EP2767601A1 - Produit plat en acier laminé à froid pour applications d'emboutissage profond et son procédé de fabrication - Google Patents
Produit plat en acier laminé à froid pour applications d'emboutissage profond et son procédé de fabrication 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
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 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
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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
- C22C38/04—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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Priority Applications (8)
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EP13155225.9A EP2767601B1 (fr) | 2013-02-14 | 2013-02-14 | Produit plat en acier laminé à froid pour applications d'emboutissage profond et son procédé de fabrication |
PCT/EP2014/052810 WO2014125016A1 (fr) | 2013-02-14 | 2014-02-13 | Produit plat en acier laminé à froid pour emboutissage et son procédé de fabrication |
JP2015557422A JP6383368B2 (ja) | 2013-02-14 | 2014-02-13 | 深絞りを適用するための冷間圧延された平鋼製品及びそれを製造するための方法 |
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 |
KR1020157024979A KR102193066B1 (ko) | 2013-02-14 | 2014-02-13 | 딥드로잉 적용을 위한 냉간압연 평강 제품 및 그 제조 방법 |
CN201910355506.7A CN110295317A (zh) | 2013-02-14 | 2014-02-13 | 用于深冲应用的冷轧扁钢产品及其制造方法 |
BR112015019413A BR112015019413A2 (pt) | 2013-02-14 | 2014-02-13 | produto plano de aço laminado a frio para aplicações de estampagem e método para a sua produção |
CN201480021223.4A CN105121673A (zh) | 2013-02-14 | 2014-02-13 | 用于深冲应用的冷轧扁钢产品及其制造方法 |
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EP (1) | EP2767601B1 (fr) |
JP (1) | JP6383368B2 (fr) |
KR (1) | KR102193066B1 (fr) |
CN (2) | CN105121673A (fr) |
BR (1) | BR112015019413A2 (fr) |
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Cited By (6)
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US20170002436A1 (en) * | 2015-07-01 | 2017-01-05 | Posco | Ferritic lightweight steel sheet having excellent strength and ductility and method for manufacturing the same |
WO2017021464A1 (fr) * | 2015-08-05 | 2017-02-09 | Salzgitter Flachstahl Gmbh | Acier hautement résistant contenant du manganèse, utilisation de l'acier pour des produits plats en acier laminés flexibles et procédé de fabrication et produit plat en acier le concernant |
DE102015116186A1 (de) | 2015-09-24 | 2017-03-30 | Thyssenkrupp Ag | Halbzeug und Verfahren zur Herstellung einer Fahrzeugkomponente, Verwendung eines Halbzeugs und Fahrzeugkomponente |
EP3225702A1 (fr) | 2016-03-29 | 2017-10-04 | Deutsche Edelstahlwerke GmbH | Acier a epaisseur reduite et procede de fabrication d'un produit allonge ou plat en acier a partir d'un tel acier |
WO2020078529A1 (fr) * | 2018-10-15 | 2020-04-23 | Thyssenkrupp Steel Europe Ag | Procédé de fabrication d'une bande en acier électrique à grains non orientés dotée d'une épaisseur intermédiaire |
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 |
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DE102014017274A1 (de) * | 2014-11-18 | 2016-05-19 | Salzgitter Flachstahl Gmbh | Höchstfester lufthärtender Mehrphasenstahl mit hervorragenden Verarbeitungseigenschaften und Verfahren zur Herstellung eines Bandes aus diesem Stahl |
CN107254636B (zh) * | 2017-05-02 | 2019-02-22 | 嘉禾福顺机械实业有限公司 | 一种泵用合金钢材料及其制备方法 |
CN113584406A (zh) * | 2021-07-14 | 2021-11-02 | 武汉钢铁有限公司 | 一种csp工艺生产的防火门板用钢及其制造方法 |
Citations (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
GB1044801A (en) * | 1963-01-30 | 1966-10-05 | Yawata Iron & Steel Co | Improvements in or relating to aluminum steels |
EP0826787A2 (fr) * | 1996-08-27 | 1998-03-04 | Fried. Krupp AG Hoesch-Krupp | Acier pour des éléments de construction et son utilisation dans les voitures et pour les revetements de facade |
JP2001271136A (ja) * | 2000-03-27 | 2001-10-02 | Nisshin Steel Co Ltd | 耐高温酸化性に優れた溶融アルミニウムめっき鋼板及びその製造方法 |
JP2007321168A (ja) * | 2006-05-30 | 2007-12-13 | Jfe Steel Kk | 高剛性低密度鋼板およびその製造方法 |
JP2010121213A (ja) * | 2003-06-18 | 2010-06-03 | Nippon Steel Corp | 延性に優れた高強度低比重鋼板の製造方法 |
US20100300585A1 (en) * | 2007-05-16 | 2010-12-02 | Arcelormittal France | Low-density steel having good drawability |
Family Cites Families (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4334923A (en) | 1980-02-20 | 1982-06-15 | Ford Motor Company | Oxidation resistant steel alloy |
JP3790398B2 (ja) | 1999-12-10 | 2006-06-28 | 新日本製鐵株式会社 | 加工部断面耐食性に優れた被覆鋼 |
JP2001271148A (ja) | 2000-03-27 | 2001-10-02 | Nisshin Steel Co Ltd | 耐高温酸化性に優れた高Al鋼板 |
DE10128544C2 (de) * | 2001-06-13 | 2003-06-05 | Thyssenkrupp Stahl Ag | Höherfestes, kaltumformbares Stahlblech, Verfahren zu seiner Herstellung und Verwendung eines solchen Blechs |
CN1161488C (zh) * | 2001-10-19 | 2004-08-11 | 大田精密工业股份有限公司 | 低密度高延展性铁基的高尔夫球铁杆头的合金材料及其应用 |
JP2005060728A (ja) * | 2003-08-11 | 2005-03-10 | Nippon Steel Corp | 低比重溶融アルミめっき鋼板及びそのプレス加工方法 |
JP2005325388A (ja) * | 2004-05-13 | 2005-11-24 | Kiyohito Ishida | 低比重鉄合金 |
JP4324072B2 (ja) * | 2004-10-21 | 2009-09-02 | 新日本製鐵株式会社 | 延性に優れた軽量高強度鋼とその製造方法 |
KR100985298B1 (ko) * | 2008-05-27 | 2010-10-04 | 주식회사 포스코 | 리징 저항성이 우수한 저비중 고강도 열연 강판, 냉연강판, 아연도금 강판 및 이들의 제조방법 |
-
2013
- 2013-02-14 EP EP13155225.9A patent/EP2767601B1/fr active Active
-
2014
- 2014-02-13 JP JP2015557422A patent/JP6383368B2/ja not_active Expired - Fee Related
- 2014-02-13 CN CN201480021223.4A patent/CN105121673A/zh active Pending
- 2014-02-13 BR BR112015019413A patent/BR112015019413A2/pt active Search and Examination
- 2014-02-13 US US14/767,741 patent/US10513762B2/en not_active Expired - Fee Related
- 2014-02-13 KR KR1020157024979A patent/KR102193066B1/ko active IP Right Grant
- 2014-02-13 WO PCT/EP2014/052810 patent/WO2014125016A1/fr active Application Filing
- 2014-02-13 CN CN201910355506.7A patent/CN110295317A/zh active Pending
Patent Citations (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
GB1044801A (en) * | 1963-01-30 | 1966-10-05 | Yawata Iron & Steel Co | Improvements in or relating to aluminum steels |
EP0826787A2 (fr) * | 1996-08-27 | 1998-03-04 | Fried. Krupp AG Hoesch-Krupp | Acier pour des éléments de construction et son utilisation dans les voitures et pour les revetements de facade |
JP2001271136A (ja) * | 2000-03-27 | 2001-10-02 | Nisshin Steel Co Ltd | 耐高温酸化性に優れた溶融アルミニウムめっき鋼板及びその製造方法 |
JP2010121213A (ja) * | 2003-06-18 | 2010-06-03 | Nippon Steel Corp | 延性に優れた高強度低比重鋼板の製造方法 |
JP2007321168A (ja) * | 2006-05-30 | 2007-12-13 | Jfe Steel Kk | 高剛性低密度鋼板およびその製造方法 |
US20100300585A1 (en) * | 2007-05-16 | 2010-12-02 | Arcelormittal France | Low-density steel having good drawability |
Non-Patent Citations (2)
Title |
---|
BRUX U ET AL: "Light-weight steels based on iron-aluminium - Influence of micro alloying elements (B, Ti, Nb) on microstructures, textures and mechanical properties", STEEL RESEARCH, DUESSELDORF, DE, vol. 73, no. 12, 1 December 2002 (2002-12-01), pages 543 - 548, XP009170715, ISSN: 0177-4832 * |
S. U. BRÜX: "Tiefziehfähige Eisen-Aluminium-Leichtbaustähle", KONSTRUKTION, 4 April 2002 (2002-04-04) |
Cited By (8)
Publication number | Priority date | Publication date | Assignee | Title |
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US20170002436A1 (en) * | 2015-07-01 | 2017-01-05 | Posco | Ferritic lightweight steel sheet having excellent strength and ductility and method for manufacturing the same |
WO2017021464A1 (fr) * | 2015-08-05 | 2017-02-09 | Salzgitter Flachstahl Gmbh | Acier hautement résistant contenant du manganèse, utilisation de l'acier pour des produits plats en acier laminés flexibles et procédé de fabrication et produit plat en acier le concernant |
DE102015116186A1 (de) | 2015-09-24 | 2017-03-30 | Thyssenkrupp Ag | Halbzeug und Verfahren zur Herstellung einer Fahrzeugkomponente, Verwendung eines Halbzeugs und Fahrzeugkomponente |
WO2017050558A1 (fr) | 2015-09-24 | 2017-03-30 | Thyssenkrupp Steel Europe Ag | Produit semi-fini et procédé de fabrication d'un élément de véhicule, utilisation d'un produit semi-fini et élément de véhicule |
EP3225702A1 (fr) | 2016-03-29 | 2017-10-04 | Deutsche Edelstahlwerke GmbH | Acier a epaisseur reduite et procede de fabrication d'un produit allonge ou plat en acier a partir d'un tel acier |
WO2017167778A1 (fr) | 2016-03-29 | 2017-10-05 | Deutsche Edelstahlwerke Specialty Steel Gmbh & Co. Kg | Acier de masse volumique réduite et procédé de fabrication d'un produit acier plat ou d'un produit acier allongé réalisé dans un acier de ce type |
WO2020078529A1 (fr) * | 2018-10-15 | 2020-04-23 | Thyssenkrupp Steel Europe Ag | Procédé de fabrication d'une bande en acier électrique à grains non orientés dotée d'une épaisseur intermédiaire |
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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BR112015019413A2 (pt) | 2017-07-18 |
CN105121673A (zh) | 2015-12-02 |
KR102193066B1 (ko) | 2020-12-21 |
WO2014125016A1 (fr) | 2014-08-21 |
US10513762B2 (en) | 2019-12-24 |
JP2016511795A (ja) | 2016-04-21 |
US20160017467A1 (en) | 2016-01-21 |
EP2767601B1 (fr) | 2018-10-10 |
JP6383368B2 (ja) | 2018-08-29 |
CN110295317A (zh) | 2019-10-01 |
KR20150119230A (ko) | 2015-10-23 |
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