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EP2383353B2 - Acier à résistance élevée comprenant du Mn, produit plat en acier composé d'un tel acier et son procédé de fabrication - Google Patents
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EP2383353B2 - 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

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Publication number
EP2383353B2
EP2383353B2 EP11164339.1A EP11164339A EP2383353B2 EP 2383353 B2 EP2383353 B2 EP 2383353B2 EP 11164339 A EP11164339 A EP 11164339A EP 2383353 B2 EP2383353 B2 EP 2383353B2
Authority
EP
European Patent Office
Prior art keywords
content
steel
hot
flat steel
steel product
Prior art date
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Active
Application number
EP11164339.1A
Other languages
German (de)
English (en)
Other versions
EP2383353A3 (fr
EP2383353B1 (fr
EP2383353A2 (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
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
ThyssenKrupp Steel Europe AG
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ThyssenKrupp Steel Europe AG
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Classifications

    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0278—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing
    • C21D8/041—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing
    • C21D8/0421—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing
    • C21D8/0447—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing
    • C21D8/0478—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. 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

  • a method for producing hot-rolled strips from a formable, in particular cold-deep-drawable, lightweight structural steel, which is to possess high tensile strength and TRIP and/or TWIP properties, is derived from the WO 2005/061152 A1 known. According to this process, a steel melt is cast in a horizontal strip casting plant to a near-net-shape, flow-stabilized and bend-free pre-strip in the range between 6 and 15 mm and subsequently subjected to further processing.
  • the steel used contains, in addition to iron and unavoidable impurities (in wt.%), 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 preferred, Nb and V in total contents of up to 0.06%, and Ti and Zr in total contents of up to 0.7%.
  • Cr contents contents of 0.2–0.3% being preferred
  • Nb and V in total contents of up to 0.06%
  • Ti and Zr in total contents of up to 0.7%.
  • the effect of chromium is seen as stabilizing the ⁇ -martensite and improving corrosion resistance.
  • higher Cr contents are recommended at Mn contents of 9–18%, while lower Cr contents are considered sufficient at Mn contents above 18%.
  • WO 2005/061152 A1 it specifies how this ratio should be set in concrete terms.
  • EP 0 425 058 A1 A use of a killed-cast steel containing 0.15–0.25% C, 3.40–6.10% Mn, 0–1.0% Ni, 0–1.0% Cr, 0–1.0% Mo, 0–0.15% V, max. 0.03% P, max. 0.03% S, max. 0.6% Si, max. 0.05% Al, balance iron and usual impurities, as a material for the manufacture of tubes for reinforcing motor vehicle doors, provided that the following relationship for the sum of the alloying elements (in wt.%) is satisfied: Mn + Ni + Cr + Mo + 10 ⁇ V ⁇ 4 , 5 shareholderss ⁇ %
  • the object of the invention was to create a flat steel product with good strength and good formability from a steel that can be produced more cost-effectively than the known high-manganese steels and at the same time has high elongation at break values and thus significantly improved formability.
  • the invention proposes a material concept according to which a steel, in addition to iron and unavoidable impurities, consists of (in wt.%) C: 0.02 - 0.5% Mn: 7 - 12.0% Yes: 0.05 - 1.0% Al: up to 3.0% Cr: 1 - 4.0% Cu: up to 2.0% Ni: up to 2.0% N: up to 0.05% P: up to 0.05% S: up to 0.01% consists of and optionally contains one or more elements from the group "V, Nb, Ti", where the sum of the contents of these elements is at most 0.5%.
  • microstructure of a flat steel product produced from such a steel according to the invention typically consists of 30 - 100% hardened microstructure (martensite, tempered martensite or bainite), while the remainder of the microstructure is austenitic.
  • a steel according to the invention due to its medium-range manganese content, can be produced at significantly reduced alloying and manufacturing costs, both by continuous casting and by strip casting.
  • carbon determines, on the one hand, the strength of martensite and, on the other hand, the quantity and stability of the retained austenite. Excessively high carbon contents negatively affect the weldability and toughness of the steel, for example, through the formation of chromium carbides.
  • the carbon content of manganese steels of the type according to the invention is therefore below 0.5 wt.%, with optimal properties being achieved when the carbon content is limited to less than 0.2 wt.%, and in particular less than 0.1 wt.%.
  • the carbon 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 delays the transformation of ferrite, pearlite, and bainite, thus stabilizing austenite up to the martensite start temperature. Manganese promotes the formation of cubically or hexagonally distorted martensite ( ⁇ - or ⁇ -martensite). These manganese martensites are characterized by high strength and significantly higher toughness compared to carbon-induced, cubically distorted ⁇ -martensite. If the manganese content is too low, bainite forms upon cooling, resulting in lower strength and elongation at break. Conversely, if the manganese content is too high, there is a risk that the entire austenite will remain stable until room temperature.
  • the manganese content of 7–12% specified according to the invention allows for the creation of a martensite matrix with a retained austenite component in the microstructure. This effect is particularly likely to occur if the Mn content is at least 7 wt.%, whereby the positive effects of manganese in a steel according to the invention can be optimized by limiting the upper limit of the Mn content to 10 wt.%, in particular to less than 9 wt.%, for example to up to 8.5 wt.%.
  • Aluminum and silicon are strong ferrite formers. Both elements counteract the influence of the austenite formers carbon and manganese.
  • the essential function of the elements silicon (Si) and aluminum (Al) in a steel according to the invention is to suppress carbide precipitation in the martensite matrix and thus 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.
  • processing becomes more difficult in both continuous casting and strip casting processes.
  • the invention provides for limiting the Si content to a maximum of 1 wt.%, whereby the positive effects of the presence of Si can be effectively utilized if the Si content of the steel according to the invention is at least 0.05 wt.%, in particular 0.1 wt.%.
  • the negative effects of Si can be particularly reliably excluded by limiting the Si content to 0.7 wt.%, in particular 0.5 wt.%.
  • the Al content can be set at a minimum of 0.01 wt. %, in particular 0.02 wt. %, while negative influences of Al can be particularly reliably excluded if the Al content of a steel according to the invention is limited to 2 wt. %, in particular 1 wt. %,.
  • the presence of copper, chromium, and nickel generally improves the resistance of a steel according to the invention to various corrosion mechanisms.
  • the positive effect of Cu and Ni can be utilized particularly reliably by adding these elements to the steel according to the invention in amounts totaling at least > 0 wt.%, and in particular 0.1 wt.%.
  • negative effects of the presence of Cu and/or Ni in steels according to the invention are avoided by limiting the Cu and Ni content to a maximum of 1 wt.% each, or by limiting the total Cu and Ni content to a maximum of 2 wt.%, and in particular 1 wt.%.
  • the presence of chromium (Cr) in a steel according to the invention specifically reduces the risk of stress corrosion cracking. Cr also contributes to increased strength. These positive effects can be observed from a Cr content of 0.1 wt.%, with the positive effect of Cr being particularly reliable when the Cr content, as in the steel according to the invention, is at least 1 wt.%.
  • the Cr content of a steel according to the invention is limited to a maximum of 4 wt.% because higher contents can lead to the formation of Cr carbides, which can negatively affect the ductility of the steel. Such negative effects can be particularly reliably prevented by limiting the Cr content to a maximum of 2 wt.%.
  • the presence of Cr in a steel according to the invention has an optimal effect when the Cr content is 1–2 wt.%.
  • Ti, Nb, and V which can be present in a total of up to 0.5 wt.% in a steel according to the invention, contribute to grain refinement and increased strength. Total contents of Ti, Nb, and V exceeding 0.5 wt.% do not enhance this effect.
  • the strength-enhancing effect of Ti, Nb, and V can be utilized particularly effectively and efficiently when the total content of these microalloying elements in a steel according to the invention is limited to 0.3 wt.%, particularly 0.2 wt.%.
  • the positive effect of the microalloying elements mentioned here is already achieved when the total content is at least 0.025 wt.%. In the case of Ti, its content is advantageously limited to a maximum of 0.15 wt.% to prevent coarse Ti precipitates.
  • the austenitic microstructure can be further stabilized by the addition of nitrogen in contents of up to 0.05 wt.%, particularly 0.03 wt.%. This effect occurs even when the nitrogen content of a steel according to the invention is at least 0.002 wt.%, in particular at least 0.0025 wt.%, with an optimal effect being achieved when the nitrogen content is limited to a maximum of 0.025 wt.%.
  • the phosphorus content of a steel according to the invention is limited to a maximum of 0.05 wt.%, preferably 0.03 wt.%, in order to reliably exclude negative influences of this element.
  • the sulfur content of a steel according to the invention is limited to a maximum of 0.01 wt.%, in particular 0.005 wt.%.
  • the alloy concept according to the invention is designed to enable the formation of hardened microstructures with or without retained austenite in hot-rolled strip.
  • the martensite start temperature M ⁇ sub>S ⁇ /sub> of a steel alloyed according to the invention is above room temperature
  • the martensite finish temperature M ⁇ sub> F ⁇ /sub> of a steel composed according to the invention is below room temperature.
  • the steel flat product according to the invention is an uncoated hot-rolled strip.
  • the possibilities for producing hot-rolled or cold-rolled strips made of manganese steel are summarized in the accompanying diagram. Specifically, they comprise the following processing steps:
  • the castability of Mn steels according to the invention is improved as a result of the reduction in Mn content.
  • One method for producing hot-rolled strip is conventional continuous casting.
  • a steel according to the invention proves particularly advantageous because it allows for a reduced hot-rolled strip thickness of less than 2.5 mm. This is due to the fact that its forming resistance is significantly reduced compared to conventional high-manganese steels as a result of the lower manganese content.
  • the higher austenite content is achieved by annealing the hot-rolled strip. This reduces the strength and significantly increases the elongation at break. After hot-rolled strip annealing, up to 70% austenite content is achieved, depending on the analytical approach; this is primarily responsible for the improved elongation at break. Since a martensite matrix is present in unannealed hot-rolled strip, it is difficult to process it directly into cold-rolled strip. Therefore, hot-rolled strip annealing can also serve the purpose of softening the hot-rolled strip for cold rolling. Both hood annealing and continuous annealing are suitable methods for hot-rolled strip.
  • Cold rolling of the annealed or unannealed hot-rolled strip further reduces the strip thickness and improves strip flatness.
  • Subsequent annealing eliminates work hardening for component manufacturing and results in an optimal microstructure with an increased austenite content.
  • Both hot-annealed and cold-annealed strip can be finished either electrolytically, by hot-dip galvanizing (following cold-annealing), or by other strip coatings. It is also possible to apply an organic coating to the resulting steel strip.
  • the desired microstructure of a steel according to the invention typically comprising 30-100% hardened microstructure (martensite, tempered martensite or bainite) and the remainder being austenite, can be achieved by hot forming and quenching the steel.
  • the resulting hot strip exhibited a tensile strength (Rm) of 1400 MPa and an elongation at break (A80) of 7%.
  • the retained austenite content of its microstructure was 14%.
  • a hot-rolled strip consisting of iron and unavoidable impurities, and containing (in wt%) 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 hood annealing at a temperature of 650°C for 40 hours.
  • the annealed hot-rolled strip exhibited a tensile strength Rm of 1030 MPa and an elongation at break A50 of 23%.
  • the austenite content of its microstructure was 30%.
  • a hot-rolled strip containing, in addition to iron and unavoidable impurities (in wt.%), 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 with a total deformation of 50% and subsequently annealed continuously at a temperature of 680 °C.
  • the tensile strength Rm of the resulting cold-rolled strip was 1120 MPa with an elongation at break A50 of 21%.
  • the austenite content of the microstructure was 30%.
  • the resulting hot strip exhibited a tensile strength (Rm) of 1345 MPa and an elongation at break (A80) of 5%.
  • the retained austenite content of its microstructure was 5.5%.
  • the hot-rolled strip obtained according to Example 5 was subjected to hot-roll annealing at 300 °C for a period of 10 minutes.
  • the annealed hot-rolled strip exhibited a tensile strength Rm of 1100 MPa and an elongation at break A80 of 8%.
  • the annealed hot-rolled strip exhibited a tensile strength Rm of 1300 MPa and an elongation at break A80 of 8%.
  • the cast strip exhibited a tensile strength Rm of 1380 MPa and an elongation at break A50 of 6%.
  • the proportion of retained austenite in the microstructure of the resulting cast strip was 2%.
  • the proportion of retained austenite in the microstructure of the strip after annealing was 35%.
  • a hot-rolled strip consisting of iron and unavoidable impurities, with (in wt%) 0.1% C, 7% Mn, 0.20% Si, 0.01% N, and 2.6% Cr, was annealed at 920 °C for three minutes, then transferred to a quenching tank within 7 seconds and quenched in water. Alternatively, quenching in oil would have yielded 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 approximately 16,000 MPa x%.
  • the microstructure of the hot-rolled strip obtained in this way consisted of cubically distorted ⁇ -martensite and small volume fractions of approximately 5% each of austenite and hexagonally distorted ⁇ -martensitanium.
  • Hot-rolled strip containing, in addition to iron and unavoidable impurities (in wt.%), 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 and subsequently hot-dip galvanized.
  • the galvanized cold-rolled strip exhibited a tensile strength Rm of 1300 MPa and an elongation at break A50 of 15%.
  • the retained austenite content of the resulting cast strip was 20%.
  • the oil-quenched steel exhibited a tensile strength Rm of 1390 MPa at an elongation at break A80 of 12%.
  • the product Rm*A was therefore 16680 MPa%.
  • the water-quenched steel exhibited a tensile strength Rm of 1350 MPa at an elongation at break A80 of 12%.
  • the product Rm*A for the water-quenched steel was therefore 16200 MPa%.
  • the microstructure of the steel consisted of cubically distorted ⁇ -martensite and small volume contents of tough austenite (approx. 4%) and hexagonally distorted ⁇ -martensite (approx. 6%).
  • the steel quenched in oil exhibited a tensile strength Rm of 1315 MPa and an elongation at break A80 of 12.1%.
  • the product Rm*A was therefore 15910 MPa%.
  • the steel quenched in water exhibited a tensile strength Rm of 1285 MPa and an elongation at break A80 of 12.3%.
  • the product Rm*A for the water-quenched steel was therefore 15810 MPa%.
  • the microstructure of the steel consisted of cubically distorted ⁇ -martensite and small volume contents of tough austenite (approx. 7%) and hexagonally distorted ⁇ -martensite (approx. 5%).
  • the steel quenched in oil exhibited a tensile strength Rm of 1350 MPa and an elongation at break A80 of 10.8%.
  • the product Rm*A was therefore 14580 MPa%.
  • the steel quenched in water exhibited a tensile strength Rm of 1350 MPa and an elongation at break A80 of 10.6%.
  • the product Rm*A was therefore 14310 MPa%.
  • the microstructure of the steel consisted of cubically distorted ⁇ -martensite and small volume contents of tough austenite (approx. 12%).
  • the inventive method achieves an improved combination of component strength and residual deformation capacity compared to the prior art for hot-formed high-strength materials, which is characterized by high values of the product of tensile strength and respective elongation at break.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical 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 (15)

  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 à 1500 MPa qui est constitué, en plus du fer et des impuretés inévitables, des éléments suivants (en % en poids)
    C : 0,02 à 0,5 %,
    Mn : 7 à 12,0 %,
    Si : 0,05 à 1,0 %,
    Al: jusqu'à 3,0 %,
    Cr : 1 à 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, dans lequel le produit plat en acier est un bande à chaud non revêtu.
  2. Produit plat en acier selon la revendication 1, caractérisé en ce que sa teneur en C est d'au moins 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 tout 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 tout au plus de 3 % 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 2 % en poids.
  10. 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.
  11. 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.
  12. 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.
  13. 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.
  14. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que la somme des teneurs des éléments optionellement présents du groupe constitué par « V, Nb, Ti » est tout au plus égale à 0,3 % en poids.
  15. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que la teneur en Ti présente optionellement est tout au plus égale à 0,15 % en poids.
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 EP2383353B2 (fr)

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MX2019010379A (es) * 2017-03-01 2019-10-22 Ak Steel Properties Inc Acero laminado en caliente con muy alta resistencia, y metodo de produccion.
CN106893931A (zh) * 2017-03-04 2017-06-27 蒋培丽 一种颗粒增强型奥氏体钢及其钢板制造工艺
CN110944765B (zh) 2017-07-25 2022-02-25 蒂森克虏伯钢铁欧洲股份公司 通过热成型扁钢产品生产的金属板构件及其生产方法
WO2019122960A1 (fr) * 2017-12-19 2019-06-27 Arcelormittal Tôle d'acier laminée à froid et traitée thermiquement, son procédé de production et utilisation d'un tel acier pour produire des pièces de véhicule
DE102017223633A1 (de) 2017-12-21 2019-06-27 Voestalpine Stahl Gmbh Kaltgewalztes Stahlflachprodukt mit metallischer Korrosionsschutzschicht und Verfahren zur Herstellung eines solchen
CN111727265B (zh) * 2018-03-13 2023-03-24 Ak钢铁产权公司 含介稳态奥氏体的镀钢在升高温度下的减缩
CN109097680B (zh) * 2018-08-10 2020-07-28 宝武集团鄂城钢铁有限公司 一种使用50t中频感应炉冶炼制得的高锰高铝无磁钢板的制造方法
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
CN110951956B (zh) * 2019-12-19 2021-07-27 中北大学 一种超高塑性twip钢的生产方法
DE102020204356A1 (de) 2020-04-03 2021-10-07 Thyssenkrupp Steel Europe Ag Gehärtetes Blechbauteil, hergestellt durch Warmumformen eines Stahlflachprodukts und Verfahren zu dessen Herstellung
US20230340650A1 (en) * 2020-10-02 2023-10-26 The University Of Hong Kong Strong and Ductile Medium Manganese Steel and Method of Making
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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