EP3405593B1 - Plat produit en acier et méthode de fabrication - Google Patents

Plat produit en acier et méthode de fabrication Download PDF

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Publication number
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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EP
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Prior art keywords
weight
levels
flat steel
steel product
steel
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EP16701442.2A
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German (de)
English (en)
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EP3405593A1 (fr
Inventor
Harald Hofmann
Hans Ferkel
Michael Gövert
Matthias Schirmer
Martin PALM
Dirk PONGE
Andreas TRIEBELS
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Max Planck Institut fuer Eisenforschung
ThyssenKrupp Steel Europe AG
ThyssenKrupp AG
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Max Planck Institut fuer Eisenforschung
ThyssenKrupp Steel Europe AG
ThyssenKrupp AG
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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)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)

Claims (14)

  1. 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 %
    ainsi que, respectivement en option, d'un ou plusieurs des éléments du groupe « Mn, Si, Nb, Ta, W, Zr, V, Mo, Ni, Cu, Ca, métaux de terres rares, Co » dans les teneurs suivantes : 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 %
    le reste étant du fer et les inévitables impuretés, des teneurs en C jusqu'à 0,15 % massique, des teneurs en N jusqu'à 0,1 % massique, des teneurs en S jusqu'à 0,03 % massiques et des teneurs en P jusqu'à 0,1 massique étant à ajouter aux inévitables impuretés,
    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 0,33 ≤ % ⁢ Ti / % ⁢ B ≤ 3,75
    Figure imgb0009
     et aussi la structure de l'acier se compose de 0,3 à 5 % volumiques de précipitations de TiB2, qui sont enrobées dans une matrice structurale composée d'au moins 80 % volumiques de Fe3Al.
  2. Produit plat en acier selon la revendication 1, caractérisé en ce que le rapport %Ti/%B est de 0,5 ≤ % ⁢ Ti/ ⁢ % ⁢ B ≤ 3,75 .
    Figure imgb0010
  3. Produit plat en acier selon la revendication 2, caractérisé en ce que le rapport %Ti/%B est de 1,0 ≤ % ⁢ Ti/ ⁢ % ⁢ B ≤ 3,75 .
    Figure imgb0011
  4. 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.
  5. 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.
  6. 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.
  7. 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.
  8. 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.
  9. 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.
  10. 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 %
    ainsi que, respectivement en option, d'un ou plusieurs des éléments du groupe « Mn, Si, Nb, Ta, W, Zr, V, Mo, Ni, Cu, Ca, métaux de terres rares, Co » dans les teneurs suivantes : 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 %
    le reste étant du fer et les inévitables impuretés, des teneurs en C jusqu'à 0,15 % massique, des teneurs en N jusqu'à 0,1 % massique, des teneurs en S jusqu'à 0,03 % massiques et des teneurs en P jusqu'à 0,1 massique étant à ajouter aux inévitables impuretés, et la relation 0,33 ≤ %Ti/%B ≤ 3,75 s'appliquant au rapport %Ti/%B, formé par la teneur en Ti %Ti et la teneur en B %B de l'acier ;
    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.
  11. 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.
  12. 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).
  13. Procédé selon l'une des revendications 10 à 12, caractérisé en ce que la température de dévidage est au moins égale à 400 °C.
  14. 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.
EP16701442.2A 2016-01-20 2016-01-20 Plat produit en acier et méthode de fabrication Active EP3405593B1 (fr)

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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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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

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