EP2383353B1 - Acier à résistance élevée comprenant du Mn, produit plat en acier composé d'un tel acier et son procédé de fabrication - Google Patents

Acier à résistance élevée comprenant du Mn, produit plat en acier composé d'un tel acier et son procédé de fabrication Download PDF

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EP2383353B1
EP2383353B1 EP11164339.1A EP11164339A EP2383353B1 EP 2383353 B1 EP2383353 B1 EP 2383353B1 EP 11164339 A EP11164339 A EP 11164339A EP 2383353 B1 EP2383353 B1 EP 2383353B1
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weight
content
strip
flat steel
maximum
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German (de)
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EP2383353A2 (fr
EP2383353A3 (fr
Inventor
Dr.-Ing. Jens-Ulrik Becker
Dr.-Ing. Jian Bian
Dr. Brigitte Hammer
Dr. Thomas Heller
Christian Höckling
Dr.-Ing. Harald Hofmann
Dipl.-Ing. Matthias Schirmer
Oliver Bülters
Thomas Rieger
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ThyssenKrupp Steel Europe AG
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ThyssenKrupp Steel Europe AG
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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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • 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
    • C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
    • 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
    • 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
    • C21D8/041—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 involving a particular fabrication or treatment of ingot or slab
    • C21D8/0415—Rapid solidification; Thin strip casting
    • 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
    • C21D8/0421—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 characterised by the working steps
    • 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
    • C21D8/0447—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 characterised by the heat treatment
    • 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
    • C21D8/0478—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 involving a particular surface treatment
    • 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

Definitions

  • DP dual-phase
  • CP complex-phase
  • MS martensitic steels
  • a problem in the development of high-strength steels is that their forming properties (elongation at break) usually deteriorate more and more with increasing strength.
  • An example of this effect is a high-strength dual-phase steel, which at a strength of 1000 MPa can only expect an A80 elongation at break of about 12%. The comparatively low elongation at break can cause the material to fail during component forming.
  • a method for producing hot strips of a formable, especially good cold deep drawable lightweight structural steel, which is to have a high tensile strength and TRIP and / or TWIP properties is known from WO 2005/061152 A1 known. According to this method, a molten steel in a horizontal strip casting plant close to the final dimensions and flow-smoothed and bend-free cast to a preliminary strip in the range between 6 and 15 mm and then fed to a further treatment.
  • a horizontal strip casting method is used for this purpose.
  • the steel used for this contains, in addition to iron and unavoidable impurities (in% by weight) C: 0.04 - 1.0%, Al: 0.05 - ⁇ 4.0%, Si: 0.05 - 6.0% , Mn 9.0-30.0% and optionally Cr: up to 6.5%, with Cr contents of 0.2-0.3% being given as preferred, Nb and V in contents of up to 0, 06% and Ti and Zr can be present in levels of up to 0.7%.
  • the effect of chromium is considered to stabilize the ⁇ -martensite and to improve the corrosion resistance.
  • higher Cr contents are recommended for Mn contents of 9-18%, while for Mn contents above 18%, lower Cr contents are considered sufficient.
  • the WO 2005/061152 A1 it indicates how this ratio should be set in practice.
  • the object of the invention was to provide a steel flat product with good strength and good ductility from a steel that can be produced more cost-effectively than the known high manganese steels and at the same time high elongation at break values and, consequently, a significantly improved Formability possesses.
  • a method for producing such a flat steel product should be specified.
  • microstructure of a steel flat product produced from such a steel according to the invention typically consists of 30-100% of hardening structures (martensite, tempered martensite or bainite), while the remainder of the structure is austenitic.
  • a steel according to the invention because of its Mn contents in an average content range, can be produced at significantly reduced alloying and production costs both during continuous casting production and during production via a strip casting process.
  • carbon firstly determines the strength of martensite and, secondly, the amount and the stability of the retained austenite.
  • the carbon content of Mn steels of the type according to the invention is below 0.5 wt .-%, with optimum properties arise when the C content to less than 0.2 wt .-%, in particular less than 0.1 wt .-%, is limited. However, if the carbon content is too low, the amount and stability of the remaining retained austenite will be affected. Therefore, the C content of a steel according to the invention is at least 0.02 wt .-%, in particular at least 0.03 wt .-%, for example at least 0.05 wt .-%.
  • Manganese is an austenite former. It retards the transformation of ferrite, pearlite and bainite and thus stabilizes austenite up to the martensite start temperature. Manganese promotes the formation of cubic or hexagonal distorted martensite ( ⁇ - or ⁇ -martensite). These manganese martensites are characterized by high strengths and a much higher toughness compared to C-induced cubic distorted ⁇ -martensite. If the manganese content is too low, bainite is formed on cooling, which results in lower strength and elongation at break. On the other hand, if the manganese content is too high, there is a risk that the entire austenite will remain stable up to room temperature.
  • the manganese content of 5-12% prescribed by the invention makes it possible to set a martensite matrix with a Residual austenite content in the microstructure. This effect occurs particularly reliably when the Mn content is at least 6% by weight or even at least 7% by weight, wherein optimization of the positive effects of manganese in a steel according to the invention can be achieved by limiting the upper limit of Mn Content is limited to 10% by weight, in particular less than 9% by weight, for example up to 8.5% by weight.
  • Aluminum and silicon are strong ferrite formers. Both elements counteract the influence of austenite formers C and Mn.
  • the essential task of the elements Si and Al in a steel according to the invention is to suppress the carbide precipitation in the martensite matrix and thus to promote the stability of the retained austenite.
  • Si and Al lead to solid solution hardening and reduce the specific gravity of the steel.
  • the Si and Al content is too low, carbide precipitation may not be effectively suppressed.
  • the contents of Si and Al are too high, the processing is made more difficult both by production by continuous casting and by production by a strip casting method.
  • the invention provides, the Si content to max. 1 wt .-%, wherein the positive effects of the presence of Si can be effectively used thereby, if the Si content of the steel according to the invention at least 0.05 wt .-%, in particular 0.1 wt .-%, is.
  • the negative effects of Si can thereby be excluded with particular certainty that the Si content is limited to 0.7% by weight, in particular 0.5% by weight.
  • the Al content can be set to at least 0.01% by weight, in particular 0.02% by weight, while negative influences of Al can be excluded with particular certainty if the Al content of a steel according to the invention is limited to 2% by weight, in particular 1% by weight.
  • the presence of copper, chromium and nickel fundamentally improves the resistance of a steel according to the invention to various corrosion mechanisms.
  • the positive effect of Cu and Ni can thereby be used with particular certainty by adding these elements having a total of at least> 0% by weight, in particular 0.1% by weight, to the steel according to the invention.
  • negative effects of the presence of Cu and / or Ni in steels of the invention are avoided by the fact that the content of Cu and Ni each max. 1 wt .-% is or the content of Cu and Ni in total to a maximum of 2 wt .-%, in particular 1 wt .-%, is limited.
  • the presence of Cr in a steel according to the invention specifically reduces the risk of the formation of stress corrosion cracking.
  • Cr contributes to the increase in strength. From a content of 0.1 wt .-% Cr these positive effects are observed, the positive effect of Cr then occurs particularly safe when the Cr content of the steel according to the invention at least 0.5 wt .-%, in particular at least 1 Wt .-%, is.
  • the Cr content of a steel according to the invention is limited to max. 4 wt .-% limited, because at higher levels Cr carbides can form, which can adversely affect the ductility of the steel. Such negative effects can be excluded by the fact that the Cr content to max. 2 wt .-% is limited.
  • the presence of Cr in a steel according to the invention has an effect if the Cr content is 1 to 2% by weight.
  • Ti, Nb and V which may be present in amounts of up to 0.5% by weight in a steel according to the invention, contribute to grain refining and strength enhancement. In total, above 0.5 wt .-% levels of Ti, Nb and V lead to no increase in this effect.
  • the strength-increasing effect of Ti, Nb and V can be used in a particularly accurate and resource-saving manner if the sum of the contents of these micro-alloying elements in a steel according to the invention is limited to 0.3% by weight, in particular 0.2% by weight , The positive effect of the micro-alloying elements mentioned here already sets in when the sum of their contents is at least 0.025% by weight. In the case of the presence of Ti, its content is advantageously reduced to max.
  • the austenitic structure can be additionally stabilized. This effect occurs already when the N content of a steel according to the invention is at least 0.002 wt .-%, in particular at least 0.0025 wt .-%, with an optimum effect results when the N content to max. 0.025 wt .-% is limited.
  • the P contents of a steel according to the invention are limited to a maximum of 0.05% by weight, preferably 0.03% by weight, in order to reliably exclude negative influences of this element.
  • the S content of a steel according to the invention is limited to max. 0.01 wt .-%, in particular 0.005 wt .-%, limited.
  • the alloy concept according to the invention is adapted so that the formation of hardened structures with or without retained austenite in the hot strip is made possible.
  • the martensite start temperature M S of a steel alloyed in the context of the invention is above and the martensite finish temperature M F of a steel assembled according to the invention is below the room temperature.
  • the castability of Mn steels according to the invention is improved as a result of the reduction in the Mn content.
  • a first possibility of warm strip production consists of conventional continuous casting.
  • an inventive steel proves to be particularly advantageous because it allows a lower hot strip thickness of less than ⁇ 2.5 mm. This is due to the fact that its deformation resistance is significantly reduced as a result of lowering the Mn content compared to conventional high-manganese steel.
  • Mn steels by strip casting.
  • hot strip thicknesses of less than 2.0 mm can be achieved.
  • the annealing of the hot strip sets the higher austenite content. Thereafter, the strength decreases, and the elongation at break increases significantly.
  • hot strip annealing up to 70% austenite is adjusted according to the analysis concept, which is mainly responsible for improving the elongation at break. Since a martensite matrix is present in the unannealed hot strip, it is difficult to process it directly to cold strip. Thus, hot strip annealing may also serve the purpose of debonding the hot strip for cold rolling. For the hot strip annealing both a bell annealing and a continuous annealing comes into question.
  • Cold rolling the annealed or unannealed hot strip further reduces strip thickness and improves strip flatness.
  • the subsequent annealing removes the strain hardening for the component production and leads to the optimal microstructure setting with increased austenite content.
  • Both the annealed hot strip and the annealed cold strip can be either electrolytic or through Hot dip galvanizing (following the cold strip annealing) or be refined by other coil coating. It is also possible to provide the respective steel strip obtained with an organic coating.
  • the desired structure of a steel according to the invention with typically 30-100% hardening structure (martensite, tempered martensite or bainite) and the remainder austenite can be achieved by thermoforming and quenching the steel.
  • a molten steel containing, in addition to iron and unavoidable impurities (in% by weight) 0.1% C, 10% Mn, 0.4% Si, 0.008% N, 1.6% Al and 2% Cr is in continuous casting potted and hot rolled at a hot rolling end temperature ET of 900 ° C to a hot strip, which has been then reeled at a reel temperature HT of 650 ° C.
  • the hot strip thus obtained had a tensile strength Rm of 1400 MPa and an elongation at break A80 of 7%.
  • the residual austenite content of his structure was 14%.
  • a molten steel containing 0.1% C, 10% Mn, 0.4% Si, 0.008% N, 1.6% Al and 1.6% Cr besides iron and unavoidable impurities (in wt%) cast in a strip casting machine to a cast strip and hot rolled at a hot rolling end temperature ET of 900 ° C to a hot strip, which has been then reeled at a reel temperature HT of 650 ° C. Subsequently, a bell annealing has been carried out.
  • the tape thus obtained had a tensile strength Rm of 990 MPa and an elongation at break A50 of 27.5%.
  • the residual austenite of the obtained hot strip was 60% after annealing.
  • a hot strip which, in addition to iron and unavoidable impurities, consists of (in% by weight) 0.1% C, 7% Mn, 0.13% Si, 0.02% Al, 1.5% Cr, 0.18% Ni , 0.13% Cu, 0.02% N and 0.079% V, was subjected to bell annealing at an annealing temperature of 650 ° C over an annealing time of 40 hours.
  • the annealed hot strip had a tensile strength Rm of 1030 MPa and an elongation at break A50 of 23%.
  • the austenite content of his fabric was 30%.
  • a hot strip containing, in addition to iron and unavoidable impurities (in% by weight) 0.1% C, 7% Mn, 0.13% Si, 0.02% Al, 0.6% Cr, 0.18% Ni, 0.13% Cu, 0.02% N, and 0.079% V was cold rolled to a total deformation of 50% and then annealed at 680 ° C annealing temperature.
  • the tensile strength Rm of the obtained cold-rolled strip was 1120 MPa at an elongation at break A50 of 21%.
  • the austenite content of the microstructure was 30%.
  • the hot strip thus obtained had a tensile strength Rm of 1345 MPa and an elongation at break A80 of 5%.
  • the residual austenite content of his structure was 5.5%.
  • the hot strip obtained according to Example 5 is over an annealing time of 10 min. subjected to a hot strip annealing at 300 ° C.
  • the annealed hot strip had a tensile strength Rm of 1100 MPa at an elongation at break A80 of 8%.
  • a composite according to Example 2 hot strip is over a glow time of 10 min. subjected to a hot strip annealing at 300 ° C.
  • the annealed hot strip had a tensile strength Rm of 1300 MPa at an elongation at break A80 of 8%.
  • a hot strip consisting of (in wt%) 0.1% C, 7% Mn, 0.20% Si, 0.01% N and 2.6% Cr besides iron and unavoidable impurities is over three minutes subjected to annealing at 920 ° C, then transferred within 7 s in a quenching tank and quenched there in water. Alternatively, deterrence in oil would have been possible with the same result. After quenching, its tensile strength Rm was 1450 MPa with an elongation at break A80 of 11%. The product RmxA80 was therefore about 16,000 MPa x%.
  • the fabric of this way obtained hot strip consisted of cubic distorted ⁇ -martensite and low volume fractions of about 5% each of austenite and hexagonal distorted ⁇ martensite.
  • a hot strip containing, in addition to iron and unavoidable impurities (in% by weight) 0.1% C, 7% Mn, 0.13% Si, 0.02% Al, 1.5% Cr, 0.18% Ni, 0.13% Cu, 0.002% N and 0.08% V was cold rolled into a cold strip and then hot dip galvanized.
  • the galvanized cold strip had a tensile strength Rm of 1300 MPa at an elongation at break A50 of 15%.
  • the content of retained austenite in the structure of the obtained cast strip was 20%.
  • a hot strip containing, in addition to iron and unavoidable impurities (in% by weight) 0.08% C, 8% Mn, 0.15% Si, 0.02% Al, 1% Cr, 0.2% Ni, 0, 15% Cu, 0.015% N and 0.06% V was cold rolled into a cold strip and then subjected to bell annealing at an annealing temperature of 550 ° C. After annealing, its tensile strength Rm was 1080 MPa and its elongation at break A50 was 25%. The proportion of retained austenite in the structure of the cast strip after annealing was 30%.
  • a steel sheet containing, in addition to iron and unavoidable impurities (in% by weight), 0.05% C, 0.06% Si, 1.1% Cr, 0.01% N and 10% Mn is within three Heated to 920 ° C minutes. Subsequently, the sheet has been transferred within 7 s in each case a quenching tank in which it has been quenched in oil or water.
  • the oil quenched steel had a tensile strength Rm of 1390 MPa at a breaking elongation A80 of 12%. Accordingly, the product Rm * A was 16,680 MPa%.
  • the quenched steel in water had a tensile strength Rm of 1350 MPa at a breaking elongation A80 of 12%.
  • the product Rm * A was accordingly 16200 MPa% for the water quenched steel.
  • the microstructure of the steel consisted of cubically distorted ⁇ -martensite and low volume contents of tough austenite (about 4%) and hexagonal distorted ⁇ -martensite (about 6%).
  • a steel sheet containing, in addition to iron and unavoidable impurities (in% by weight), 0.05% C, 10% Mn, 0.06% Si, 0.009% N, 1.1% Cr and 1% Ni is within heated to 920 ° C for three minutes. Subsequently, the sheet has been transferred within 7 s in each case a quenching tank in which it has been quenched in oil or water.
  • the oil quenched steel had a tensile strength Rm of 1315 MPa at an elongation at break A80 of 12.1%.
  • the product Rm * A was accordingly 15910 MPa%.
  • the water-quenched steel had a tensile strength Rm of 1285 MPa at a breaking elongation A80 of 12.3%.
  • the product Rm * A was therefore 15810 MPa%.
  • the microstructure of the steel was cubic distorted ⁇ -martensite and low Volume contents of tough austenite (about 7%) and hexagonal distorted ⁇ -martensite (about 5%).
  • the oil quenched steel had a tensile strength Rm of 1350 MPa at an elongation at break A80 of 10.8%. Accordingly, the product Rm * A was 14580 MPa%.
  • the water-quenched steel had a tensile strength Rm of 1350 MPa at an elongation at break A80 of 10.6%. For the water-quenched steel, the product Rm * A was 14310 MPa%.
  • the microstructure of the steel consisted of cubically distorted ⁇ -martensite and low volume contents of tough austenite (about 12%).
  • the procedure according to the invention achieves an improved combination of component strength and residual deformation capacity, which is characterized by high values of the product of tensile strength and respective elongation at break compared to the state of the art for hot-formed highest-strength materials.

Claims (17)

  1. Produit plat en acier avec une épaisseur n'excédant pas 2,5 mm et un allongement à la rupture A80 d'au moins 4 % et une résistance à la traction Rm de 900 - 1 500 MPa qui est constitué, en plus du fer et des impuretés inévitables, des éléments suivants (en % en poids) :
    C : 0,02 - 0,5 %,
    Mn : 5 - 12,0%,
    Si : 0,05 - 1,0 %,
    Al : jusqu'à 3,0 %,
    Cr : 0,1 - 4,0%,
    Cu : jusqu'à 2,0 %,
    Ni : jusqu'à 2,0 %,
    N : jusqu'à 0,05 %,
    P : jusqu'à 0,05 %,
    S : jusqu'à 0,01 %
    et
    optionnellement d'un élément ou de plusieurs éléments sélectionnés dans le groupe « V, Nb, Ti », la somme des teneurs de ces éléments étant tout au plus égale à 0,5 %,
    la structure de l'acier étant constituée de 30 à 100 % d'une structure de durcissement (martensite, martensite revenue, bainite), tandis que le reste de la structure est austénitique.
  2. Produit plat en acier selon la revendication 1, caractérisé en ce que sa teneur en C est au moins de 0,03 % en poids.
  3. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Mn est tout au plus de 10 % en poids.
  4. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Mn est inférieure à 9,5 % en poids.
  5. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Si est tout au plus de 0,5 % en poids.
  6. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Al est tout au plus de 2 % en poids.
  7. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Cr est au moins de 0,5 % en poids.
  8. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Cr est au moins de 1 % en poids.
  9. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Cr est tout au plus de 3 % en poids.
  10. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Cr est tout au plus de 2 % en poids.
  11. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Cu est tout au plus de 1 % en poids.
  12. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Ni est tout au plus de 1 % en poids.
  13. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en N est au moins de 0,0025 % en poids.
  14. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en N est tout au plus de 0,03 % en poids.
  15. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que la somme des teneurs des éléments optionnellement présents du groupe constitué par « V. Nb, Ti » est tout au plus égale à 0,3 % en poids.
  16. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que la teneur en Ti présente optionnellement est tout au plus égale à 0,15 % en poids.
  17. Procédé de fabrication d'un produit plat en acier constitué conformément à l'une des revendications 1 à 16, comportant les étapes de travail suivantes :
    - Fusion d'une masse d'acier qui est constitué, en plus du fer et des impuretés inévitables, des éléments suivants (en % en poids) :
    C : 0,02 - 0,5 %,
    Mn : 5 - 12,0 %,
    Si : 0,05 - 1,0 %,
    Al : jusqu'à 3,0 %,
    Cr : 0,1 - 4,0 %,
    Cu : jusqu'à 2,0 %,
    Ni : jusqu'à 2,0 %,
    N : jusqu'à 0,05 %,
    P: jusqu'à 0,05 %,
    S : jusqu'à 0,01 %
    et optionnellement d'un élément ou de plusieurs éléments sélectionnés dans le groupe « V, Nb, Ti », la somme des teneurs de ces éléments étant tout au plus égale à 0,5 %,
    - Production d'un produit de départ pour un laminage à chaud consécutif, en ce que l'acier en fusion est coulé en un toron dont au moins une brame ou une brame mince est séparée en tant que produit de départ pour le laminage à chaud, ou est coulé en une bande obtenue par coulée, la bande étant amenée en tant que produit de départ au laminage à chaud,
    - Traitement thermique du produit de départ afin d'amener le produit de départ à une température de début de laminage à chaud de 1 1 50 - 1 000 °C,
    - Laminage à chaud du produit de départ en une bande à chaud avec une épaisseur tout au plus de 2,5 mm, le laminage à chaud étant achevé à une température finale de laminage à chaud de 1 050 - 800 °C,
    - Embobinage de la bande à chaud en une bobine à une température d'embobinage ≤ 700 °C,
    - Les étapes de travail suivantes pouvant être chacune au choix consécutives à l'embobinage :
    - Recuit de la bande à chaud à une température de recuit de la bande à chaud de 250 - 950 °C,
    - Laminage à froid de la bande à chaud recuite dans une étape ou plusieurs étapes en une bande à froid avec une épaisseur étant tout au plus de 60 % de celle de la bande à chaud,
    - Recuit de la bande à froid à une température de recuit de 450 - 950 °C,
    - Revêtement de la surface de la bande à chaud ou de la bande à froid avec un revêtement anticorrosif métallique,
    - Revêtement de la surface de la bande à chaud ou de la bande à froid avec un revêtement organique.
EP11164339.1A 2010-04-30 2011-04-29 Acier à résistance élevée comprenant du Mn, produit plat en acier composé d'un tel acier et son procédé de fabrication Active EP2383353B1 (fr)

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EP3589757A1 (fr) * 2017-03-01 2020-01-08 Ak Steel Properties, Inc. Acier laminé à chaud à très haute résistance et son procédé de fabrication
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CN110306117B (zh) * 2019-08-02 2021-04-02 宝武集团鄂城钢铁有限公司 一种高均匀性超厚结构用钢板及其制造方法
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WO2022068201A1 (fr) * 2020-10-02 2022-04-07 The University Of Hong Kong Acier au manganèse demi-dur robuste et ductile et son procédé de fabrication
CN114150227B (zh) * 2021-12-07 2022-11-18 武汉科技大学 用中薄板坯轧制Rm≥1500MPa高韧性热冲压钢及生产方法
CN115572887B (zh) * 2022-10-31 2023-06-09 常州大学 一种超细孪晶梯度结构中锰钢及其制备方法

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