | Cold-rolled flat steel product for deep-drawing applications and method for the production thereof |
PCT/EP2014/052810 WO2014125016A1 (en) | 2013-02-14 | 2014-02-13 | Cold-rolled flat steel product for deep-drawing applications and method for the production thereof |
JP2015557422A JP6383368B2 (en) | 2013-02-14 | 2014-02-13 | Cold rolled flat steel product for applying deep drawing and method for producing the same |
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EP3225702A1 (en) | 2016-03-29 | 2017-10-04 | Deutsche Edelstahlwerke GmbH | Steel with reduced density and method for producing a steel flat or long product made from such steel |
WO2017167778A1 (en) | 2016-03-29 | 2017-10-05 | Deutsche Edelstahlwerke Specialty Steel Gmbh & Co. Kg | Steel having reduced density and method for producing a flat or long steel product from such a steel |
WO2020078529A1 (en) * | 2018-10-15 | 2020-04-23 | Thyssenkrupp Steel Europe Ag | Method for producing an no electric strip of intermediate thickness |
US11970757B2 (en) | 2018-11-08 | 2024-04-30 | Thyssenkrupp Steel Europe Ag | Electric steel strip or sheet for higher frequency electric motor applications, with improved polarization and low magnetic losses |
Also Published As
Publication number | Publication date |
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EP2767601B1 (en) | 2018-10-10 |
JP2016511795A (en) | 2016-04-21 |
KR20150119230A (en) | 2015-10-23 |
JP6383368B2 (en) | 2018-08-29 |
BR112015019413A2 (en) | 2017-07-18 |
CN110295317A (en) | 2019-10-01 |
KR102193066B1 (en) | 2020-12-21 |
WO2014125016A1 (en) | 2014-08-21 |
CN105121673A (en) | 2015-12-02 |
US10513762B2 (en) | 2019-12-24 |
US20160017467A1 (en) | 2016-01-21 |
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