EP3781717B1 - Tõle en acier laminé à froid et son utilisation, et méthode de production d'un tel produit en acier plat - Google Patents

Tõle en acier laminé à froid et son utilisation, et méthode de production d'un tel produit en acier plat Download PDF

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Publication number
EP3781717B1
EP3781717B1 EP18729562.1A EP18729562A EP3781717B1 EP 3781717 B1 EP3781717 B1 EP 3781717B1 EP 18729562 A EP18729562 A EP 18729562A EP 3781717 B1 EP3781717 B1 EP 3781717B1
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Prior art keywords
flat steel
steel product
cold
content
rolled
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EP18729562.1A
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German (de)
English (en)
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EP3781717A1 (fr
Inventor
Jonas Karl Moritz SCHWABE
Harald Hofmann
Matthias Schirmer
Evgeny BALICHEV
Annette BÄUMER
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ThyssenKrupp Steel Europe AG
ThyssenKrupp AG
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ThyssenKrupp Steel Europe AG
ThyssenKrupp AG
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
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    • 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
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    • 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
    • C21D8/0273—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • 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
    • C21D8/0426—Hot rolling
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • 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
    • C21D8/0436—Cold rolling
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    • 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
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    • 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
    • C21D8/0473—Final recrystallisation annealing
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    • 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
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • 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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
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    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
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    • C23C2/06—Zinc or cadmium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/12—Aluminium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
    • C23C2/36—Elongated material
    • C23C2/40—Plates; 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
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    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium

Definitions

  • the invention relates to a cold-rolled flat steel product which has an optimal combination of its mechanical properties for forming into components, in particular vehicle components and the like.
  • the invention further relates to a method for producing such a cold-rolled flat steel product.
  • the invention also names particularly suitable uses for such flat steel products.
  • contents of a steel or a flat steel product are mentioned in this text, these contents always refer to the weight (in% by weight), unless expressly stated otherwise. If information on the composition of atmospheres or gas mixtures is given in this text, the content information given for the individual components always refers to the volume (in% by volume), unless expressly stated otherwise. If information is given in this text about the content of individual components in the structure of a flat steel product, these always refer to the proportion in area % determined on the microstructure in accordance with DIN EN 13925 (2003.07) (specification in area %), unless expressly stated otherwise is.
  • flat steel product refers to steel strips or steel sheets produced in a rolling process and those obtained from them Blanks, boards and comparable products are understood, the thickness of which is significantly smaller than their width and length.
  • n-value we mean the n-value determined as “n 10-20 ” in tensile tests according to DIN 10275.
  • the tensile test itself is carried out in accordance with DIN EN ISO 6892-1 (sample form 1).
  • a cold-rolled steel sheet which, after annealing, should have TRIP properties and a tensile strength of at least 1000 MPa, in particular at least 1180 MPa, with a total elongation of at least 15%, in particular at least 20%.
  • the steel sheet consists of (in wt.%) C: 0.1 - 0.3%; Mn: 4 - 10%, Al: 0.05 - 5%, Si: 0.05 - 5%; and Nb: 0.008 - 0.1, the balance iron and unavoidable impurities, with Mn contents of 4 - 7%, in particular 6 - 7%, Si contents of 0.1 - 1.1 and Al contents of 0.5 - 1.6% are particularly preferred.
  • the microstructure of the cold-rolled sheet consists of at least 20% retained austenite and more than 50% lath-type ferrite. At the same time, the retained austenite and ferrite have an ultra-fine grain size of less than 5 ⁇ m.
  • an appropriately composed melt melted by vacuum induction melting was cast into slabs on a laboratory scale, which were then pre-rolled into 20 mm thick plates. The plates were held at a temperature of 1230 ° C for 3 hours to effect homogenization and were then hot rolled in three steps into plates with a thickness of 4 mm.
  • the hot-rolled plates leaving the finishing hot rolling mill at a final temperature of 900 °C were then accelerated to cool down to a coiling temperature of 750 °C, at which they were then held for one hour.
  • the plates were then kept at room temperature in the oven. In this way, the processes that occur when a hot strip produced in a corresponding manner is wound into a reel and cools to room temperature in the reel should be simulated.
  • the hot-rolled plates were cold-rolled with a thickness reduction of 40 - 50%.
  • the cold-rolled plates finally passed through a continuous annealing device in which an annealing cycle was simulated in which the plates were heated at a heating rate of 10 ° C / s to 650 - 750 ° C, in particular 680 - 740 ° C, and for 180 seconds Temperature have been maintained in order to then be cooled to room temperature at a cooling rate of 10 ° C / s.
  • a steel sheet with high specific strength and excellent ductility which contains 0.15 to 0.5% by weight of carbon (C), 6.0 to 8.0% by weight of manganese (Mn), 5.0 to 6, 0% by weight aluminum (Al), 0.05 to 0.5% by weight silicon (Si), less than 0.02% by weight (except 0) sulfur (S), the balance being iron (Fe) and unavoidable impurities.
  • the steel can contain 0.005 - 1.0% by weight of Ti, V, Nb or Zr.
  • the yield strength of the steel is greater or equal to 550 MPa.
  • the tensile strength multiplied by the elongation is greater than or equal to 28,000 MPa%.
  • a process for producing manganese steel with a high aluminum content is known.
  • a flat steel product is made from a steel with (in mass%) 0.10 to 0.35% C, 5.0 to 9.0% Mn, 4.0 to 7.5% Al, less than 0.003% P, less than 0.002% S, the rest Fe and unavoidable impurities, cast into a starting material, which is then heated to 1200 ° C over 1.5 hours and then in several stages starting from an initial temperature of 1050 - 1100 ° C and with a Final temperature of 850 - 900 °C is hot rolled.
  • the degree of deformation achieved during hot rolling is 80 to 85%.
  • the hot strip obtained in this way is wound into a coil at a coiling temperature of 600 - 700 °C and then cold rolled with a cold rolling ratio of 65 to 70%. Finally, a final annealing is carried out at 860 - 930 °C for a period of 0.5 hours, which is followed by quenching with water.
  • the cold-rolled steel sheet produced in this way should have high strength and ductility with a high aluminum content.
  • the invention has solved this problem in that such a flat steel product is designed according to claim 1.
  • Flat steel products according to the invention are particularly suitable for the production of vehicle components, in particular for chassis or body parts of motor vehicles, such as cars or trucks. These parts include, for example, steering components, wheel rims, vehicle chassis components and the like.
  • flat steel products according to the invention can also be used particularly well for the production of devices that are intended to offer ballistic protection. Due to their good formability, flat steel products according to the invention are also particularly suitable for internal or external high-pressure forming processes.
  • flat steel products according to the invention can also be used to produce components for internal combustion engines, such as camshafts, piston rods and the like.
  • flat steel products according to the invention can be used successfully in the field of container construction or other applications in which large-volume bodies with complex shapes have to be produced.
  • the flat steel product according to the invention has a composition and a structural state that give it properties optimized for the respective intended use.
  • the invention provides a carbon ("C") content of 0.08 - 0.25% by weight in order to ensure a sufficient amount of austenite in the structure of the flat steel product.
  • the C content is limited to 0.25% by weight in order to avoid the tendency to form brittle kappa carbides at the grain boundaries. Such carbides would impair the hot and cold formability of the flat steel products according to the invention.
  • the carbon has a strengthening effect through the formation of mixed crystals and increases the stacking fault energy, which in turn contributes to increasing the strength. In addition to the negative effects on formability, higher C contents would impair weldability.
  • the upper limit of the C content is limited to 0.25% by weight, with C contents of at most 0.22% by weight, in particular at most 0.19% by weight or very particularly preferably at most 0.17% by weight have proven to be particularly favorable in terms of avoiding negative effects of the C content.
  • the positive effects of the presence of C in the flat steel product according to the invention can be exploited by ensuring that the C content is at least 0.08% by weight, whereby: Contained at least 0.11% by weight of C, in particular at least 0.13% by weight of C, the advantageous effects are particularly reliably adjusted.
  • Aluminum is present in the flat steel product according to the invention in amounts of 3 - 5.4% by weight in order, on the one hand, to reduce the density and thus the weight of the flat steel product and, on the other hand, to increase the tensile strength through solid solution hardening. Al also contributes to the formation of the ferrite content in the structure of the flat steel product according to the invention. These favorable effects occur with Al contents of at least 3% by weight, with levels of at least 4% by weight being particularly favorable in this regard. However, in order to avoid negative influences, the Al content of a flat steel product according to the invention is limited to a maximum of 5.4% by weight. Al contents above this limit would lead to a deterioration in cold formability due to the formation of intermetallic phases. Al contents of at most 5.1% by weight have proven to be particularly suitable for achieving good cold formability. In addition, Al, when present in higher levels, forms embrittling particles with nitrogen and carbon, reduces thermal conductivity and lowers the Young's modulus.
  • Manganese is present in the flat steel product according to the invention in levels of 9 - 14% by weight. Mn contributes to the formation of a sufficient amount of austenite in the structure of the flat steel product and its stability. At the same time, the presence of Mn in the amounts prescribed according to the invention improves the hot formability, weldability and strength of the flat steel product. Mn has a deoxidizing effect during the production of the steel from which the flat steel product according to the invention is made. Excessively high Mn contents are avoided in order not to impair the corrosion resistance of the flat steel product.
  • Mn contents that are too high lead to too high a stability of the austenite, so that the TRIP effect is prevented or limited, which has a negative effect on the formability of the flat steel product.
  • the positive influences of Mn can be used particularly safely in a flat steel product according to the invention at levels of at least 9% by weight.
  • Negatives Influences of the presence of Mn while at the same time optimizing the cost-benefit ratio can be avoided by limiting the Mn content to a maximum of 12% by weight, in particular a maximum of 11.0% by weight.
  • Mn contents of at most 10.7% by weight have proven to be particularly favorable for achieving good formability.
  • B Boron
  • B can optionally be present in the flat steel product according to the invention in order to support the development of a fine structure.
  • B Boron
  • up to 0.1% by weight of B can be provided. This results in a positive contribution of B to the properties of a flat steel product according to the invention even at levels of 0.005% by weight.
  • the positive influence of B can be used particularly effectively with B contents of less than 0.02% by weight.
  • Chromium can optionally be added to the flat steel product according to the invention in amounts of up to 2% by weight in order to improve the corrosion and oxidation resistance. At levels above 2% by weight, Cr carbides can form, which can impair the deformability of the flat steel product.
  • the positive influence of Cr can be used particularly effectively with Cr contents of less than 0.8% by weight.
  • the positive effects of Cr can be used particularly safely in the flat steel product according to the invention if the Cr content is at least 0.05% by weight, in particular at least 0.10% by weight.
  • Si silicon
  • Si silicon
  • Al silicon
  • Si like Al
  • Si reduces the density of the material and contributes to deoxidation.
  • too high Si contents can worsen the ductility and reduce the weldability of the flat steel product according to the invention.
  • These negative influences can be reliably avoided by limiting the Si content to a maximum of 0.3% by weight in a flat steel product according to the invention.
  • the effects of Si in the flat steel product according to the invention already occur when the Si content is at least 0.05% by weight, in particular at least 0.1% by weight.
  • Phosphorus is generally undesirable in the flat steel product of the invention because it causes segregation and impairs cold workability, weldability and oxidation resistance. Therefore, the P content is limited to at most 0.1% by weight, in particular at most 0.05% by weight.
  • S Sulfur
  • S is also an undesirable accompanying element in the flat steel product according to the invention, since if the content is too high, it reduces the hot formability during hot rolling and worsens the corrosion resistance.
  • Tantalum (“Ta”) and tungsten (“W”) can be added to the flat steel product according to the invention to increase strength by forming carbide in amounts of up to 0.5% by weight.
  • An optimal cost-benefit ratio results from contents of up to 0.1% by weight.
  • Nickel optionally present in amounts of up to 2% by weight increases the amount and stability of the austenite present in the structure of a flat steel product according to the invention. At the same time, Ni contributes to the strength and toughness of the flat steel product. Ni also increases corrosion resistance. These advantageous effects can be used in particular when the Ni content of a flat steel product according to the invention is at least 0.05% by weight. The positive influence of Ni can be used particularly effectively with Ni contents of less than 1.0% by weight.
  • Cu copper
  • amounts of up to 2% by weight improves the corrosion resistance of the flat steel product.
  • higher Cu contents worsen hot formability and weldability.
  • the positive influence of Cu can be used particularly effectively with Cu contents of less than 0.1% by weight.
  • Ca can optionally be added to the flat steel product in amounts of up to 0.15% by weight to bind harmful S contents.
  • Ca proves to be particularly effective in concentrations of up to 0.05% by weight, which are therefore preferred if Ca is present at all. Harmful effects of Ca can be reliably avoided by limiting the Ca content to less than 0.01% by weight.
  • N Nitrogen
  • the N content of the flat steel product is limited to a maximum of 0.02% by weight, in particular 0.01% by weight, with practical N contents in the range of 0.001 - 0.008% by weight.
  • Co Co
  • Co can optionally be added to the flat steel product according to the invention in amounts of up to 2% by weight in order to increase the amount and stability of the austenite present in the structure. At the same time, Co increases the recrystallization temperature. Optimal effects of the presence of Co occur when the Co content is limited to a maximum of 1% by weight, with Co contents of less than 0.01% by weight having proven to be sufficient in many cases.
  • Sb Antimony
  • the elements assigned to the groups “Ti, Nb, V, Mo” and “Zr, La, Ce, Y” are of particular importance. According to the invention, at least one element from at least one of these groups is present in the flat steel product according to the invention in order to support edge stability, i.e. the avoidance of the formation of cracks, during hot rolling through the formation of precipitates.
  • the elements from the group “Ti, Nb, V, Mo” can be present alone, i.e. without the presence of an element from the group “Zr, La, Ce, Y”, or in combination with at least one of the elements Group "Zr, La, Ce, Y".
  • the elements of the group "Zr, La, Ce, Y" can be present alone, i.e. without the presence of an element of the group “Ti, Nb, V, Mo", or in combination with at least one of the elements of the group "Ti, Nb, V, Mo".
  • the content of this one element is 0.05 - 1% by weight. If, on the other hand, two or more elements from the group “Ti, Nb, V, Mo” are present, the sum of the contents is also 0.05 - 1% by weight.
  • Particularly favorable influences of the elements of the group “Ti, Nb, V, Mo” arise when their content is individual in the case that only one element of this group is present or in the case that two or more elements of this group are present , in total is at least 0.08% by weight.
  • An optimal cost-benefit ratio can be obtained if, in the case of only one element of this group being present, individually or in the case of two or more elements of this group being present, in the sum of the contents of the elements of the group present in each case at most 0.5% by weight, in particular at most 0.35% by weight.
  • An optimal cost-benefit ratio can be obtained if, in the case where only one element of this group is present, individually or in the case where two or more elements of this group are present, in total, the content of the elements of the group present in each case at most 0.2% by weight, in particular at most 0.15% by weight.
  • Ti In addition to improving edge stability, titanium (“Ti”) increases strength through the formation of Ti carbides and improves the r-value. This has a positive effect on the edge stability and strength of Ti, especially if Nb is also present at the same time. The simultaneous presence of Ti and Nb is therefore preferred.
  • Ti also improves the low-temperature toughness and high-temperature strength of the material.
  • excessive Ti contents should be avoided in order to avoid negative influences on deformability and welding properties.
  • the advantageous effect of Ti can be used in particular when the Ti content is at least 0.06% by weight.
  • Nb niobium
  • edge stability which results in particular when Ti and Nb are present at the same time
  • Nb carbides causes an increase in strength through the formation of Nb carbides and improves the r-value, which also has this effect occurs particularly safely when Ti is present at the same time.
  • the addition of Nb also improves the low-temperature toughness and high-temperature strength of the material.
  • excessive Nb contents should be avoided in order to avoid negative influences on deformability and welding properties.
  • the advantageous effect of Nb can be used in particular when the Nb content is at least 0.03% by weight.
  • V Vanadium
  • the positive influences of V can be used particularly safely at levels of at least 0.03% by weight.
  • Mo Molybdenum
  • Ce cerium
  • La lanthanum
  • Zr zirconium
  • Y yttrium
  • Ce, La, Zr and Y compensate for the negative influences that high Al contents can have on these properties of the flat steel product.
  • the effects of Ce, La, Zr and Y are the same, so that these elements can be exchanged for each other.
  • the aluminum equivalent Al eq formed from the respective Al and Si content must be in the range of 3 - 8% by weight ensures that the contents of the similarly acting alloy elements Al and Si are limited to such an extent that the formation of extremely brittle intermetallic precipitates is prevented.
  • the range specified for Al eq can be limited according to the invention to a maximum of 7.6% by weight, in particular a maximum of 7% by weight or a maximum of 6.5% by weight.
  • the minimum value for Al eq can be set to 4.8% by weight be raised in order to safely utilize the positive effects of the simultaneous presence of AI and Si.
  • the ratio %Mn/%Al of the contents of Mn ("%Mn”) and Al (“%Al”) should be more than 1.2% by weight, so that there is a sufficient amount of austenite despite the high Al content achieved in the structure of the flat steel product.
  • the alloy engineering measures explained above and the procedural measures explained below ensure that the austenite content in the structure of the flat steel product according to the invention is 10 - 60% by area. With such austenite contents, the steel of a flat steel product according to the invention has TRIP properties and the flat steel product has a high n value of at least 0.21.
  • the rest of the structure of the flat steel product according to the invention that is not occupied by austenite consists of ferrite as a result of the high Al content.
  • a flat steel product according to the invention has an n-value of at least 0.21, with flat steel products according to the invention regularly achieving n-values of at least 0.25, in particular at least 0.26.
  • High n-values represent a high formability associated with a high elongation at break A50 and therefore allow the formation of complex components. However, too high n-values should be avoided as this would result in high deformation forces required.
  • Flat steel products have n values that are regularly not higher than 0.5, in particular not higher than 0.4.
  • the austenite grain size in the structure of a flat steel product according to the invention is on average 0.85 - 3 ⁇ m. Grains that are too small would inhibit the TRIP effect. The desired n value would not be achieved. However, grains that are too large would lead to a large decrease in yield strength and tensile strength. Optimally, the average grain size of the austenite is at least 0.9 ⁇ m. It has also proven to be advantageous if the maximum size of the austenite grains in the structure of a flat steel product according to the invention is limited to 1.5 ⁇ m.
  • a high degree of recrystallization in the ferrite grains is sought so that they can support the deformation of the austenite grains.
  • This degree of recrystallization can be quantified using the so-called “ Kernal Average Misorientation ” (“KAM”).
  • KAM Kernal Average Misorientation
  • a low KAM in the ferrite ultimately means a high deformability of the ferrite. Since the structure of a flat steel product according to the invention consists of austenite and ferrite ("duplex structure"), a low KAM of the ferrite can compensate for a low austenite grain size.
  • the preliminary product which is typically a slab, a thin slab or It is a cast strip and needs to be heated through. Incomplete, inhomogeneous heating would result in the risk of cracks forming in the subsequent hot rolling process.
  • the preheating temperatures suitable for thorough heating are 1100 - 1300 °C, although in practice preheating temperatures of at least 1150 °C have proven to be particularly reliable. By limiting the preheating temperature to a maximum of 1250 °C, negative effects of preheating, such as an excessively doughy consistency of the preliminary product and an associated tendency to stick during hot rolling, can be counteracted.
  • the hot rolling of the preliminary product into a hot strip can be carried out in a conventional manner on a hot rolling train that is available for this purpose in practice.
  • the only important thing is that the hot strip still has a final hot rolling temperature of 850 - 1050 °C at the end of hot rolling.
  • Hot rolling end temperatures below 850 °C would require such high hot rolling forces that the desired degrees of forming cannot be achieved on conventional hot rolling stands.
  • Optimal hot rolling end temperatures are therefore in the range of 900 - 1050 °C.
  • the hot strips obtained are, if necessary, cooled in a conventional manner to the coiling temperature of 400 - 900 ° C specified according to the invention, with which they are then coiled into a coil.
  • the minimum coiling temperature of 400 ° C is due to the poor thermal conductivity of the steel of a flat steel product according to the invention necessary because otherwise high temperature gradients in the flat steel product would lead to tensions and the resulting poor flatness of the hot strip. Cooling too quickly in the cooling section could interrupt the recrystallization processes that begin at the end of hot rolling.
  • the hot strip wound into a coil can be cooled using a coil shower in order to shorten the cooling time and have a positive effect on scale formation.
  • the hot strip can optionally undergo an annealing treatment after cooling in the coil, in which it is at a temperature of 700 - 1000 ° C, in particular, for a period of time sufficient for complete recrystallization 700 - 900 °C.
  • the hot strip annealing is preferably carried out as a hood annealing, in which case the annealing time typically lasts 0.5 - 60 hours.
  • the hot strip can be subjected to a pickling treatment before cold rolling.
  • the scale formation on the hot strip surface caused by oxygen-affinous elements during the manufacturing process can be reduced by extending the residence time of the hot strip in the pickling medium.
  • Hot strip pickling can be carried out using different pickling media such as hydrochloric acid.
  • the cold rolling of the hot-rolled strip into a cold-rolled strip takes place with a total degree of deformation of 25 - 90%, in particular at least 40% or at least 50%.
  • the minimum degree of deformation provided according to the invention is necessary in order to initiate the recrystallization, in particular of the ferrite contained in the structure of the flat steel product, during the final annealing.
  • too high a degree of deformation should be avoided, as this would result in too large a degree of deformation Work hardening and the associated risk of belt breaks would result.
  • the mechanical properties of the flat steel product according to the invention are decisively influenced by the final annealing.
  • the final annealing can be carried out in a continuous process through a conventional continuous furnace or as a hood annealing in batch operation.
  • the cold-rolled flat steel product is heated to a final annealing temperature that is at least 950 ° C and at a rate that is typically 1 - 100 K/s, in particular 10 - 80 K/s or 20 - 50 Kls is heated to a maximum of 1070 °C. Heating up too quickly can have an unfavorable effect on the homogeneity of the heating and thus on the homogeneous distribution of properties of the flat steel product.
  • the final annealing temperature is selected so that the necessary austenite grain size is achieved, which is a prerequisite for the TRIP properties and the n value of the flat steel product according to the invention.
  • the necessary austenite grain size can be set particularly reliably if the final annealing temperature is at least 970 °C.
  • Optimally practical final annealing temperatures are in the range of 1000 - 1070 °C.
  • the holding times at the final annealing temperature in the continuous annealing furnace are, depending on the level of the final annealing temperature, not more than 10 minutes, in particular not more than 5 minutes or 3 minutes, with higher continuous final annealing temperatures enabling shorter holding times and minimum holding times of at least 20 seconds each are practical.
  • the cold-rolled strip placed in the coil under the hood is heated to the final annealing temperature at a heating rate of 0.001 - 0.5 Kls, in particular 0.002 - 0.5 Kls or 0.008 - 0.5 Kls heated, which is in each case more than 800 ° C, in particular more than 850 ° C.
  • a final annealing temperature of 950 °C should not be exceeded in order to avoid excessive grain growth.
  • the annealing times after reaching the final annealing temperature are in the range of 0.5 - 60 hours, in particular 1 - 30 hours. In this way, flat steel products according to the invention with an n value of at least 0.21 and austenite grain sizes of 0.85 - 3 ⁇ m can be produced particularly reliably.
  • the flat steel product according to the invention can be provided with a protective coating.
  • a protective coating This can, for example, be applied in a conventional manner using coating systems available in practice as a zinc or aluminum-based coating.
  • the analysis data for the individual elements refer to the determined contents in% by weight. If "-" is entered in the respective table field, this means that the content of the respective element was below the respective detection limit and the element in question was therefore ineffective with regard to the properties.
  • the detection limits for P and Ti are 0.005 each % by weight, for Cr, Co, S and Ca each at 0.001% by weight, for V, Mo and Ni each at 0.01% by weight, for Cu and Nb each at 0.02% by weight , for B at 0.0004% by weight and for Ce, La, Y, Zr, As and Sn each at 0.002% by weight.
  • Elements that were present in such low levels are to be classified as unavoidable impurities, just like the elements not listed. These include, for example, contents of As, Sn, Mg and H.
  • the sum of the microalloying elements Ti, Nb, V, Mo, the sum of the rare earth metals Ce, La, Y, Zr, the ratio of Mn to Al and the Al Equivalent of the individual melts are given in Table 2.
  • melts A and B are not according to the invention since they meet the requirements of the invention for the presence of at least one element from the groups "Ti, Nb, V, Mo” and "Zr, La, Ce, Y" cannot be fulfilled.
  • melts A - H were cast in a conventional manner into blocks, which were then heated through at a preheating temperature VWT for a period of VWD.
  • the blocks were rolled into slabs in an equally conventional manner in a conventional hot rolling stand.
  • the slabs were rolled in a hot rolling mill into hot strip with a thickness of 2.5 - 3.0 mm.
  • the hot rolling was each ended with a hot rolling final temperature WET.
  • the resulting hot strips were cooled in air to a coiling temperature HT, at which they were coiled into a coil.
  • hot strip annealing Some of the hot strips were then subjected to hot strip annealing, which was carried out as a hood annealing with an annealing temperature of 850 ° C and an annealing time of 6 hours.
  • the annealed hot strips like the non-annealed hot strips, were cold-rolled into cold-rolled steel strip in a conventional cold rolling facility with a total cold forming degree of KGW.
  • the cold-rolled steel strips obtained were final annealed in a continuous annealing furnace (“Conti”) or in batches in a hood annealing furnace (“hood”). They were each heated to the respective final annealing temperature Tsg at an average heating rate HR, at which they were each maintained for a period of time tsg.
  • preheating temperature VWT preheating time VWD
  • hot strip thickness WB hot rolling end temperature WET
  • coiling temperature HT the result of the assessment of the edge cracks on the respective hot strip.
  • the information as to whether hot strip annealing was carried out in the manner explained above, the total cold forming degree KGW, the type of final annealing, the heating rate HR of the final annealing, the final annealing temperature Tsg and the final annealing duration tsg are given in Table 3a and Table 3b.
  • the upper and lower yield strengths ReH and ReL, the yield strength Rp0.2, the tensile strength Rm, the elongation at break A50, the n-value n 10-20 are determined on the cold-rolled and finally annealed steel strips obtained , the r value r 10-20 , the austenite grain size KG, the KAM value determined with a step size of 100 nm and a deposition value of 5 °, and the quotient KG/KAM.
  • the yield strengths ReH and ReL, the yield strength Rp0.2, the tensile strength Rm and the elongation at break A50 were determined in accordance with DIN EN ISO 6892-1:2009 on the cold-rolled strip in the transverse direction.
  • the mean circle-equivalent grain diameter was determined using EBSD (Electron Back Scattering Diffraction).
  • EBSD Electro Back Scattering Diffraction
  • a tolerance angle of 5° was chosen with a minimum grain size of five contiguous neighboring measuring points with a step size of 0.15 ⁇ m.
  • the n 10-20 and the r 10-20 values as well as the KAM value were determined in the manner already explained above. Values that were not recorded are marked with “-” in Table 3.
  • Examples 10, 11, 15, 16, 20, 23 were final annealed in a continuous furnace with a final annealing temperature of 830 ° C, which was outside the temperature range of 950 - 1070 ° C specified according to the invention for a final annealing that takes place in a continuous process.
  • the flat steel products produced in Examples 10, 11, 15, 16, 20, 23 accordingly had very low n values, which are below the minimum value of 0.21 provided for in the invention.

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Claims (15)

  1. Produit plat en acier laminé à froid, lequel présente une valeur n d'au moins 0,21, mesurée comme décrit dans la description, et qui est produit à partir d'un acier qui est composé de (en % en poids) C : 0,08 à 0,25 %, Al : 3 à 5,4 %, Mn : 9 à 14 %, B : 0 à 0,1 %, Cr: 0 à 2 %, Si : 0 à 0,4 %, P : 0 à 0,1 %, S : 0 à 0,3 %, Ta : 0 à 0,5 %, W : 0 à 0,5 %, Ni : 0 à 2 %, Cu : 0 à 2 %, Ca : 0 à 0,15 %, N : 0 à 0,02 % Co : 0 à 2 %
    ainsi que d'un élément ou de plusieurs éléments du groupe « Ti, Nb, V, Mo », avec la condition que la somme des teneurs en ces éléments soit d'au moins 0,05 % et d'au plus 1 %, et/ou d'un élément ou de plusieurs éléments du groupe « Zr, La, Ce, Y », avec la condition que la somme des teneurs en ces éléments soit d'au moins 0,05 % et d'au plus 0,3 %, ainsi que le reste du fer et des impuretés inévitables,
    où, pour le rapport %Mn/%AI, il vaut % Mn / % Al > 1,2
    Figure imgb0008
    et pour Al eq = % Al + 0,4 × % Si 3 − 3 × % Si 2 + 8,3 × % Si
    Figure imgb0009
     il vaut 3 ≤ Al eq ≤ 8
    Figure imgb0010
    avec %Mn : teneur en Mn respective de l'acier
    %AI : teneur en Al respective de l'acier
    %Si : teneur en Si respective de l'acier
    la structure du produit plat en acier étant constituée de 10 à 60 % de la surface d'austénite et de 40 à 90 % de la surface de ferrite avec une taille moyenne des grains d'austénite de 0,85 à 3 µm.
  2. Produit plat en acier selon la revendication 1, caractérisé en ce que pour le quotient KG/(KAM 1 5°) de la taille moyenne de grains KG de l'austénite et de la valeur KAM 1 5° déterminée à la ferrite il vaut KG/(KAM 1 5°) > 2,7 µm/°.
  3. Produit plat en acier selon l'une des revendications précédentes,
    caractérisé en ce que sa valeur n est d'au moins 0,25.
  4. Produit plat en acier selon l'une des revendications précédentes,
    caractérisé en ce que la taille moyenne de grains de l'austénite est de 0,9 à 1,5 µm.
  5. Produit plat en acier selon l'une des revendications précédentes,
    caractérisé en ce que sa teneur en Al est de 4 à 5,4 % en poids.
  6. Produit plat en acier selon l'une des revendications précédentes,
    caractérisé en ce que sa teneur en C est de 0,11 à 0,19 % en poids.
  7. Produit plat en acier selon l'une des revendications précédentes,
    caractérisé en ce que sa teneur en Mn est de 9 à 12 % en poids.
  8. Produit plat en acier selon l'une des revendications précédentes,
    caractérisé en ce que sa teneur en Si est d'au moins 0,01 % en poids.
  9. Produit plat en acier selon l'une des revendications précédentes,
    caractérisé en ce que pour Aleq il vaut Aleq ≤ 7.
  10. Produit plat en acier selon l'une des revendications précédentes,
    caractérisé en ce que sa résistance à la traction Rm est d'au plus 1050 MPa, en particulier d'au plus 950 MPa.
  11. Utilisation d'un produit plat en acier laminé à froid constitué selon l'une des revendications précédentes pour la fabrication de pièces de véhicule.
  12. Procédé pour la production d'un produit plat en acier laminé à froid constitué selon l'une des revendications 1 à 10, comprenant les étapes de travail suivantes :
    a) fusion d'une masse d'acier fondu qui est composée de (en % en poids) C : 0,08 à 0,25 %, Al : 3 à 5,4 %, Mn : 9 à 14 %, B : 0 à 0,1 %, Cr : 0 à 2 %, Si : 0 à 0,4 %, P : 0 à 0,1 %, S : 0 à 0,3 %, Ta : 0 à 0,5 %, W: 0 à 0,5 %, Ni : 0 à 2 %, Cu : 0 à 2 %, Ca : 0 à 0,15 %, N : 0 à 0,02 %, Co : 0 à 2 % ainsi que d'un élément ou de plusieurs éléments du groupe « Ti, Nb, V, Mo », avec la condition que la somme des teneurs en ces éléments soit d'au moins 0,05 % et d'au plus 1 %, ou d'un élément ou de plusieurs éléments du groupe « Zr, La, Ce, Y », avec la condition que la somme des teneurs en ces éléments soit d'au moins 0,05 % et d'au plus 0,3 %, ainsi que le reste du fer et des impuretés inévitables, où, pour le rapport %Mn/%AI, il vaut %Mn/%AI > 1,2 et pour Aleq = %AI + 0,4 × (%Si)3 - 3 × (%Si)2 + 8,3 × %Si il vaut 3 ≤ Aleq ≤ 8 avec %Mn : teneur en Mn respective de l'acier, %AI : teneur en Al respective de l'acier, %Si : teneur en Si respective de l'acier ;
    b) coulage de l'acier fondu en un produit préalable, tel qu'un lingot, une brame, une brame mince ou une bande coulée ;
    c) maintien au chauffage du produit préalable à une température de préchauffage de 1100 à 1350 °C ;
    d) laminage à chaud du produit préalable en une bande chaude ayant une température finale de laminage à chaud de 850 à 1050 °C ;
    e) refroidissement de la bande chaude à une température de bobinage de 400 à 900 °C ;
    f) bobinage de la bande chaude refroidie à la température de bobinage en une bobine ;
    g) facultatif : recuit de la bande chaude à une température de recuit de la bande chaude de 700 à 1000 °C ;
    h) facultatif : décapage de la bande chaude ;
    i) laminage à froid de la bande chaude en une bande en acier laminée à froid ayant un taux de déformation total de 25 à 90 % ;
    j) recuit final de la bande en acier laminée à froid, le recuit final étant
    - soit effectué en tant que recuit continu au cours d'un passage continu à travers un four de recuit continu, dans lequel la bande en acier laminée à froid est maintenue pendant une durée d'au moins 20 sec et inférieure à 10 min à une température de recuit final d'au moins 950 °C et d'au plus 1070 °C, la vitesse de chauffage à laquelle le produit plat en acier laminé à froid est chauffé à la température de recuit final étant de 1 à 100 K/s,
    - soit exécuté en tant que recuit sous cloche pendant une durée de 0,5 à 60 h à une température de recuit final qui est supérieure à 800 °C et peut aller jusqu'à 950 °C, la vitesse de chauffage à laquelle le produit plat en acier laminé à froid est chauffé à la température de recuit final étant de 0,001 à 0,5 K/s.
  13. Procédé selon la revendication 12, caractérisé en ce que la température finale de laminage à chaud est d'au moins 900 °C.
  14. Procédé selon l'une des revendications 12 à 13, caractérisé en ce que la température de recuit final est, dans le cas où le recuit final est exécuté en tant que recuit continu, d'au moins 1000 °C, ou, dans le cas où le recuit final est exécuté en tant que recuit sous cloche, supérieure à 850 °C.
  15. Procédé selon l'une des revendications 12 à 14, caractérisé en ce que la température de bobinage est de 600 à 850 °C.
EP18729562.1A 2018-03-26 2018-03-26 Tõle en acier laminé à froid et son utilisation, et méthode de production d'un tel produit en acier plat Active EP3781717B1 (fr)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
PCT/EP2018/057631 WO2019185108A1 (fr) 2018-03-26 2018-03-26 Produit en acier plat laminé à froid ainsi qu'utilisation et procédé pour la fabrication d'un tel produit en acier plat

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EP3781717B1 true EP3781717B1 (fr) 2024-03-06

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Family Cites Families (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR101481069B1 (ko) * 2012-12-27 2015-01-13 한국기계연구원 연성이 우수한 고비강도 강판 및 이의 제조방법
WO2015001367A1 (fr) * 2013-07-04 2015-01-08 Arcelormittal Investigación Y Desarrollo Sl Feuille d'acier laminée à froid, procédé de fabrication et véhicule
CN104694816A (zh) * 2015-03-13 2015-06-10 北京科技大学 强塑积大于30GPa·%的高Al中锰钢的制备方法
CN104928568B (zh) * 2015-06-30 2017-07-28 宝山钢铁股份有限公司 一种铁素体低密度高强钢及其制造方法

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