EP2767601B1 - Produit plat en acier laminé à froid pour applications d'emboutissage profond et son procédé de fabrication - Google Patents

Produit plat en acier laminé à froid pour applications d'emboutissage profond et son procédé de fabrication Download PDF

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Publication number
EP2767601B1
EP2767601B1 EP13155225.9A EP13155225A EP2767601B1 EP 2767601 B1 EP2767601 B1 EP 2767601B1 EP 13155225 A EP13155225 A EP 13155225A EP 2767601 B1 EP2767601 B1 EP 2767601B1
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Prior art keywords
flat steel
steel product
cold
annealing
weight
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German (de)
English (en)
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EP2767601A1 (fr
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Evgeny BALICHEV
Harald Hofmann
Jose Jimenez
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ThyssenKrupp Steel Europe AG
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ThyssenKrupp Steel Europe AG
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Priority to EP13155225.9A priority Critical patent/EP2767601B1/fr
Application filed by ThyssenKrupp Steel Europe AG filed Critical ThyssenKrupp Steel Europe AG
Priority to BR112015019413A priority patent/BR112015019413A2/pt
Priority to US14/767,741 priority patent/US10513762B2/en
Priority to CN201480021223.4A priority patent/CN105121673A/zh
Priority to CN201910355506.7A priority patent/CN110295317A/zh
Priority to PCT/EP2014/052810 priority patent/WO2014125016A1/fr
Priority to JP2015557422A priority patent/JP6383368B2/ja
Priority to KR1020157024979A priority patent/KR102193066B1/ko
Publication of EP2767601A1 publication Critical patent/EP2767601A1/fr
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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
    • 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
    • C21D8/0405—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 of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • 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
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • 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
    • 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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations
    • 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
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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

Definitions

  • the invention relates to a cold-rolled steel flat product for thermoforming applications, which has a reduced weight as a result of a density reduction with optimized mechanical properties and an optimized deformability. Likewise, the invention relates to a method for producing such a flat steel product.
  • Al-containing deep-drawing steels may contain a maximum of 6.5% by weight of Al (cf. U. Brüx "Thermoformable iron-aluminum lightweight steels", construction April 4, 2002 ).
  • EP 0 826 787 A2 is a high strength lightweight steel known, consisting of (in wt .-%)> 5 to 9, preferably 7 - 9% Al, ⁇ 0.2% Si, 0.03 - 0.2% Mn and the balance of Fe and unavoidable impurities, wherein optionally in total up to 1% of Cu, Mo, W, Co, Cr and Ni, and in total up to 0.1% of Sc, Y and rare earths may be present in the steel.
  • the steel may additionally contain up to 0.1% C, in total up to 0.5% of Ti, Zr, Hf, V, Nb, and Ta, up to 0.01% B and up to 0.1% P included.
  • that goes EP 0 826 787 A2 not on the effects that can be achieved by the presence of each optionally added alloying elements.
  • the object of the invention was to provide a flat steel product which, with a significant weight reduction, has optimized deformation suitability and likewise optimized mechanical properties.
  • this object is achieved with regard to the cold-rolled flat steel product by providing a product having the features specified in claim 1.
  • a cold-rolled flat steel product according to the invention for deep-drawing applications consists of a steel which, in addition to iron and unavoidable impurities (in% by weight) C: 0.008-0.1%, Al: 6.5-12%, Nb: 0.1-0, 2%, Ti: 0.15-0.5%, P: up to 0.1%, S: up to 0.03%, N: to to 0.1% and optionally one or more elements from the group "Mn, Si, rare earth metals, Mo, Cr, Zr, V, W, Co, Ni, B, Cu, Ca, N" with the proviso contains, Mn: up to 1%, rare earth metals: up to 0.2%, Si: up to 2%, Zr: up to 1%, V: up to 1%, W: up to 1%, Mo: up to 1%, Cr : up to 3%, Co: up to 1%, Ni: up to 2%, B: up to 0.1%, Cu: up to 3%, Ca: up to 0.015%.
  • the ratio% Ti 0.00
  • the cold-rolled steel strip according to the invention is distinguished by r values of at least 1.3, with flat steel products according to the invention regularly achieving r values of greater than 1.3.
  • the high r-value stands for a good deep drawability of the cold-rolled steel flat product according to the invention, since with increasing r-value the tendency to thinning during deep-drawing is reduced and consequently stronger deep-drawing degrees are made possible. Otherwise there would be a risk of component failure at the thinned area.
  • a cold-rolled steel flat product according to the invention not only has high r values, but also achieves an elongation A50 of regularly more than 18%. Steel flat products produced under optimum processing conditions have elongations A50 of 25% or more.
  • the ⁇ -carbide content of a flat steel product according to the invention is from 0% by volume (completely ⁇ -carbide-free state) to at most 0.1% by volume. Due to the minimized ⁇ -carbide content, the processability of the flat steel product according to the invention is reliably ensured.
  • a composite steel flat product according to the invention is further distinguished by the fact that the grains are globulitically pronounced in their microstructure.
  • the ratio of the grain length in the rolling direction to the grain width in the transverse direction of the band is generally less than 1.5, in particular less than 1.2. That is, the length of the grains is at most 50%, in particular at most 20%, greater than their width.
  • the steel according to the invention may contain a large number of further alloying elements in order to set certain properties.
  • the relevant elements are summarized in the group "Mn, Si, rare earth metal, Mo, Cr, Zr, V, W, Co, Ni, B, Cu, Ca, N".
  • Mn, Si, rare earth metal, Mo, Cr, Zr, V, W, Co, Ni, B, Cu, Ca, N can be present in the steel according to the invention or completely absent, wherein the respective element is considered to be "non-existent” even if it is present in the steel flat product according to the invention in an amount in which it is ineffective and is therefore attributable to the production-unavoidable impurities.
  • Aluminum is present in the steel of the present invention at levels of 6.5-12 wt%, with Al contents greater than 6.8 wt% being advantageous in view of the desired density reduction.
  • Typical Al contents of flat steel products according to the invention are in the range from 6.5 to 10% by weight, in particular from 6.8 to 9% by weight.
  • the presence of high Al contents reduces the density of the steel and significantly improves its corrosion and oxidation resistance.
  • Al increases the tensile strength at these levels.
  • excessive contents of Al can lead to a deterioration of the forming behavior, which is expressed in a decrease in the r value.
  • the Al content is limited to a maximum of 12 wt .-%.
  • An optimally balanced ratio of reduced density and processability arises when 6.5 to 10% by weight of Al, in particular at least 6.8% by weight of Al, are present in the steel according to the invention.
  • the C content is limited to at most 0.1% by weight in steel according to the invention, with C contents of 0.015-0.05% by weight, in particular 0.008-0.05% by weight, being particularly favorable.
  • C contents above 0.1 wt.% Can cause the formation of undesirable brittle kappa carbides ("K carbides") at the grain boundaries and consequent reduction in hot and cold workability.
  • K carbides undesirable brittle kappa carbides
  • ⁇ -carbides Fe-Al-C compounds
  • ⁇ -carbides are formed early in the processing of generic steels during hot processing at high temperatures on the grain boundaries and cause embrittlement of the material.
  • the lowest possible free C content is set, thus largely preventing the formation of ⁇ carbides.
  • 0.15-0.5% by weight of Ti and 0.1-0.2% by weight of Nb are present in the first place for this purpose.
  • the effect of titanium can then be used particularly reliably if the Ti content is 0.15-0.3% by weight.
  • niobium when Nb is present in amounts of 0.1-0.15% by weight in the steel according to the invention.
  • the respective contents of Ti and Nb must be adjusted in such a way that they fulfill the condition prescribed according to the invention for the ratio of these contents.
  • Ti and Nb contents which fulfill these requirements cause the formation of finely dispersed Ti and Nb carbides in the steel according to the invention, which promote the formation of a fine structure which supports the deformability of the flat steel product.
  • V, Zr and W are also effective carbide formers and, in amounts of up to 1% by weight each, can supplement the effect of the Nb and Ti required contents provided according to the invention.
  • the effect of V, Zr and W can be used particularly purposefully if their content is limited to in each case up to 0.5% by weight, in particular 0.3% by weight.
  • Mn By adding Mn in amounts of up to 1% by weight, in particular up to 0.5% by weight, the hot workability and weldability of the steel according to the invention can be improved.
  • Mn aids in deoxidation during melting and contributes to increasing the strength of the steel.
  • Mo can be present in amounts of up to 1% by weight in the steel according to the invention. Mo also forms carbides and contributes to increasing the tensile strength, creep resistance and fatigue strength of a flat steel product of the present invention.
  • the carbides formed by Mo with C are particularly fine and thus improve the fineness of the structure of the flat steel product according to the invention. High levels of Mo, however, degrade the hot and cold workability. In order to avoid this particularly reliably, the optionally present Mo content of a steel according to the invention can be limited to 0.5% by weight.
  • the S content to a maximum of 0.03 wt .-%, preferably at most 0.01 wt .-%, and the P content to a maximum of 0 , 1 wt .-%, preferably at most 0.05 wt .-%, limited.
  • the N content of the flat steel product according to the invention is limited to at most 0.1% by weight, in particular at most 0.02% by weight, preferably at most 0.001% by weight, in order to avoid the formation of relatively large amounts of Al nitrides. These would degrade the mechanical properties.
  • rare earth metals in amounts of up to 0.2% by weight contributes to improved resistance to oxidation and increased strength of a flat steel product of the present invention.
  • contents of rare earth metals are desulfurizing and deoxidizing.
  • the oxides formed by the respective lateral earth metal have a fine grain effect and promote positive texture selection for improved technological properties.
  • Particularly suitable rare earth metals are Ce and La.
  • the positive influences of rare earth metals in the steel according to the invention can be used particularly purposefully if the contents of rare earth metals are in the range of up to 0.05% by weight.
  • the carbides formed by the presence of one or more of the elements Ti, Nb, V, Zr, W, Mo contribute to increasing the strength of the steel of the present invention.
  • Si in amounts of up to 2 wt .-%, in particular up to 0.5 wt .-%, supported during the melting also the deoxidation and increases the strength and corrosion resistance of the steel according to the invention. At too high a content, however, the presence of Si reduces the ductility of the steel and its weldability.
  • Typical Si contents of steels according to the invention are in the range of 0.1-0.5% by weight, in particular 0.1-0.2% by weight.
  • Cu in amounts of up to 3% by weight improves corrosion resistance in the steel of the present invention, but at higher levels may also deteriorate hot workability and weldability. If present, therefore, the Cu content in a practical embodiment of the invention to at most 1 wt .-%, in particular 0.5 wt .-%, limited.
  • steels according to the invention can also be cast into blocks, which are then rolled out into slabs by pre-blocking.
  • the reheated slabs are hot rolled at a hot rolling end temperature WET to a hot strip and the resulting hot strip was wound at a reel temperature HT each to form a coil.
  • a cast strip was produced as a precursor via a two-roll strip caster, which was then also hot-rolled into a hot strip with a hot rolling end temperature WET.
  • the processing to the hot strip was carried out in a continuous process sequence without interruption following the strip casting, so that the precursor already had a temperature lying in the range of inventively predetermined preheating temperatures when entering the hot rolling device and the preheating could be omitted.
  • the hot strip produced from the steel E3 has been coiled after hot rolling at a reel temperature HT to form a coil.
  • the so annealed hot strips are in one or two stages with cold rolling degrees KWG1 (cold rolling degree of the first cold rolling stage) and KWG2 (cold rolling degree of the respective second cold rolling stage) each cold-rolled into a cold-rolled steel strip. If two-stage cold rolling has been carried out, an intermediate annealing at an intermediate annealing temperature ZGT has been carried out between the cold rolling stages. After cold rolling, the cold-rolled steel flat products have undergone a final annealing at an annealing temperature SGT. The intermediate annealing and the final annealing have each been completed in continuous operation.
  • the cold-rolled steel strips produced from the steels E1 and E2 produced according to the invention in accordance with the invention have yield strengths which are regularly greater than 300 MPa, in particular greater than 320 MPa and thereby reach values of 380 MPa and more, and tensile strengths which are regularly greater 460 MPa, in particular greater than 480 MPa, achieving values of 530 MPa and more, as well as elongation values A50 of at least 18%, which regularly reach more than 21%, in particular greater than 25%, and always have r values of 1.3 or greater.
  • Cold-rolled steel strips not assembled according to the invention do not achieve such r-values even if these steel strips have been produced taking into account production parameters that are closely related to the parameters set in the production of the cold-rolled steel flat products according to the invention. Also according to the invention composite, but not according to the invention processed flat steel products do not reach the properties of steel flat products produced according to the invention or can not even be cold-rolled.
  • the steel strips produced according to the invention have, despite their high Al contents, a superior deep-drawing capability, without the need for expensive alloying or process-engineering measures.
  • a flat steel product with optimum deformation properties (r ⁇ 2, n ⁇ 0.2, A50 ⁇ 30%) is achieved by a combination of alloy according to the invention, high degree of cold deformation and low hot rolling temperature (about 850 ° C).
  • the cold-rolled steel strips produced from the steels according to the invention in accordance with the invention contain, in addition to a Fe (Al) mixed-crystal matrix, locally occurring hardening precursor phase.
  • a Fe (Al) mixed-crystal matrix in common hot rolling parameters is in rolled full ferrite phase region and obtained hot strip with typical three-layer structure, which in turn is characterized by recrystallized globulitician edge areas and the only recovered core area with stem crystals.
  • the hot strip annealing performed according to the invention reduces the dislocation density in the recovered area and facilitates subsequent cold rolling processing. Without the hot strip annealing, the alpha fiber texture component is strong but weak with hot strip annealing.
  • a low maximum cold rolling degree of up to 50% results in weak gamma fiber texture components
  • one-stage cold rolling with a high cold rolling degree of at least 65%, especially at least 80%, or two-stage cold rolling with correspondingly high deformation in the last rolling stage results in one strong gamma fiber component.
  • These dependencies are more pronounced at lower hot rolling end temperatures, which are in the range of 830-960 ° C, especially 840-880 ° C.
  • the deformation behavior of the resulting cold-rolled steel flat product is significantly influenced by the texture.
  • High r and n values as well as a high elongation at break A50 are particularly noticeable when the gamma fast texture component dominates over the alpha fiber texture component.
  • the inventively predetermined hot strip annealing and the inventively provided parameters of cold rolling ensure that this goal is achieved.

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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 (14)

  1. Produit plat en acier laminé à froid pour applications d'emboutissage profond,
    - composé d'un acier qui, outre le fer et les inévitables impuretés, contient (en % en poids)
    C : 0,008 - 0,1 %,
    Al : 6,5 - 12 %,
    Nb : 0,1 - 0,2 %,
    Ti : 0,15 - 0,5 %,
    P : jusqu'à 0,1 %,
    S : jusqu'à 0,03 %,
    N : jusqu'à 0,1 %
    ainsi que, facultativement, un ou plusieurs éléments du groupe « Mn, Si, terres rares, Mo, Cr, Zr, V, W, Co, Ni, B, Cu, Ca, N » avec pour condition
    Mn : jusqu'à 1 %,
    terres rares : jusqu'à 0,2 %,
    Si : jusqu'à 2 %,
    Zr : jusqu'à 1 %,
    V : jusqu'à 1 %,
    W : jusqu'à 1 %,
    Mo : jusqu'à 1 %,
    Cr : jusqu'à 3 %,
    Co : jusqu'à 1 %,
    Ni : jusqu'à 2 %,
    B : jusqu'à 0,1 %,
    Cu : jusqu'à 3 %,
    Ca : jusqu'à 0,015 %,
    - la relation suivante s'appliquant pour le rapport %Ti/%Nb de la teneur en Ti %Ti par la teneur en Nb %Nb 2,5 ≥ % Ti / % Nb ≥ 1,5.
    Figure imgb0005
    - et la valeur r du produit plat en acier, en présence d'une texture du produit plat en acier qui est caractérisée par une faible occupation des fibres α de moins de 4 et une forte occupation des fibres y de plus de 4, étant au moins égale à 1,3.
  2. Produit plat en acier selon la revendication 1, caractérisé en ce que sa teneur en Al est de 6,5 à 10 % en poids.
  3. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Al est supérieure à 6,8 % en poids.
  4. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en C est inférieure ou égale à 0,05 % massique.
  5. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Nb est de 0,1 à 0,15 % massique.
  6. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que sa teneur en Ti est de 0,15 à 0,3 % massique.
  7. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que sa structure contient de 0 à 0,1 % volumique de carbures κ.
  8. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que dans sa structure, les grains possèdent un rapport < 1,5 des longueurs de grain dans le sens du laminage par la largeur de grain dans le sens transversal du produit plat en acier.
  9. Procédé de production d'un produit plat en acier laminé à froid conçu pour des applications d'emboutissage profond, comprenant les étapes suivantes
    - production d'un acier liquide qui, outre le fer et les inévitables impuretés, contient (en % en poids)
    C : 0,008 - 0,1 %,
    Al : 6,5 - 12 %,
    Nb : 0,1 - 0,2 %,
    Ti : 0,15 - 0,5 %,
    P : jusqu'à 0,1 %,
    S : jusqu'à 0,03 %,
    N : jusqu'à 0,1 %
    ainsi que, facultativement, un ou plusieurs éléments du groupe « Mn, Si, terres rares, Mo, Cr, Zr, V, W, Co, Ni, B, Cu, Ca, N » avec pour condition
    Mn : jusqu'à 1 %,
    terres rares : jusqu'à 0,2 %,
    Si : jusqu'à 2 %,
    Zr : jusqu'à 1 %,
    V : jusqu'à 1 %,
    W : jusqu'à 1 %,
    Mo : jusqu'à 1 %,
    Cr : jusqu'à 3 %,
    Co : jusqu'à 1 %,
    Ni : jusqu'à 2 %,
    B : jusqu'à 0,1 %,
    Cu : jusqu'à 3 %,
    Ca : jusqu'à 0,015 %,
    - la relation suivante s'appliquant pour le rapport %Ti/%Nb de la teneur en Ti %Ti par la teneur en Nb %Nb, 2,5 ≥ %Ti/%Nb ≥ 1,5 ;
    - coulée de l'acier liquide pour obtenir un produit primaire ;
    - facultativement, réchauffage à coeur ou maintien du produit primaire à une température de préchauffage de 1 000 à 1 300 °C ;
    - laminage à chaud du produit primaire en un feuillard à chaud, la température finale de laminage à chaud étant de 820 à 1 000 °C ;
    - bobinage du feuillard à chaud en une bobine, la température de bobinage se trouvant dans la plage de la température ambiante à 750 °C ;
    - recuit du feuillard à chaud à une température de recuit supérieure à 650 °C et maximale de 1 200 °C sur une durée de recuit de 1 à 50 h ;
    - facultativement, décapage du feuillard à chaud ;
    - laminage à froid du feuillard à chaud recuit et facultativement décapé pour obtenir un produit plat en acier laminé à froid en une ou plusieurs étapes avec un degré de laminage à froid total d'au moins 65 % ;
    - recuit final du produit plat en acier laminé à froid à une température de recuit finale de 650 à 850 °C, de sorte que la valeur r du produit plat en acier, en présence d'une texture du produit plat en acier qui est caractérisée par une faible occupation des fibres α de moins de 4 et une forte occupation des fibres γ de plus de 4, est au moins égale à 1,3.
  10. Procédé selon la revendication 9, caractérisé en ce que le produit primaire et un feuillard de coulée.
  11. Procédé selon la revendication 9 ou 10, caractérisé en ce que la température finale de laminage à chaud est de 830 à 960 °C.
  12. Procédé selon l'une des revendications 9 à 11, caractérisé en ce que la température de bobinage est de 450 à 750 °C.
  13. Procédé selon l'une des revendications 9 à 12, caractérisé en ce que le recuit du feuillard à chaud est réalisé sous la forme d'un recuit sous cloche.
  14. Procédé selon l'une des revendications 9 à 13, caractérisé en ce que le laminage à froid est réalisé en deux étapes ou plus et un recuit intermédiaire est effectué entre les étapes du laminage à froid.
EP13155225.9A 2013-02-14 2013-02-14 Produit plat en acier laminé à froid pour applications d'emboutissage profond et son procédé de fabrication Active EP2767601B1 (fr)

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EP13155225.9A EP2767601B1 (fr) 2013-02-14 2013-02-14 Produit plat en acier laminé à froid pour applications d'emboutissage profond et son procédé de fabrication
US14/767,741 US10513762B2 (en) 2013-02-14 2014-02-13 Cold-rolled flat steel product for deep drawing applications and method for production thereof
CN201480021223.4A CN105121673A (zh) 2013-02-14 2014-02-13 用于深冲应用的冷轧扁钢产品及其制造方法
CN201910355506.7A CN110295317A (zh) 2013-02-14 2014-02-13 用于深冲应用的冷轧扁钢产品及其制造方法
BR112015019413A BR112015019413A2 (pt) 2013-02-14 2014-02-13 produto plano de aço laminado a frio para aplicações de estampagem e método para a sua produção
PCT/EP2014/052810 WO2014125016A1 (fr) 2013-02-14 2014-02-13 Produit plat en acier laminé à froid pour emboutissage et son procédé de fabrication
JP2015557422A JP6383368B2 (ja) 2013-02-14 2014-02-13 深絞りを適用するための冷間圧延された平鋼製品及びそれを製造するための方法
KR1020157024979A KR102193066B1 (ko) 2013-02-14 2014-02-13 딥드로잉 적용을 위한 냉간압연 평강 제품 및 그 제조 방법

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BR112015019413A2 (pt) 2017-07-18
WO2014125016A1 (fr) 2014-08-21
EP2767601A1 (fr) 2014-08-20
CN110295317A (zh) 2019-10-01
CN105121673A (zh) 2015-12-02
JP6383368B2 (ja) 2018-08-29
KR20150119230A (ko) 2015-10-23
JP2016511795A (ja) 2016-04-21
US20160017467A1 (en) 2016-01-21
KR102193066B1 (ko) 2020-12-21

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