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EP3781717A1 - Produit en acier plat laminé à froid ainsi qu'utilisation et procédé pour la fabrication d'un tel produit en acier plat - Google Patents

Produit en acier plat laminé à froid ainsi qu'utilisation et procédé pour la fabrication d'un tel produit en acier plat

Info

Publication number
EP3781717A1
EP3781717A1 EP18729562.1A EP18729562A EP3781717A1 EP 3781717 A1 EP3781717 A1 EP 3781717A1 EP 18729562 A EP18729562 A EP 18729562A EP 3781717 A1 EP3781717 A1 EP 3781717A1
Authority
EP
European Patent Office
Prior art keywords
flat steel
steel product
elements
steel
content
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP18729562.1A
Other languages
German (de)
English (en)
Other versions
EP3781717B1 (fr
Inventor
Jonas Karl Moritz SCHWABE
Harald Hofmann
Matthias Schirmer
Evgeny BALICHEV
Annette BÄUMER
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
ThyssenKrupp AG
Original Assignee
ThyssenKrupp Steel Europe AG
ThyssenKrupp AG
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by ThyssenKrupp Steel Europe AG, ThyssenKrupp AG filed Critical ThyssenKrupp Steel Europe AG
Publication of EP3781717A1 publication Critical patent/EP3781717A1/fr
Application granted granted Critical
Publication of EP3781717B1 publication Critical patent/EP3781717B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • 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
    • 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
    • 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
    • C21D8/0273—Final recrystallisation 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0426—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
    • C21D8/04—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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—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
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • 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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • 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
    • 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
    • C23C2/06—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
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
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    • C22C38/105—Ferrous alloys, e.g. steel alloys containing cobalt containing Co and Ni
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    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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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 optimum combination of its mechanical properties for the forming into components, in particular vehicle components and the like.
  • the invention relates to a method for producing such a cold-rolled steel flat product.
  • the invention calls for such flat steel products particularly suitable uses.
  • contents of a steel or a flat steel product are mentioned in the present text, these contents always refer to the weight (stated in% by weight), unless expressly stated otherwise. If information on the composition of atmospheres or gas mixtures is given in the present text, these relate to the individual
  • High-strength, cold-formable steels and steel flat products produced therefrom are used in particular for the production of body components for
  • 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, balance iron and unavoidable impurities, with Mn contents of 4-7%,
  • At least 20% of the microstructure of the cold-rolled sheet consists of retained austenite and more than 50% of lathet-type annealed ferrite. At the same time, the retained austenite and the ferrite have an ultrafine grain size of less than 5 pm.
  • laboratory scale is a corresponding melted, melted by vacuum induction melt melted into slabs, which has then been pre-rolled to 20 mm thick plates. The plates were kept at a temperature of 1230 ° C for 3 hours to effect homogenization, and then hot rolled in three steps into plates of 4 mm thickness. The hot rolled plates leaving the finish hot roll stand at a final temperature of 900 ° C were then quenched to a coiler temperature of 750 ° C where they were subsequently held for one hour. Then the plates are in the oven
  • the object has arisen to create a cold rolled flat steel product satisfying the practical requirements of its usability with high reliability, which can be produced reliably even on a large industrial scale.
  • the invention has achieved this object in that such a flat steel product according to claim 1 is formed.
  • 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 passenger 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 may also be used particularly well for the production of devices intended to provide ballistic protection. Because of her good
  • flat steel products according to the invention are also particularly suitable for internal or external high-pressure forming processes.
  • components for internal combustion engines such as camshafts, piston rods and the like, can also be produced from flat steel products according to the invention.
  • a flat steel product according to the invention is therefore characterized in that it has a value of at least 0.21 in the cold-rolled state, the flat steel product being made of a steel which consists of (in% by weight)
  • Elements is at least 0.05% and at most 1%, and / or one or more elements from the group "Zr, La, Ce, Y" with the proviso that the sum of the contents of these elements is at least 0.05% and at most 0.3%, as well as the balance iron and unavoidable impurities
  • % Mn /% Al> 1, 2 for the ratio% Mn /% AI and for Al eq % Al + 0.4 x (% Si) 3 - 3 x (% Si) 2 + 8.3 x% Si is 3 ⁇ Al eq ⁇ 8 with% Mn: respective Mn content of the steel
  • the structure of the flat steel product consists of 10 - 60 area austenite and 40 - 90 area% ferrite with an average austenite grain size of 0.85 - 3 pm.
  • the flat steel product according to the invention in this case has a composition and a structural state, which give it optimized properties for the respective purposes.
  • the invention provides a content of carbon ("C") of 0.08 - 0.25 wt .-%, in order to ensure a sufficient amount of austenite in the structure of the flat steel product.
  • C content of carbon
  • the C content is limited to 0.25 wt .-% to the
  • the carbon acts as solidifying agent
  • the upper limit of the C content according to the invention is limited to 0.25 wt .-%, with C contents of at most 0.22 wt .-%, in particular of not more than 0.19 wt .-% or more preferably of at most 0.17 wt .-% have been found to be particularly favorable in terms of avoiding negative effects of C-content.
  • the positive effects of the presence of C in the flat steel product according to the invention can be utilized in that the C content is at least 0.08% by weight, with contents of at least 0.11% by weight C, in particular at least 0, 13 wt .-% C, set the beneficial effects particularly safe.
  • Aluminum is present in the flat steel product according to the invention in amounts of 3 to 5.4% by weight in order to reduce the density on the one hand and the weight of the flat steel product on the other hand
  • AI 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 at Al contents of at least 3% by weight, with contents of at least 4% by weight being particularly favorable in this respect.
  • the Al content of a flat steel product according to the invention is limited to at most 5.4% by weight. Al contents above this limit would lead to a deterioration in cold workability due to formation of intermetallic phases. Al contents of not more than 5.1% by weight have proven to be particularly suitable for achieving good cold workability.
  • Al forms particles that emit nitrogen and carbon embrittlement, reduces thermal conductivity, and lowers the modulus of elasticity.
  • Manganese is present in the flat steel product of the present invention at levels of 6-14% 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 by the invention improves the thermoformability, weldability and strength of the material
  • Mn acts in the production of the steel from which the flat steel product according to the invention consists, deoxidizing. Too high Mn contents are avoided so as not to impair the corrosion resistance of the flat steel product. In addition, too high Mn contents lead to too high stability of the austenite, so that the TRIP effect is prevented or restricted, which has a negative effect on the formability of the flat steel product.
  • the positive effects of Mn in a flat steel product according to the invention can be used with particular certainty at levels of at least 8% by weight, in particular at least 9% by weight. Negative influences of the presence of Mn with simultaneously optimized cost-benefit ratio can be avoided by limiting the Mn content to at most 12% by weight, in particular at most 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 Boron
  • B may optionally be present in the flat steel product of the present invention to aid in the formation of a fine texture.
  • B may optionally be present in the flat steel product of the present invention to aid in the formation of a fine texture.
  • B Boron
  • up to 0.1 wt .-% B may 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 wt .-%.
  • the positive influence of B at B contents of less than 0.02% by weight can be used particularly effectively.
  • Chromium (“Cr”) may optionally be added to the flat steel product of the present invention in amounts of up to 2% by weight in order to remove the corrosion and
  • Cr carbides may be formed which increase the ductility of the
  • Steel flat product can affect.
  • the effective influence of Cr at Cr contents of less than 0.8% by weight can be used particularly effectively.
  • the positive effects of Cr can be used particularly reliably 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.
  • excessive Si contents may degrade the ductility and degrade the weldability of the flat steel product of the present invention.
  • Phosphorus is basically undesirable in the invention
  • the P content is limited to at most 0.1% by weight, especially at most 0.05% by weight.
  • S Sulfur
  • S is also in the flat steel product according to the invention an undesirable accompanying element, since it is too high levels the
  • Hot workability during hot rolling reduces and deteriorates corrosion resistance.
  • Tantalum Tantalum
  • W tungsten
  • Ni nickel
  • Ni contributes to the strength and toughness of the flat steel product. Likewise, Ni increases the
  • Cu copper
  • the positive influence of Cu can be used particularly effectively at Cu contents of less than 0.1% by weight.
  • Ca Calcium
  • Ca may optionally be added to the steel flat product at levels of up to 0.15% by weight for setting deleterious S levels.
  • Ca is particularly effective in amounts of up to 0.05 wt .-%, which, as far as Ca is ever present, are therefore preferred. Detrimental effects of Ca can thereby be safely avoided that the Ca content is limited to less than 0.01 wt .-%.
  • N Nitrogen
  • the N content of the flat steel product according to the invention is limited to not more than 0.02 wt .-%, in particular 0.01 wt .-%, with practical N contents in the range of 0.001 to 0.008 wt .-% can be found.
  • Co Cobalt
  • Co Cobalt
  • Flat steel product is present to reduce edge stability by the formation of precipitates, i. avoiding the formation of cracks during the
  • the elements of the group "Ti, Nb, V, Mo” alone i. without the presence of an element of the group “Zr, La, Ce, Y", or in combination with at least one of the elements of the group “Zr, La, Ce, Y”.
  • the elements of the group "Zr, La, Ce, Y" alone i. without the presence of any 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 of the group "Ti, Nb, V, Mo" are present, the sum of the contents is also 0.05-1% by weight.
  • An optimal cost-benefit relation can be obtained if, in the case that only one element of this group is present, individually or in the case that two or more elements of this group are present, in sum the content of the respectively present elements of the group at most 0.2 wt .-%, in particular at most 0.15 wt .-%, is.
  • Ti titanium
  • Ti carbides titanium carbides
  • Nb titanium
  • Ti carbides titanium carbides
  • Nb titanium
  • Ti enhances strength through the formation of Ti carbides and improves r-value.
  • the positive effect on the edge stability and the strength of Ti results in particular when Nb is present at the same time.
  • the simultaneous presence of Ti and Nb is therefore preferred.
  • the addition of Ti also improves the low temperature toughness and heat resistance of the material. Too high levels of Ti should, however, be avoided in order to avoid negative influences on the ductility and the welding properties.
  • the beneficial effect of Ti can be used especially when the Ti content is at least 0.06 wt .-%.
  • niobium (“Nb”) in addition to improving the edge stability, which results especially when Ti and Nb coexist, produces one
  • Nb carbides Increasing the strength by the formation of Nb carbides and improves the r-value, which effect is particularly safe when Ti is present at the same time.
  • the addition of Nb also improves the r-value, which effect is particularly safe when Ti is present at the same time.
  • Nb can be used especially when the Nb content is at least 0.03 wt .-%.
  • V Vanadium
  • V improves the r value of the flat steel product.
  • the positive effects of V at levels of at least 0.03% by weight can be used particularly reliably.
  • Mo molybdenum
  • Ce cerium
  • La lanthanum
  • Zr zirconium
  • Y yttrium
  • the edge stability On the other hand, they also act desulphurising and deoxidizing. In addition, they increase the r-value and improve the thermoforming ability. Ce, La, Zr and Y compensate in this way the negative influences that high Al contents on these properties of the
  • Steel flat product may have.
  • the effects of Ce, La, Zr and Y are the same, so that these elements can be interchanged.
  • the additional proviso according to which the aluminum equivalent Al eq formed from the respective Al and Si content must be in the range from 3 to 8% by weight ensures that the contents of the similarly acting alloying elements Al and Si are limited to the extent that the formation of extremely embrittling intermetallic precipitates is prevented.
  • the range specified for Al eq can be restricted according to the invention to not more than 7.6% by weight, in particular not more than 7% by weight or not more than 6.5% by weight.
  • the minimum value for Al eq may be 4.8% by weight.
  • the ratio% Mn /% Al of the contents of Mn ("% Mn") and Al ("% Al") should be more than 1.2% by weight, so that, despite the high Al content, a sufficient amount of austenite in the structure of
  • Flat steel product has an n-value of at least 0.21, wherein
  • n values of at least 0.25, in particular at least 0.26.
  • Flea n values represent high high elongation at break A50
  • the average grain size of the austenite is at least 0.9 pm. It has also proved to be favorable if the maximum size of the austenite grains in the structure of a
  • Steel flat product according to the invention is limited to 1, 5 pm.
  • Recrystallization degree can with the so-called "Kernal Average Misorientation "(" KAM ”) can be quantified.
  • the KAM is a measure of the
  • a low KAM in the ferrite thus ultimately means a high deformability of the ferrite. Since the structure of a
  • a ferrite low KAM may be low
  • KAM of the ferrite is hereby measured in longitudinal section as "KAM 1 5 °", whereby the sample was analyzed by EBSD with a
  • the process according to the invention comprises the following working steps: a) melting a molten steel consisting of (in% by weight) C: 0.08-0.25%, AI:
  • Hot rolling end temperature which is 850 - 1050 ° C; e) cooling the hot strip to a coiler temperature 400-900 ° C
  • f) coiling the hot strip cooled to the coiler temperature into a coil is; f) coiling the hot strip cooled to the coiler temperature into a coil; g) optional: annealing of the hot strip at a hot strip annealing temperature of 700 - 1000 ° C; h) optional: pickling of the hot strip; i) cold rolling the hot strip to a cold rolled steel strip with a total degree of deformation of 25-90%; j) finish annealing the cold rolled steel strip, heating the steel strip to a final annealing temperature and final annealing
  • - is carried out either as continuous annealing in continuous flow through a continuous annealing furnace in which the cold-rolled steel strip is kept for a period of at least 20 seconds and less than 10 minutes to a final annealing temperature of not less than 950 ° C and not more than 1070 ° C, - or as a bell annealing for a period of 0.5 - 60 h at a
  • Final annealing temperature is more than 800 ° C and up to 950 ° C.
  • composite molten steel produced which is typically a slab, a thin slab or a cast strip, are heated through.
  • preheating temperatures are 1100 - 1300 ° C, wherein preheating temperatures of at least 1150 ° C have proven to be particularly reliable in practice.
  • Preheat temperature is limited to at most 1250 ° C, can negatively impact the preheating, such as too doughy consistency of the
  • Hot rolling of the precursor to a hot strip can be done in
  • Hot strip at the end of hot rolling still has a hot rolling end temperature, which is 850 - 1050 ° C. Below 850 ° C
  • Hot rolling temperatures would require such high hot rolling forces that the desired degree of deformation can not be achieved on conventional hot rolling stands. Optimal hot rolling temperatures are therefore in the range of 900 - 1050 ° C.
  • predetermined reel temperature of 400 - 900 ° C cooled, with which they are then coiled to form a coil.
  • the minimum coiler temperature of 400 ° C is due to the poor thermal
  • Conductivity of the steel of a flat steel product according to the invention required because otherwise would result in high temperature gradients in the steel flat product to tensions and a concomitant poor flatness of the hot strip. Too fast cooling in the cooling section could stop the recrystallization processes that begin with the end of hot rolling.
  • the coil wound to the hot strip can be cooled by means of a coil shower to shorten the cooling time and positively influence the formation of scale.
  • the hot strip after cooling in the coil can optionally undergo an annealing, in which it is maintained over a sufficient for the complete recrystallization period at a temperature of 700-1000 ° C, especially 700-900 ° C.
  • the hot strip annealing is optionally carried out as a bell annealing, in which case the annealing time typically takes 0.5 to 60 hours.
  • the hot strip may be subjected to a pickling treatment prior to cold rolling. The in the course of
  • Production process by oxygen-affine elements caused by scale formation on the hot strip surface can be reduced by an extended residence time of the hot strip in the pickling medium.
  • the Hotbandbeizung can be carried out with different pickling media such as hydrochloric acid.
  • the cold-rolling of the hot-rolled strip to a cold-rolled strip is carried out with a Perfectumformgrad 25-90%, in particular at least 40% or at least 50%.
  • the final annealing can be completed in a continuous flow through a conventional continuous furnace or as batch annealing in batch mode.
  • the cold-rolled steel flat product with a typically 1 - 100 K / s, in particular 10 - 80 K / s or 20 - 50 K / s heating rate amounts to a final annealing temperature, which is at least 950 ° C and at most 1070 ° C, heated. Too rapid heating may adversely affect the homogeneity of the heating and, consequently, the homogeneous distribution of properties of the flat steel product.
  • the final annealing temperature is chosen so that the necessary
  • Austenitkorn sets, which is a prerequisite for the TRIP properties and the n value of the flat steel product according to the invention.
  • the necessary austenitic grain size can be adjusted particularly safely if the final annealing temperature is at least 970 ° C.
  • Optimally practical final annealing temperatures are in the range of 1000 - 1070 ° C.
  • Final annealing temperatures can produce flat steel products according to the invention having austenite grain sizes of 0.9-1.5 pm and a n-value lying regularly above 0.25, for example above 0.26.
  • the holding times at the final annealing temperature in the continuous annealing furnace amount to no more than 10 minutes, in particular not more than 5 minutes or 3 minutes, depending on the level of the final annealing temperature, with higher continuous annealing temperatures allowing shorter holding times and minimum holding times of at least 20 seconds being practical ,
  • the under the hood placed in the coil is cold rolled with a
  • the annealing times after reaching the final annealing temperature are in the range of 0.5 - 60 h,
  • the flat steel product according to the invention can be provided with a protective coating. This can be applied, for example, in a conventional manner by means of coating systems available in practice as a zinc or aluminum-based coating.
  • melts A - H were prepared, the wet-chemically determined analyzes of which are given in Table 1.
  • the analysis data of the individual elements relate in each case to the determined contents in% by weight. If this 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 concerned was consequently ineffective with regard to the properties.
  • the detection limits are 0.005 wt% for P and Ti, 0.001 wt% for Cr, Co, S, and Ca respectively, and 0.01 wt% for V, Mo, and Ni, respectively.
  • Cu and Nb each at 0.02 wt%
  • B at 0.0004 wt% and for Ce, La, Y, Zr, As and Sn each at 0.002 wt%).
  • Allocate impurities include, for example, contents of As, Sn, Mg and H.
  • the sums 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 individual melts are given in Table 2.
  • melts A and B are not
  • melts A - H were cast in a conventional manner to blocks, which then at a
  • Preheat temperature VWT have been through a period VWD Maschinenmint.
  • the blocks After being soaked, the blocks have also been conventionally rolled into slabs in a conventional hot rolling mill.
  • the slabs were rolled in a hot rolling mill to hot strip with a thickness of 2.5 - 3.0 mm.
  • the hot rolling was finished with a hot rolling end temperature WET.
  • the hot strips obtained in this case were cooled in air in each case to a reel temperature HT at which they have been coiled to form a coil.
  • Edge cracks have been classified as such hot bands where regular indentations larger than 15 mm have been found.
  • Hot tapes affected by "edge cracks” are classified as having regular notches with a size of 2 - 15 mm.
  • the rating “none” is in the
  • Hot tapes were made in which maximum notches were present with a size of less than 2 mm.
  • hot strips were then subjected to a hot strip annealing, which has been carried out as a bell annealing with an annealing temperature of 850 ° C and an annealing time of 6 hours.
  • the annealed as well as the unannealed hot tapes have been cold rolled into cold rolled steel strip in a conventional cold rolling machine with a total cold forming degree KGW.
  • the cold-rolled steel strips obtained are in continuous (“Konti”) in a continuous annealing furnace or batchwise in one
  • Annealing annealing furnace (“hood") has been final annealed. They are each with an average heating rate HR on the respective
  • Final annealing temperature Tsg have been heated, in which they have been held for a duration tsg.
  • Hot-rolled annealing the total cold forming degree KGW, the type of final annealing, the heat-up rate HR of the final annealing, the final annealing temperature Tsg and the final annealing time tsg are given in Table 3a and Table 3b.
  • the yield strengths ReH and ReL, the yield strength Rp0.2, the tensile strength Rm and the elongation at break A50 have been determined according to DIN EN ISO 6892-1: 2009 on cold-rolled strip in the transverse direction.
  • to Determination of the austenite grain size KG was determined by means of EBSD (Electron Back Scattering Diffraction) of the mean circular equivalent grain diameter.
  • n 10-2 o and the r 10 2o value and the KAM value have been determined in the manner already explained above. Unrecorded values are indicated in Table 3 by.
  • predetermined temperature range of 950 - 1070 ° C was.
  • Table 4a means that the corresponding value has not been determined.
  • Table 4b indicates that the corresponding value has not been determined.

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Abstract

L'invention concerne un produit en acier plat laminé à froid à résistance élevée ayant une valeur n d'au moins 0,21, satisfaisant des exigences pratiques concernant sa capacité d'utilisation en toute sécurité, pouvant être produit de manière sûre à l'échelle industrielle. Le produit en acier plat est fabriqué à partir d'un acier qui se compose (en % en poids) de C : 0,08 - 0,25%, Al : 3 - 5,4%, Mn : 6 - 14%, B : 0 - 0,1%, Cr : 0 - 2%, Si : 0 - 0,4%, P : 0 - 0,1%, S : 0 - 0,3%, Ta : 0 - 0,5%, W : 0 - 0,5%, Ni : 0 - 2%, Cu : 0 - 2%, Ca : 0 - 0,15%, N : 0 - 0,02% Co : 0 - 2% ainsi que d'un ou plusieurs éléments du groupe « Ti, Nb, V, Mo », avec la condition que la somme des teneurs en ces éléments soit de 0,05 - 1%, et/ou d'un ou plusieurs éléments du groupe « Zr, La, Ce, Y », avec la condition que la somme des teneurs en ces éléments soit de 0,05 - 0,3%, le reste étant du fer et des impuretés inévitables, pour le rapport %Mn/%Al, on a %Mn/%Al > 1,2 et pour Aleq = %Al + 0,4 x (%Si)3 - 3 x (%Si)2 + 8,3 x %Si, on a 3 < Aleq < 8, %Mn étant la teneur en Mn, %Al la teneur en Al et %Si la teneur en Si de l'acier, la structure du produit en acier plat étant composée à 10 - 60% en superficie d'austénite et à 40 - 90% en superficie de ferrite avec une grosseur de grain moyenne de l'austénite de 0,85 - 3 μm. L'invention concerne en outre un procédé pour la fabrication d'un tel produit en acier plat, qui comprend comme étape de travail essentielle un recuit final effectué sous la forme de recuit continu pendant 20 s à 10 min à 950 à 1070°C ou de recuit sous cloche pendant 0,5 à 60 h à > 850 - 950°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)

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