EP3405593B1 - Plat produit en acier et méthode de fabrication - Google Patents
Plat produit en acier et méthode de fabrication Download PDFInfo
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- EP3405593B1 EP3405593B1 EP16701442.2A EP16701442A EP3405593B1 EP 3405593 B1 EP3405593 B1 EP 3405593B1 EP 16701442 A EP16701442 A EP 16701442A EP 3405593 B1 EP3405593 B1 EP 3405593B1
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- flat steel
- steel product
- steel
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- 229910000831 Steel Inorganic materials 0.000 title claims description 119
- 239000010959 steel Substances 0.000 title claims description 119
- 238000004519 manufacturing process Methods 0.000 title claims description 22
- 238000000034 method Methods 0.000 title claims description 12
- 239000000047 product Substances 0.000 claims description 60
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 46
- 229910052796 boron Inorganic materials 0.000 claims description 26
- 238000005098 hot rolling Methods 0.000 claims description 26
- 229910052719 titanium Inorganic materials 0.000 claims description 25
- 239000011159 matrix material Substances 0.000 claims description 22
- 239000012535 impurity Substances 0.000 claims description 14
- 229910052721 tungsten Inorganic materials 0.000 claims description 13
- 229910052720 vanadium Inorganic materials 0.000 claims description 13
- 229910052758 niobium Inorganic materials 0.000 claims description 12
- 229910052715 tantalum Inorganic materials 0.000 claims description 12
- 229910052802 copper Inorganic materials 0.000 claims description 10
- 229910052759 nickel Inorganic materials 0.000 claims description 10
- 239000002244 precipitate Substances 0.000 claims description 10
- 229910052726 zirconium Inorganic materials 0.000 claims description 10
- 238000000137 annealing Methods 0.000 claims description 9
- 229910052791 calcium Inorganic materials 0.000 claims description 9
- 229910052742 iron Inorganic materials 0.000 claims description 9
- 229910052750 molybdenum Inorganic materials 0.000 claims description 9
- 229910052761 rare earth metal Inorganic materials 0.000 claims description 9
- 150000002910 rare earth metals Chemical class 0.000 claims description 9
- 229910052710 silicon Inorganic materials 0.000 claims description 9
- 238000005266 casting Methods 0.000 claims description 7
- 229910052804 chromium Inorganic materials 0.000 claims description 7
- 239000002245 particle Substances 0.000 claims description 6
- 229910017372 Fe3Al Inorganic materials 0.000 claims description 5
- 238000010438 heat treatment Methods 0.000 claims description 5
- 229910052748 manganese Inorganic materials 0.000 claims description 5
- 238000002844 melting Methods 0.000 claims description 4
- 238000010276 construction Methods 0.000 claims description 3
- 230000008018 melting Effects 0.000 claims description 3
- 239000000161 steel melt Substances 0.000 claims description 3
- QYEXBYZXHDUPRC-UHFFFAOYSA-N B#[Ti]#B Chemical compound B#[Ti]#B QYEXBYZXHDUPRC-UHFFFAOYSA-N 0.000 claims 4
- 229910033181 TiB2 Inorganic materials 0.000 claims 4
- 239000002243 precursor Substances 0.000 claims 4
- 239000010936 titanium Substances 0.000 description 29
- 229910045601 alloy Inorganic materials 0.000 description 17
- 239000000956 alloy Substances 0.000 description 17
- 239000011651 chromium Substances 0.000 description 10
- 239000010949 copper Substances 0.000 description 10
- 230000000694 effects Effects 0.000 description 10
- 239000011572 manganese Substances 0.000 description 10
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 10
- 239000000463 material Substances 0.000 description 9
- 238000005096 rolling process Methods 0.000 description 9
- 230000007704 transition Effects 0.000 description 9
- 239000011575 calcium Substances 0.000 description 8
- 230000007797 corrosion Effects 0.000 description 8
- 238000005260 corrosion Methods 0.000 description 8
- 239000010955 niobium Substances 0.000 description 7
- 238000012360 testing method Methods 0.000 description 7
- 230000015572 biosynthetic process Effects 0.000 description 6
- 229910052799 carbon Inorganic materials 0.000 description 6
- 230000003647 oxidation Effects 0.000 description 6
- 238000007254 oxidation reaction Methods 0.000 description 6
- 229910052698 phosphorus Inorganic materials 0.000 description 5
- 229910000838 Al alloy Inorganic materials 0.000 description 4
- 238000007792 addition Methods 0.000 description 4
- 229910052782 aluminium Inorganic materials 0.000 description 4
- 230000008092 positive effect Effects 0.000 description 4
- 230000008569 process Effects 0.000 description 4
- 229910052717 sulfur Inorganic materials 0.000 description 4
- 238000003466 welding Methods 0.000 description 4
- 241000196324 Embryophyta Species 0.000 description 3
- 230000009931 harmful effect Effects 0.000 description 3
- 230000006872 improvement Effects 0.000 description 3
- 229910000765 intermetallic Inorganic materials 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 150000001247 metal acetylides Chemical class 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 238000013001 point bending Methods 0.000 description 3
- 229910018575 Al—Ti Inorganic materials 0.000 description 2
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 229910015372 FeAl Inorganic materials 0.000 description 2
- 239000000470 constituent Substances 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 239000000155 melt Substances 0.000 description 2
- 238000000465 moulding Methods 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 238000005554 pickling Methods 0.000 description 2
- 238000011160 research Methods 0.000 description 2
- 238000007711 solidification Methods 0.000 description 2
- 230000008023 solidification Effects 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- 229910000521 B alloy Inorganic materials 0.000 description 1
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 1
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- UJXVAJQDLVNWPS-UHFFFAOYSA-N [Al].[Al].[Al].[Fe] Chemical compound [Al].[Al].[Al].[Fe] UJXVAJQDLVNWPS-UHFFFAOYSA-N 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 239000007864 aqueous solution Substances 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 239000010941 cobalt Substances 0.000 description 1
- 229910017052 cobalt Inorganic materials 0.000 description 1
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000006735 deficit Effects 0.000 description 1
- 230000001419 dependent effect Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 230000029142 excretion Effects 0.000 description 1
- 239000003779 heat-resistant material Substances 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 229910021326 iron aluminide Inorganic materials 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 238000005457 optimization Methods 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 239000002893 slag Substances 0.000 description 1
- 238000010561 standard procedure Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 description 1
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 1
- 239000010937 tungsten Substances 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical group [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 229910052845 zircon Inorganic materials 0.000 description 1
- GFQYVLUOOAAOGM-UHFFFAOYSA-N zirconium(iv) silicate Chemical compound [Zr+4].[O-][Si]([O-])([O-])[O-] GFQYVLUOOAAOGM-UHFFFAOYSA-N 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
-
- C—CHEMISTRY; METALLURGY
- 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
Definitions
- the invention relates to a flat steel product based on Fe-Al-Ti-B and a method for producing such a flat steel product.
- flat steel products when this text refers to "flat steel products", it means rolled products that are in the form of strips, sheet metal, or blanks and blanks obtained therefrom.
- the flat steel products according to the invention are heavy plate with typical plate thicknesses of 6-200 mm or hot-rolled strip or strip with typical plate thicknesses of 1.5-6 mm.
- the heat-resistant iron-based alloy presented there should be composed according to the general formula Fe x Al y C z , whereby (each in atomic%) the variable y should apply 1% ⁇ y ⁇ 28% and the variable z should apply ⁇ 24% , whereas the variable x is to be determined on the basis of a diagram depending on the respective C and Al content of the steel. It is mentioned in passing that the steel can contain more than forty further constituents, including TiB 2 , a range of 0.1-2 atom% being provided for each of these constituents. How steel procured in this way can be processed into flat steel products is left open.
- the articles also report on the results of research aimed at producing Fe 3 Al cast alloys based on boride-reinforced alloys.
- the influence of Cr and B additions on the mechanical properties and oxidation behavior of L21-ordered Fe-Al-Ti-based alloys at high temperatures "by Kerin, R. and M. Palm in Acta mater., 2008.56 (10): p 2400 - 2405 ., " L21-ordered Fe-Al-Ti alloys "by Kerin, R., et al. In Intermetallics, 2010. 18: p. 1360-1364 .
- fine-grain alloys can be produced on the basis of the Fe-Al-Ti-B system, the structure of which consists of an Fe 3 Al matrix with very small borides ( ⁇ 1 ⁇ m) along the grain boundaries.
- the compositions of the alloys are chosen so that the Fe 3 Al phase is primarily excreted, whereas the borides are excreted in the (residual) eutectic.
- the borides thus increase the strength, improve the ductility and fix the grain size of the Fe 3 Al matrix.
- Fe-Al-Ti-B cast alloys can also be modified by adding additional elements.
- elements are considered which increase the D0 3 / B2 transition temperature.
- Mo also promotes the formation of complex borides so that no more TiB 2 is formed.
- a hot-rolled ferritic steel sheet which consists of (in% by weight) 0.001-0.15% C, ⁇ 1% Mn, ⁇ 1.5% Si, 6-10% Al, 0.020-0.5% Ti, ⁇ 0.050% S, ⁇ 0.1% P and the balance consists of iron and unavoidable impurities, whereby in the steel may optionally have one or more of the following elements with the following proviso: ⁇ 1% Cr, ⁇ 1% Mo, ⁇ 1% Ni, ⁇ 0.1% Nb, ⁇ 0.2% V, ⁇ 0.01% B.
- the average ferrite grain size d IV of the structure measured on a surface perpendicular to the transverse direction in relation to the rolling is less than 100 ⁇ m.
- a correspondingly composed steel melt is cast into a preliminary product, which is then hot-rolled starting from a hot-rolling start temperature of at least 1150 ° C. to form a hot-rolled strip, the final temperature of the hot rolling being at least 900 ° C.
- the hot-rolled strip obtained is cooled in such a way that the temperature range from 850-700 ° C. is run through in more than 3 seconds in order to allow the formation of k-precipitates.
- a flat steel product according to the invention is therefore characterized in that it is made from a steel which consists of (in% by weight) Al: 12 - 20%, Cr: 0.3 - 7%, Ti: 0.2 - 2%, B: 0.1 - 0.6%, as well as optionally one or more of the elements of the group "Mn, Si, Nb, Ta, W, Zr, V, Mo, Ni, Cu, Ca, rare earth metals, Co" in the following contents: Mn: up to 2% Si: 0.05 - 5% Nb, Ta, W: in total up to 0.2% Zr: up to 1% V: up to 1% Mon: up to 1% Ni: up to 2% Cu: up to 3% Ca: up to 0.015% Rare earth metals: up to 0.2% Co: up to 1% Balance iron and unavoidable impurities, the inevitable impurities having C contents of up to 0.15% by weight, N contents of up to 0.1% by weight, S contents of up to 0.03% by weight % and P contents of up to
- % Ti /% B applies to the ratio formed from the Ti content% Ti and the B content% B of the steel 0.33 ⁇ % ⁇ Ti / % ⁇ B ⁇ 3.75 and the structure of the steel or the flat steel product made therefrom consists of 0.3-5% by volume of TiB 2 precipitates which are embedded in a structure matrix comprising at least 80% by volume of Fe 3 Al.
- the parameters for the production of the flat steel product according to the invention from a steel composed in this way are set in such a way that a structure optimization is achieved by means of which the properties of a flat steel product according to the invention are further optimized.
- the method according to the invention for producing a flat steel product designed according to the invention comprises the following steps: a) melting of a steel which consists of (in% by weight) Al: 12 - 20%, Cr: 0.3 - 7%, Ti: 0.2 - 2%, B: 0.1 - 0.6%, as well as optionally one or more of the elements of the group "Mn Si, Nb, Ta, W, Zr, V, Mo, Ni, Cu, Ca, rare earth metals, Co" in the following contents: Mn: up to 2% Si: 0.05 - 5% Nb, Ta, W: in total up to 0.2% Zr: up to 1% V: up to 1% Mon: up to 1% Ni: up to 2% Cu: up to 3% Ca: up to 0.015% Rare earth metals: up to 0.2% Co: up to 1% Remainder iron and unavoidable impurities, the inevitable impurities C contents of up to 0.15 wt .-%, N contents of up to 0.1 wt
- % and P contents of up to 0.1% by weight are to be added, and the ratio% Ti /% B which is formed from the Ti content% Ti and the B content% B of the steel applies 0.33 ⁇ % ⁇ Ti / ⁇ % ⁇ B ⁇ 3.75 ; b) pouring the molten steel into a preliminary product in the form of a slab, thin slab or cast strip; c) hot rolling the preliminary product to a hot-rolled hot strip, the preliminary product having a hot rolling start temperature of 1000-1300 ° C. at the start of hot rolling and the hot rolling end temperature being at least 850 ° C.; d) coiling the hot strip at a coiling temperature between room temperature and 750 ° C.
- Aluminum is contained in a flat steel product according to the invention in contents of 12-20% by weight. At Al contents of at least 12% by weight, in particular more than 12% by weight, the intermetallic forms Iron aluminide phase Fe 3 Al, which is the main component of the structure of a steel flat product according to the invention.
- the high Al contents lead to a reduced density, a concomitantly reduced weight, a high resistance to corrosion and oxidation, as well as a high tensile strength.
- excessively high Al contents would make the cold formability of steels according to the invention difficult. Excessive Al contents also result in poorer welding suitability due to the formation of a stable welding slag during the welding process, and an increased electrical resistance during resistance welding.
- the Al content of a steel according to the invention is limited to at most 20% by weight, in particular up to 16% by weight.
- Ti and B form titanium borides in the steel according to the invention, which bring about a fine structure, an increased yield strength, a higher ductility, a higher modulus of elasticity and increased wear resistance.
- a Ti content of at least 0.2% by weight, in particular at least 0.4% by weight, and a B content of at least 0.10% by weight, in particular at least 0, 15% by weight required.
- the Ti content% Ti is so matched to the B content% B of the steel that the ratio% Ti /% B, that is the quotient of the Ti content% Ti as dividend and the B content% B as a divisor, 0.33 to 3.75, in particular 0.5 - 3.75 or 1.0 to 3.75.
- the ratio% Ti /% B ratio at least 0.33, the risk of FeB formation is reduced.
- the low-melting phase FeB could otherwise lead to cracks during hot rolling and loss of ductility (reduction in elongation at break). This can be avoided particularly safely if the ratio% Ti /% B is 0.5-3.75, in particular 1.0-3.75.
- the presence of Ti in the flat steel product according to the invention can also improve the oxidation resistance and the heat resistance. Excessively high levels of Ti borides would, however, lead to strong solidifications if a steel flat product according to the invention is cold worked. Therefore, the upper limit of the Ti content is 2% by weight, particularly at most 1.5% by weight or 1.1% by weight, and the upper limit of the B content is 0.60% by weight, in particular at most 0.4% by weight.
- Chromium is present in the steel according to the invention in contents of up to 7% by weight and at least 0.3% by weight, in particular at least 0.5% by weight or at least 1.0% by weight, in order to reduce the brittleness Lower ductile transition temperature and improve overall ductility.
- the presence of Cr increases the resistance of the steel to low and high temperature corrosion and improves the resistance to oxidation.
- Cr contents of up to 5% by weight have been found to be particularly effective, considering the cost / benefit, and levels have also been found in practice of up to 3% by weight have been found to be sufficient to bring about the improvements in a steel according to the invention brought about by the addition of Cr.
- the brittle-ductile transition temperature can also be reduced by the optional addition of manganese in contents of up to 1% by weight.
- Mn also enters the steel as an unavoidable impurity due to production, if Mn is used for deoxidation.
- Mn contributes to increasing the strength, but can worsen the corrosion resistance. This is prevented by the maximum Mn content according to the invention being reduced to 2% by weight, in particular max. 1% by weight or max. 0.3% by weight.
- Silicon can get into the steel of a flat steel product according to the invention as a deoxidizing agent in the production of steel, but can also be added to the steel in amounts of up to 5% by weight, in particular up to 2% by weight, in order to increase the strength and corrosion resistance optimize, where too high Si contents can lead to brittle material behavior.
- the Si content of a flat steel product according to the invention is typically at least 0.05% by weight, in particular at least 0.1% by weight.
- Phosphorus and sulfur are to be attributed to the impurities of a steel according to the invention which are undesirable but which are inevitable due to the production.
- the levels of P and S should therefore be kept so low that harmful effects are avoided.
- the P content must be limited to a maximum of 0.1% by weight and the S content to a maximum of 0.03% by weight, with S contents of at most 0.01% by weight or P contents of Max. 0.05% by weight have proven to be particularly advantageous.
- the optional elements niobium, tantalum, tungsten, zircon and vanadium form with C in the steel according to the invention strength-increasing carbides and can contribute to the improvement of the heat resistance, however, if the contents are too high, they deteriorate the cold formability and weldability.
- the latter applies in particular to Nb, Ta and W, which are therefore permitted in the steel according to the invention in a total content of at most 0.2% by weight, in particular at most up to 0.1% by weight.
- the Zr and V contents in the steel according to the invention are limited to up to 1% by weight, with Zr contents of up to 0.1% by weight and V contents of up to 0.5% by weight have shown to be particularly cheap.
- Zr deteriorates the corrosion behavior, whereas if the V contents are too high, the oxidation behavior is impaired.
- the positive effects of Zr and V can be used in particular if at least 0.02% by weight of Zr or V is present in the steel.
- Molybdenum can optionally be added to the steel of a flat steel product according to the invention in order to improve the tensile strength as well as creep resistance and fatigue strength at high temperatures. Mo can also contribute to a fine structure by forming fine carbides and complex borides. These positive effects are achieved if the Mo content is at least 0.2% by weight. However, too high a Mo content leads to a deterioration in the hot and cold formability.
- the Mo content of a flat steel product according to the invention is therefore limited to a maximum of 1% by weight, in particular a maximum of 0.7% by weight.
- Nickel can optionally be present in the flat steel product according to the invention in contents of up to 2% by weight in order to improve its strength and toughness and to improve its corrosion resistance. With Ni contents of more than 2% by weight, these effects no longer increase significantly.
- the positive effects of Ni can be used in particular if there is at least 0.2% by weight, in particular at least 1% by weight, of Ni in the steel.
- Copper can also optionally be present in the steel according to the invention in order to improve the corrosion resistance.
- up to 3% by weight of Cu in particular up to 1% by weight of Cu, can be added to the steel.
- the positive effects of Cu can be used in particular if there is at least 0.2% by weight of Cu in the steel.
- Calcium can be added to the steel during steel production to bind S and to avoid clogging effects when casting the steel. Optimal effects are achieved here in steel compositions according to the invention if the Ca content is up to 0.015% by weight, in particular at most 0.01% by weight, whereby Ca can be used reliably if at least 0.001% by weight Ca in the steel available.
- Rare earth metals "SEM” can be added to the steel according to the invention in contents of up to 0.2% by weight, in particular up to 0.05% by weight, in order to improve the oxidation resistance. This effect is achieved in particular if there is at least 0.001% by weight of SEM in the steel.
- Nitrogen is at most present in the steel according to the invention as an undesirable impurity which, however, is generally unavoidable due to production. In order to avoid harmful influences, the N content must be kept as low as possible. By reducing the N content to at most 0.1% by weight, in particular max. 0.03% by weight, the formation of disadvantageous Al nitrides can be reduced to a minimum, which could impair the mechanical properties and the deformability.
- Cobalt can optionally be present in the steel according to the invention in contents of up to 1% by weight in order to increase its heat resistance. This effect is achieved in particular if there is at least 0.2% by weight of Co in the steel.
- the proportion of TiB 2 in the structure of a flat steel product according to the invention is 0.3-5% by volume.
- the presence of such amounts of TiB 2 causes ductility of the Fe 3 Al matrix as a result of a significantly increased dislocation density in the vicinity of the TiB 2 particles and promotes the recrystallization of the structure. At the same time, grain coarsening by grain boundary pinning is prevented.
- at least 0.3% by volume of TiB 2 in the structure is required, and they are particularly reliable if the content of TiB 2 in the structure of the steel according to the invention is at least 0.5% by volume, in particular at least 0.8% by volume. Harmful effects of excessively high Ti boride contents can be reliably prevented by the TiB 2 content in the structure of the steel flat product according to the invention being limited to max. 3 vol .-% is limited.
- the grain size of the Fe 3 Al of the microstructure By the grain size of the Fe 3 Al of the microstructure to at most 500 ⁇ m, in particular max. 100 ⁇ m, is limited, good strength and ductility at room temperature and good strength at high temperature are achieved.
- the average grain size of the Fe 3 Al of the microstructure should be 20-100 ⁇ m in order to ensure sufficient ductility and good creep resistance of the steel at room temperature, with average grain sizes of 50 ⁇ m having proven particularly advantageous in practice.
- the effect of the TiB 2 precipitates in the microstructure matrix of the flat steel product according to the invention can be further optimized in that at least 70% of the TiB 2 precipitates in the Microstructure matrix with an average particle diameter of 0.5-10 ⁇ m, in particular 0.7-3 ⁇ m, is present.
- the structural matrix of a flat steel product according to the invention consists of at least 80% by volume of the intermetallic phase Fe 3 Al, with the aim here being that the matrix consists of Fe 3 Al as completely as possible, optimally up to 100% by volume.
- the structure matrix can also contain optional contents of the mixed crystal Fe (Al) or of the intermetallic phase FeAl. High contents of at least 80 vol .-% Fe 3 Al are necessary to adjust the high corrosion resistance, heat resistance, hardness and wear resistance.
- a steel melt composed according to the invention in the manner described above is melted in step a) of the method according to the invention and cast in step b) to form a preliminary product in the form of a slab, thin slab or cast strip.
- the operational melting of a high-alloy steel of the type according to the invention via the electric furnace route is more suitable as a result of its suitability for liquefying large amounts of alloys than via the classic blast furnace converter route of an integrated iron and steel mill.
- the melt can be cast in conventional continuous casting.
- a casting process close to the final dimension such as processes in which the melt is processed into thin slabs which are uninterruptedly after the casting into hot strip (casting and rolling process), or cast strip, is also subjected to a hot rolling process immediately thereafter.
- the respective preliminary product is brought to the preheating temperature of 1200 - 1300 ° C. This can be done in one separate heating process or by holding at the relevant temperature from the casting heat. If a separate heating is carried out, it should extend over a period of 15 - 1500 min in order to ensure homogeneous heating. If the temperature or holding time is too low, this cannot be achieved with the necessary certainty due to the low thermal conductivity of the steel, which can lead to cracks in the hot strip.
- a suitable hot rolling start temperature ensures the formability, especially in the last pass, and thus avoids high loads on the rolls.
- the hot rolling start temperature in the range of 1000-1200 ° C, in particular 1100-1170 ° C, according to the invention, the risk of damage to the roller due to excessive rolling forces can therefore be prevented.
- a too high hot rolling start temperature would, however, lead to a low strength of the material for hot rolling. This can lead to unwanted deformations during processing and sticking of the rolling stock to the rolls.
- the hot rolling end temperature must be at least 850 ° C. in order to avoid excessive rolling forces and to be able to achieve high degrees of forming. Even at even lower hot rolling end temperatures, the required flatness of the hot strip could not be guaranteed with the security required from an operational point of view.
- the hot strip is coiled in step d) at a coiling temperature that is between room temperature and 750 ° C.
- Water or aqueous solutions are particularly suitable as cooling media with which a homogeneous cooling over the strip cross-section can be guaranteed.
- Reel temperatures of at least 400 ° C, in particular at least 450 ° C, have proven particularly useful with regard to practical use, the upper limit of the range of the reel temperature being limited to a maximum of 700 ° C, in particular a maximum of 550 ° C can to avoid excessive scale formation on the hot strip.
- the hot strip obtained after hot rolling has an elongation at break of 2-4% in the tensile test.
- the hot strip can optionally be annealed at an annealing temperature of 200-1000 ° C for an annealing time of 1 - 200 h. This serves to increase the ductility at room temperature.
- a hood annealing process with a peak temperature above 650 ° C is suitable for hot strip annealing. Lower annealing temperatures or holding times show no effect, whereas higher annealing temperatures or holding times can lead to loss of ductility due to coarsening of the grain as a result of coarsening of the Ti boride particles and the Fe3Al matrix.
- the hot strip obtained according to the invention can also be subjected to a pickling treatment with common media, the pickling time being chosen so that the stable Al oxides which are formed on the hot strip are also removed.
- a flat steel product alloyed according to the invention therefore has high yield strengths and tensile strengths. At the same time, its density is greatly reduced compared to conventional steels of the same strength class.
- the typical density of steels according to the invention is in the range from 6.2 to 6.7 g / cm 3 and is typically 6.4 g / cm 3 on average. This results in a high strength / density ratio compared to other heat-resistant materials.
- the BDTT value (brittle-ductile transition) can be reduced to surprisingly low temperatures of approximately 75-100 ° C.
- Typical hot stretching limits of flat steel products according to the invention are at 650 ° C with approx. 130-170 MPa in the range of conventional ferritic Cr steels, such as the steel standardized under material number 1.4512 (hot stretching limit approx. 70 MPa) and the one designed for high heat resistance under the material number 1.4509 (hot stretch limit approx. 150 MPa) standardized steel.
- the tensile strength of the flat steel product according to the invention is still regularly at least 100 MPa.
- flat steel products produced and procured according to the invention are particularly suitable for the production of, in particular, heat-resistant components for plant construction (for example heavy plate), for gas turbines, for offshore plants and for in particular heat-resistant components for automobile construction, in particular exhaust gas systems or turbocharger housings (hot strip) .
- heat-resistant components for plant construction for example heavy plate
- gas turbines for offshore plants
- heat-resistant components for automobile construction in particular exhaust gas systems or turbocharger housings (hot strip)
- hot strip turbocharger housings
- Further preferred uses are conceivable in the low temperature range (e.g. biogas plants, brake discs, vehicle underbody).
- each of the alloys A - F listed in Table 1 were melted in a vacuum induction furnace under argon and poured into molds measuring 250 ⁇ 150 ⁇ 500 mm. After solidification, the cast blocks obtained were preheated to 1200 mm on a duo reversing stand and preheated to 1200 ° C and each divided into six pre-blocks with a height of 40 mm. The pre-blocks obtained were preheated to a preheating temperature of 1200 ° C. over a preheating period of 180 min each.
- the heated blooms starting from a hot rolling start temperature WST, were hot-rolled in a conventional manner at a hot rolling end temperature WET into hot strip with a thickness of 3 mm.
- the hot strips obtained have cooled from the respective hot rolling end temperature WET to the respective coiling temperature HT and have been wound into a coil at this temperature.
- the mechanical properties were determined in the tensile test according to DIN EN 10002, whereas the brittle-ductile transition temperature in the four-point bending test has been determined.
- alloys A - F could be rolled on a laboratory scale without any problems using industrial conditions.
- the tensile strengths Rm of flat steel products according to the invention at room temperature typically have 550-700 MPa and yield strengths Rp0.2 of 400-650 MPa with an elongation A50 of typically 2-5%.
- the tensile strength could be increased in particular if roughing and finishing rolls were carried out in different rolling directions.
- the Vickers hardness HV5 typically varies between 335 and 370 for flat steel products according to the invention.
- the hot stretch limit ⁇ 0.2 (measured transversely to the rolling direction according to DIN EN 10002) at 650 ° C is typically 120 ⁇ 170 MPa.
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- Chemical & Material Sciences (AREA)
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- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
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- Heat Treatment Of Sheet Steel (AREA)
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Claims (14)
- Produit plat en acier fabriqué à partir d'un acier qui se compose, en % massiques
Al : 12 - 20 %, Cr : 0,3 - 7 %, Ti : 0,2 - 2 %, B : 0,1 - 0,6 % Mn : jusqu'à 2 % Si : 0,05 - 5 %, Nb, Ta, W : additionnés jusqu'à 0,2 %, Zr : jusqu'à 1 %, V : jusqu'à 1 %, Mo : jusqu'à 1 %, Ni : jusqu'à 2 %, Cu : jusqu'à 3 %, Ca : jusqu'à 0,015 %, métaux de terres rares : jusqu'à 0,2 %, Co : jusqu'à 1 %
et
la relation suivante s'appliquant au rapport %Ti/%B, formé par la teneur en Ti %Ti et la teneur en B %B de l'acier - Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que la grosseur de grain du Fe3Al dans la matrice structurale est au maximum égale à 500 µm.
- Produit plat en acier selon la revendication 4, caractérisé en ce que la grosseur de grain du Fe3Al dans la matrice structurale est de préférence au maximum égale à 100 µm.
- Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce qu'au moins 70 % des précipitations de TiB2 dans la matrice structurale sont présents avec un diamètre de particule moyen de 0,5 - 10 µm.
- Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que la somme de ses teneurs en Nb, Ta, W est au maximum de 0,1 % massique.
- Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que la structure de l'acier se compose d'au moins 0,5 % volumique de précipitations de TiB2.
- Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que la structure de l'acier se compose d'au plus 3 % volumiques de précipitations de TiB2.
- Procédé de fabrication d'un produit plat en acier configuré selon l'une des revendications précédentes, comprenant les étapes de travail suivantes :a) fusion d'un acier qui se compose, en % massiques
Al : 12 - 20 %, Cr : 0,3 - 7 %, Ti : 0,2 - 2 %, B : 0,10 - 0,6 % Mn : jusqu'à 2 % Si : 0,05 - 5 %, Nb, Ta, W : additionnés jusqu'à 0,2 %, Zr : jusqu'à 1 %, V : jusqu'à 1 %, Mo : jusqu'à 1 %, Ni : jusqu'à 2 %, Cu : jusqu'à 3 %, Ca : jusqu'à 0,015 %, métaux de terres rares : jusqu'à 0,2 %, Co : jusqu'à 1 % b) coulée de l'acier liquide en un produit semi-fini sous la forme d'une brame, d'une brame mince ou d'un feuillard de coulée ;c) laminage à chaud du produit semi-fini en un feuillard laminé à chaud, le produit semi-fini présentant au début du laminage à chaud une température de début de laminage à chaud de 1000 - 1300 °C et la température de fin de laminage à chaud étant au moins égale à 850 °C ;d) dévidage du feuillard laminé à chaud à une température de dévidage comprise entre la température ambiante et 750 °C. - Procédé selon la revendication 10, caractérisé en ce que le feuillard laminé à chaud obtenu après le dévidage (étape d)) est recuit à une température de recuit de 200 - 1000 °C sur une durée de recuit de 1-200 h.
- Procédé selon l'une des revendications 10 ou 11, caractérisé en ce que le produit semi-fini est réchauffé à la température de début de laminage à chaud sur une durée de réchauffage de 15 - 1500 min entre les étapes de travail b) et c).
- Procédé selon l'une des revendications 10 à 12, caractérisé en ce que la température de dévidage est au moins égale à 400 °C.
- Utilisation d'un produit plat en acier configuré selon l'une des revendications 1 à 9 pour la fabrication de composants pour la construction d'équipements, pour la fabrication de composants pour des turbines à gaz, pour la fabrication de composants particulièrement résistants à la chaleur pour la construction automobile, pour la fabrication de composants pour des installations qui sont utilisées dans la plage des basses températures, ainsi que pour la fabrication d'éléments structuraux par façonnage après un réchauffage préalable.
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
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PCT/EP2016/051109 WO2017125147A1 (fr) | 2016-01-20 | 2016-01-20 | Produit plat en acier et son procédé de fabrication |
Publications (2)
Publication Number | Publication Date |
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EP3405593A1 EP3405593A1 (fr) | 2018-11-28 |
EP3405593B1 true EP3405593B1 (fr) | 2020-05-20 |
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Family Applications (1)
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EP16701442.2A Not-in-force EP3405593B1 (fr) | 2016-01-20 | 2016-01-20 | Plat produit en acier et méthode de fabrication |
Country Status (4)
Country | Link |
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US (1) | US20190032161A1 (fr) |
EP (1) | EP3405593B1 (fr) |
CN (1) | CN108603257B (fr) |
WO (1) | WO2017125147A1 (fr) |
Families Citing this family (2)
Publication number | Priority date | Publication date | Assignee | Title |
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CN107791327A (zh) * | 2017-11-08 | 2018-03-13 | 刘兴满 | 一种水泵转轴的制造工艺 |
EP3719147A1 (fr) * | 2019-04-01 | 2020-10-07 | ThyssenKrupp Steel Europe AG | Produit en acier plat laminé à chaud et son procédé de fabrication |
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Publication number | Priority date | Publication date | Assignee | Title |
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DE59209325D1 (de) * | 1992-09-16 | 1998-06-18 | Sulzer Innotec Ag | Herstellung von Eisenaluminid-Werkstoffen |
JPH08100243A (ja) | 1994-08-05 | 1996-04-16 | Toyota Motor Corp | 高耐熱性鉄基合金 |
EP1995336A1 (fr) * | 2007-05-16 | 2008-11-26 | ArcelorMittal France | Acier à faible densité présentant une bonne aptitude à l'emboutissage |
-
2016
- 2016-01-20 WO PCT/EP2016/051109 patent/WO2017125147A1/fr active Application Filing
- 2016-01-20 US US16/071,566 patent/US20190032161A1/en not_active Abandoned
- 2016-01-20 CN CN201680079664.9A patent/CN108603257B/zh active Active
- 2016-01-20 EP EP16701442.2A patent/EP3405593B1/fr not_active Not-in-force
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Also Published As
Publication number | Publication date |
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WO2017125147A1 (fr) | 2017-07-27 |
CN108603257A (zh) | 2018-09-28 |
EP3405593A1 (fr) | 2018-11-28 |
CN108603257B (zh) | 2021-02-26 |
US20190032161A1 (en) | 2019-01-31 |
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