EP3332046B1 - Acier au manganèse à haute résistance contenant de l'aluminium, procédé de fabrication d'un produit plat en acier à partir de cet acier et produit plat en acier fabriqué d'après celui-ci - Google Patents

Acier au manganèse à haute résistance contenant de l'aluminium, procédé de fabrication d'un produit plat en acier à partir de cet acier et produit plat en acier fabriqué d'après celui-ci Download PDF

Info

Publication number
EP3332046B1
EP3332046B1 EP16747515.1A EP16747515A EP3332046B1 EP 3332046 B1 EP3332046 B1 EP 3332046B1 EP 16747515 A EP16747515 A EP 16747515A EP 3332046 B1 EP3332046 B1 EP 3332046B1
Authority
EP
European Patent Office
Prior art keywords
steel
strip
hot
slab
weight
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.)
Active
Application number
EP16747515.1A
Other languages
German (de)
English (en)
Other versions
EP3332046A1 (fr
Inventor
Peter PALZER
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.)
Salzgitter Flachstahl GmbH
Original Assignee
Salzgitter Flachstahl GmbH
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 Salzgitter Flachstahl GmbH filed Critical Salzgitter Flachstahl GmbH
Publication of EP3332046A1 publication Critical patent/EP3332046A1/fr
Application granted granted Critical
Publication of EP3332046B1 publication Critical patent/EP3332046B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—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
    • 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
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing
    • C21D8/0421—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing characterised by the working steps
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing
    • C21D8/0421—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing characterised by the working steps
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing
    • C21D8/0447—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing characterised by the heat treatment
    • C21D8/0463—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing characterised by the heat treatment 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
    • 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
    • C22C38/02—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with 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
    • C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C23C2/34—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
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
    • C25D7/00—Electroplating characterised by the article coated
    • C25D7/06—Wires; Strips; Foils
    • C25D7/0614—Strips or foils
    • 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
    • C21D2211/008—Martensite

Definitions

  • the invention relates to a high-strength manganese steel containing aluminum, a method for producing a flat steel product from this steel and a flat steel product produced by this method.
  • the steel consists of the elements (content in percent by weight and based on the steel melt): C: up to 0.5; Mn: 4 to 12.0; Si: up to 1.0; Al: up to 3.0; Cr: 0.1 to 4.0; Cu: up to 4.0; Ni: up to 2.0; N: up to 0.05; P: up to 0.05; S: up to 0.01; as well as remainder iron and unavoidable impurities.
  • One or more elements from the group “V, Nb, Ti” are optionally provided, the sum of the contents of these elements being at most equal to 0.5.
  • This steel is said to be characterized by the fact that it is more cost-effective to manufacture than steels with a high manganese content and at the same time has high elongation at break and thus a significantly improved formability.
  • a method for producing a flat steel product from the above-described high-strength manganese-containing steel comprises the following work steps: - Melting the above-described steel melt, - Generating a starting product for subsequent hot rolling by converting the steel melt into a strand from which at least one slab or thin slab is used as the starting product for the hot rolling is divided or cast into a cast strip that is fed to the hot rolling as a starting product, - heat treatment of the starting product in order to bring the starting product to a hot rolling start temperature of 1150 to 1000 ° C, - hot rolling of the starting product to a hot strip with a Thickness of at most 2.5 mm, the hot rolling being terminated at a final hot rolling temperature of 1050 to 800 ° C, - Coiling of the hot strip into a coil at a coiling temperature of ⁇ 700 ° C.
  • the disclosure document WO 2014/132968 A1 discloses a high strength hot rolled steel containing, in weight percent: C: 0.01-0.2; Si: 0-2.5; Mn: 0-4.0; Al: 0-2.0; N: 0-0.01; Ni: 0-2.0; Mo: 0-1.0; V: 0-0.3; Cr: 0-2.0; Mg: 0-0.01, Ca: 0 - 0.01, Cu: 0 - 2.0 and the remainder iron and unavoidable impurities. Simultaneous addition of Mo and Cr is not intended.
  • the patent application EP 2 772 556 A1 discloses a high strength steel strip with improved formability.
  • the steel composition contains in% by weight: C: 0.03-0.35; Si: 0.5-3.0; Mn: 3.5-10; P: 0.1 or less; S: 0.02 or less with the balance iron and unavoidable impurities.
  • the present invention is based on the object of creating a high-strength aluminum-containing manganese steel with good forming properties and increased resistance to delayed crack formation and hydrogen embrittlement, a method for producing a flat steel product from this steel and a flat steel product produced according to this method, based on offer the steel a good combination of strength and forming properties.
  • a high-strength aluminum-containing manganese steel having a multiphase structure consisting of ferrite and / or martensite and / or bainite as well as retained austenite and a TRIP and / or TWIP effect with a residual austenite proportion of 5% to 65%, with a tensile strength Rm> 800 up to 1700 MPa, with an elongation at break A50 of 6 to 45%, preferably> 8 to 45%, and the following chemical composition (in% by weight): C: 0.01 to ⁇ 0.3;; Mn: 4 to ⁇ 10;Al:> 1 to 4; Si: 0.01 to 1; Cr: 0.1 to 4; Mo; 0.02 to 1; P: ⁇ 0.1; S: ⁇ 0.1; N: ⁇ 0.3; with the addition of one or more of the following elements (in% by weight): W: 0.03 to 3; Co: 0.05 to 3; Zr: 0.03 to 0.5; The remainder iron including unavoidable steel-ac
  • Manganese content (medium manganese steel) based on the alloy elements C, Mn, Cr, Al, Si and Mo relatively inexpensive. Due to the increased Al content, the steel has a lower specific density compared to other low-alloy manganese steels with medium manganese contents.
  • the manganese steel according to the invention is also distinguished by an increased resistance to delayed crack formation (delayed fracture) and to hydrogen embrittlement. This is achieved by precipitating molybdenum carbide, which acts as a hydrogen trap.
  • An A50 test specimen was used for the elongation at break tests in accordance with DIN 50 125.
  • the steel according to the invention has a multiphase structure consisting of ferrite and / or martensite and / or bainite and retained austenite and a TRIP and / or TWIP effect.
  • the residual austenite is partially or completely converted into martensite by the TRIP effect. Due to the TRIP effect, the elongation at break, especially in terms of uniform elongation, and tensile strength increase significantly.
  • the steel according to the invention is particularly suitable for producing high-strength heavy plate, hot and cold strip, which can be provided with a metallic or non-metallic coating.
  • An application in vehicle construction, shipbuilding, plant construction, infrastructure construction, in aerospace and home appliance technology is conceivable.
  • Alloy elements are usually added to the steel in order to specifically influence certain properties.
  • An alloying element can influence different properties in different steels. The effect and interaction generally depends heavily on the amount, the presence of other alloying elements and the state of solution in the material. The relationships are varied and complex. In the following, the effect of the alloying elements in the alloy according to the invention will be discussed in more detail become.
  • the positive effects of the alloying elements used according to the invention are described below: Carbon C: Is required for the formation of carbides, stabilizes the austenite and increases the strength. Higher contents of C impair the welding properties and lead to a deterioration in the elongation and toughness properties, which is why a maximum content of less than 0.3% by weight is specified. In order to achieve sufficient strength of the material, a minimum addition of 0.01% by weight is required.
  • Manganese Mn Stabilizes austenite, increases strength and toughness and enables deformation-induced martensite and / or twin formation in the alloy according to the invention. Contents less than 4% by weight are not sufficient to stabilize the austenite and thus worsen the elongation properties, while contents of 10% by weight and more stabilize the austenite too much and thereby reduce the strength properties, in particular the yield point. For the manganese steel according to the invention with medium manganese contents, a range from 4 to ⁇ 10% by weight is preferred.
  • Aluminum Al An Al content greater than 1% by weight improves the strength and elongation properties, reduces the specific density and influences the transformation behavior of the alloy according to the invention. Al contents of more than 4% by weight deteriorate the elongation properties. Higher Al contents also significantly worsen the casting behavior in continuous casting. This results in a higher effort when potting. Below 4% by weight, Al retards the precipitation of carbides. Therefore a maximum content of 4% by weight and a minimum content of> 1% by weight are specified.
  • Silicon Si hinders the carbon diffusion, reduces the specific density and increases the strength and the elongation and toughness properties. Furthermore, an improvement in cold rollability could be observed through the addition of Si. Contents of more than 1% by weight lead to embrittlement of the material and have a negative effect on hot and cold rollability and coatability, for example through galvanizing. A maximum content of 1% by weight and a minimum content of 0.01% by weight are therefore specified. A maximum content of less than 1% by weight is preferably specified.
  • Chromium Cr Improves strength and reduces the rate of corrosion, delays the formation of ferrite and pearlite and forms carbides.
  • the maximum content is set at less than 4% by weight, since higher contents result in a deterioration in the elongation properties.
  • a minimum Cr content is set at 0.1% by weight.
  • Molybdenum Mo Acts as a carbide former, increases strength and increases the resistance to delayed crack formation and hydrogen embrittlement. Mo contents of more than 1% by weight deteriorate the elongation properties, which is why a maximum content of 1% by weight and a minimum content of 0.02% by weight are specified.
  • Phosphorus P is a trace element from iron ore and is dissolved in the iron lattice as a substitution atom. Phosphorus increases hardness through solid solution strengthening and improves hardenability. As a rule, however, attempts are made to lower the phosphorus content as much as possible, since, among other things, due to its low diffusion rate, it is highly susceptible to segregation and to a great extent reduces the toughness. The accumulation of phosphorus at the grain boundaries can cause cracks to appear along the grain boundaries during hot rolling. In addition, phosphorus increases the transition temperature from tough to brittle behavior by up to 300 ° C. For the reasons mentioned above, the phosphorus content is limited to less than 0.1% by weight.
  • Sulfur S Like phosphorus, it is bound as a trace element in iron ore. It is generally undesirable in steel, since it tends to segregate strongly and has a strong embrittling effect, as a result of which the elongation and toughness properties are impaired. Attempts are therefore made to achieve the lowest possible amounts of sulfur in the melt (e.g. by means of a deep vacuum treatment). For the reasons mentioned above, the sulfur content is limited to less than 0.1% by weight.
  • N is also an accompanying element in steel production. In the dissolved state, it improves the strength and toughness properties of steels with a higher manganese content with greater than or equal to 4% wt. Lower Mn-alloyed steels ⁇ 4% by weight with free nitrogen tend to have a strong aging effect. The nitrogen diffuses at dislocations even at low temperatures and blocks them. It thus causes an increase in strength combined with a rapid loss of toughness.
  • a setting of the nitrogen in the form of nitrides is possible, for example, by adding aluminum, vanadium, niobium or titanium. For the reasons mentioned above, the nitrogen content is limited to less than 0.3% by weight.
  • Micro-alloy elements are generally only added in very small amounts ( ⁇ 0.1% by weight per element). In contrast to the alloying elements, they mainly work through the formation of precipitates, but can also influence the properties in a dissolved state. Despite the small additions, micro-alloying elements have a strong influence on the manufacturing conditions as well as the processing and final properties.
  • Typical micro-alloy elements are vanadium, niobium and titanium. These elements can be dissolved in the iron lattice and form carbides, nitrides and carbonitrides with carbon and nitrogen.
  • Vanadium V and niobium Nb These have a grain-refining effect through the formation of carbides, which at the same time improves strength, toughness and elongation properties. Contents of more than 1% by weight bring no further advantages. For vanadium and niobium, a minimum content of greater than or equal to 0.02% by weight and a maximum content of less than or equal to 1% by weight are optionally provided.
  • Titanium Ti Has a grain-refining effect as a carbide former, which at the same time improves strength, toughness and elongation properties and reduces intergranular corrosion. Contents of Ti of more than 1 wt .-% worsen the elongation properties, which is why a maximum content of 1 wt .-% is optionally specified. Minimum contents of 0.02% by weight can preferably be provided.
  • Tin Sn Tin increases the strength, but, like copper, builds up under the scale and at the grain boundaries at higher temperatures. By penetrating the grain boundaries, it leads to the formation of low-melting phases and the associated cracks in the structure and to solder brittleness, which is why an optional Maximum content of less than or equal to 0.5% by weight and a minimum content of 0.005% by weight can be provided.
  • Copper Cu Reduces the rate of corrosion and increases strength. Contents above 3 wt.% Worsen the producibility by the formation of low-melting phases during casting and hot rolling, which is why a maximum content of 3 wt.% And a minimum content of 0.005 wt.% Are optionally specified. A minimum content of 0.5% by weight is preferably provided.
  • Tungsten W acts as a carbide former and increases strength and heat resistance. W contents of more than 3% by weight deteriorate the elongation properties, which is why a maximum content of 3% by weight and a minimum content of 0.03% by weight are optionally specified. A minimum content of 0.05% by weight is preferably provided.
  • Cobalt Co Increases the strength of the steel, stabilizes the austenite and improves the high temperature strength. Contents of over 3% by weight worsen the elongation properties, which is why a maximum content of less than or equal to 3% by weight and a minimum content of 0.05% by weight are optionally specified. A minimum content of 0.08% by weight is preferably provided.
  • Zirconium Zr Acts as a carbide former and improves strength. Zr contents of more than 0.5% by weight deteriorate the elongation properties, which is why a maximum content of 0.5% by weight and a minimum content of 0.03% by weight are optionally specified. A minimum content of 0.05% by weight is preferably provided.
  • Calcium is used to modify non-metallic oxidic inclusions, which could otherwise lead to undesired failure of the alloy due to inclusions in the structure, which act as stress concentration points and weaken the metal bond. Furthermore, Ca improves the homogeneity of the alloy according to the invention. In order to develop a corresponding effect, an optional minimum content of 0.0005% by weight is necessary. Contents of above 0.1% by weight Ca bring no further advantage in the inclusion modification, impair the producibility and should be avoided due to the high vapor pressure of Ca in steel melts. Hence a Maximum content of 0.1% by weight provided.
  • the process results in a steel product in the form of a heavy plate, hot or cold strip. It is intended that the hot strip will be wound at a maximum temperature of 780 ° C.
  • the room temperature is given as the lower limit, as the winding temperature has only a minor influence on subsequent processing properties.
  • strips with a thickness of more than 3 mm are referred to as heavy plate, and these can still be wound up, for example, with a thickness of 5 mm.
  • Heavy plate with a greater thickness, for example 50 mm is flattened to sheet material after hot rolling, since it can no longer be wound. If required, the hot or cold strip can also be cut.
  • the final hot rolling temperature is usually between 950 ° C and A c 1 + 50 K.
  • the usual thickness ranges for pre-strip are 1 mm to 35 mm and for slabs and thin slabs 35 mm to 450 mm. It is preferably provided that the slab or thin slab is hot rolled into a hot strip or heavy plate with a thickness of 70 mm to 1.5 mm or the pre-strip cast close to its final dimensions is hot rolled into a hot strip with a thickness of 8 mm to 1 mm.
  • the cold strip according to the invention has a thickness of, for example, greater than 0.15 mm.
  • a pre-strip produced near net dimensions using the two-roll casting method with a thickness of less than or equal to 3 mm, preferably 1 mm to 3 mm, is already understood as hot strip.
  • the pre-strip produced in this way as hot strip does not have a 100% cast structure due to the forming of the two counter-rotating rolls. Hot rolling thus already takes place inline during the two-roller casting process, so that separate hot rolling can be omitted.
  • the hot rolling reheating temperatures in the range of 720 ° C to 1200 ° C are provided. If only a few roller passes need to be made, the reheating temperature can be selected at the lower end of the range.
  • the hot strip, as well as the heavy plate, can optionally be subjected to a heat treatment in the temperature range between 610 and 780 ° C. for 1 minute to 48 hours, with higher temperatures being associated with shorter treatment times and vice versa.
  • the annealing can take place both in a hood annealing (longer annealing times) and, for example, in a continuous annealing (shorter annealing times).
  • the heat treatment can also be omitted if the hot strip or heavy plate already has the finished properties.
  • the annealed hot strip is optionally cold-rolled with the aim of setting the thicknesses required for the end application of greater than or equal to 0.15 mm.
  • a further annealing process can then be carried out, possibly coupled with a coating process and finally your skin-pass process, with which the surface structure required for the end application is set.
  • the flat steel product is preferably hot-dip galvanized or electrolytically galvanized or coated with a metallic, inorganic or organic coating.
  • a flat steel product in the form of heavy plate, hot strip or cold strip produced by the process according to the invention has a tensile strength Rm> 800 to 1700 MPa and an elongation at break A50 of 6 to 45%, preferably> 8 to 45%. High strengths tend to be associated with lower elongations at break and vice versa.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Electrochemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)

Claims (13)

  1. Acier au manganèse à haute résistance contenant de l'aluminium, lequel acier présente une structure polyphasique, comprenant de la ferrite et/ou de la martensite et/ou de la bainite ainsi que de l'austénite résiduelle et a un effet TRIP et/ou TWIP, et a une teneur en austénite résiduelle de 5 % à 65 %, une résistance à la traction Rm > 800 à 1700 MPa, un allongement à la rupture A50 de 6 à 45 %, de préférence > 8 à 45 %, et la composition chimique suivante (en % en poids) :
    C : 0,01 à < 0,3
    Mn : 4 à < 10
    Al : > 1 à 4
    Si : 0,01 à 1
    Cr: 0,1 à 4
    Mo : 0,02 à 1
    P: < 0,1
    S: < 0,1
    N: < 0,3
    avec ajout d'un ou de plusieurs des éléments suivants (en % en poids) :
    W : 0,03 à 3
    Co : 0,05 à 3
    Zr : 0,03 à 0,5
    le reste étant du fer incluant des éléments inévitables d'accompagnement de l'acier, et avec ajout facultatif d'un ou de plusieurs des éléments suivants (en % en poids) :
    V : 0,01 à 1
    Nb : 0,01 à 1
    Ti : 0,01 à 1
    Sn : 0 à 0,5
    Cu : 0,005 à 3
    Ca: 0,0005 à 0,1.
  2. Acier selon la revendication 1, caractérisé en ce que l'acier contient (en % en poids) :
    Si : 0,01 à < 1.
  3. Acier selon la revendication 1 ou 2, caractérisé en ce que l'acier contient (en % en poids) :
    V : 0,02 à 1.
  4. Acier selon l'une des revendications 1 à 3, caractérisé en ce que l'acier contient (en % en poids) :
    Nb : 0,02 à 1.
  5. Acier selon l'une des revendications 1 à 4, caractérisé en ce que l'acier contient (en % en poids) :
    Ti : 0,02 à 1.
  6. Acier selon l'une des revendications 1 à 5, caractérisé en ce que l'acier contient (en % en poids) :
    Sn : 0,005 à 0,5.
  7. Acier selon l'une des revendications 1 à 6, caractérisé en ce que l'acier contient (en % en poids) :
    Cu : 0,5 à 3.
  8. Acier selon l'une des revendications 1 à 7, caractérisé en ce que l'acier contient (en % en poids) :
    W: 0,05 à 3.
  9. Acier selon l'une des revendications 1 à 8, caractérisé en ce que l'acier contient (en % en poids) :
    Co : 0,08 à 3.
  10. Acier selon l'une des revendications 1 à 9, caractérisé en ce que l'acier contient (en % en poids) :
    Zr : 0,05 à 0,5.
  11. Procédé de fabrication d'un produit plat en acier ayant une résistance à la traction Rm > 800 à 1700 MPa et un allongement à la rupture A50 de 6 à 45 %, de préférence > 8 à 45 %, à partir d'un acier selon l'une des revendications précédentes 1 à 10, le procédé comprenant les étapes suivantes :
    - obtenir un acier fusion contenant (en % en poids) :
    C : 0,01 à < 0,3
    Mn : 4 à < 10
    Al : > 1 à 4
    Si : 0,01 à 1
    Cr: 0,1 à 4
    Mo : 0,02 à 1
    P: < 0,1
    S: < 0,1
    N: < 0,3
    avec ajout d'un ou de plusieurs des éléments suivants (en % en poids) :
    W : 0,03 à 3
    Co : 0,05 à 3
    Zr : 0,03 à 0,5
    le reste étant du fer incluant des éléments inévitables d'accompagnement de l'acier, et avec ajout facultatif d'un ou de plusieurs des éléments suivants (en % en poids) :
    V: 0,01 à 1
    Nb : 0,01 à 1
    Ti : 0,01 à 1
    Sn : 0 à 0,5
    Cu : 0,005 à 3
    Ca: 0,0005 à 0,1
    - couler l'acier en fusion pour obtenir une pré-bande à l'aide d'un procédé de coulée de bande horizontale ou verticale proche des dimensions finales ou couler de l'acier en fusion pour obtenir une brame ou une brame mince à l'aide d'un procédé de coulée de brame ou de brame mince horizontale ou verticale,
    - réchauffer la brame ou la brame mince jusqu'à une température de 1050 °C à 1250 °C puis laminer à chaud la brame ou la brame mince pour former une bande chaude ou une tôle grossière ou réchauffer la pré-bande réalisée à des dimensions proches des dimensions finales, notamment avec épaisseur supérieure à 3 mm, jusqu'à une température de 1000 °C à 1200 °C puis laminer à chaud la pré-bande pour former une bande chaude ou une tôle grossière ou laminer à chaud la pré-bande sans réchauffage à partir de la chaleur de coulée pour obtenir une bande chaude ou une tôle grossière avec chauffage intermédiaire facultatif entre les passes de laminage individuelles du laminage à chaud,
    - bobiner la bande chaude et éventuellement de la tôle grossière à une température de bobinage comprise entre 780 °C et la température ambiante,
    - porter facultativement au rouge la bande chaude ou la tôle grossière avec les paramètres suivants: température de rougeoiement: 610 à 780 °C, temps de rougeoiement : 1 minute à 48 heures,
    - laminage à froid facultatif de la bande chaude ou de la pré-bande réalisée des dimensions proches des dimensions finales avec une épaisseur inférieure ou égale à 3 mm pour obtenir la bande froide,
    - porter facultativement au rouge la bande froide avec les paramètres suivants : température de rougeoiement : 610 à 780 °C, temps de rougeoiement : 1 minute à 48 heures.
  12. Procédé selon la revendication 11, caractérisé en ce que la brame est laminée à chaud pour obtenir une bande chaude d'une épaisseur de 70 mm à 1,5 mm ou la pré-bande est laminée à chaud pour obtenir une bande chaude d'une épaisseur de 8 mm à 1 mm.
  13. Produit plat en acier fabriqué selon un procédé des revendications 11 ou 12, caractérisé en ce que le produit plat en acier est galvanisé à chaud ou par électrolyse ou est muni d'un revêtement métallique, minéral ou organique.
EP16747515.1A 2015-08-05 2016-08-03 Acier au manganèse à haute résistance contenant de l'aluminium, procédé de fabrication d'un produit plat en acier à partir de cet acier et produit plat en acier fabriqué d'après celui-ci Active EP3332046B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102015112886.1A DE102015112886A1 (de) 2015-08-05 2015-08-05 Hochfester aluminiumhaltiger Manganstahl, ein Verfahren zur Herstellung eines Stahlflachprodukts aus diesem Stahl und hiernach hergestelltes Stahlflachprodukt
PCT/EP2016/068564 WO2017021459A1 (fr) 2015-08-05 2016-08-03 Acier au manganèse hautement résistant contenant de l'aluminium, procédé de fabrication d'un produit plat en acier à partir de cet acier et produit plat en acier fabriqué d'après celui-ci

Publications (2)

Publication Number Publication Date
EP3332046A1 EP3332046A1 (fr) 2018-06-13
EP3332046B1 true EP3332046B1 (fr) 2021-02-24

Family

ID=56567612

Family Applications (1)

Application Number Title Priority Date Filing Date
EP16747515.1A Active EP3332046B1 (fr) 2015-08-05 2016-08-03 Acier au manganèse à haute résistance contenant de l'aluminium, procédé de fabrication d'un produit plat en acier à partir de cet acier et produit plat en acier fabriqué d'après celui-ci

Country Status (6)

Country Link
US (1) US20180230579A1 (fr)
EP (1) EP3332046B1 (fr)
KR (1) KR20180036731A (fr)
DE (1) DE102015112886A1 (fr)
RU (1) RU2709560C2 (fr)
WO (1) WO2017021459A1 (fr)

Families Citing this family (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102016110661A1 (de) * 2016-06-09 2017-12-14 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines kaltgewalzten Stahlbandes aus einem hochfesten, manganhaltigen Stahl
DE102017223633A1 (de) 2017-12-21 2019-06-27 Voestalpine Stahl Gmbh Kaltgewalztes Stahlflachprodukt mit metallischer Korrosionsschutzschicht und Verfahren zur Herstellung eines solchen
DE102018132816A1 (de) 2018-12-19 2020-06-25 Voestalpine Stahl Gmbh Verfahren zur Herstellung von thermo-mechanisch hergestellten profilierten Warmbanderzeugnissen
DE102018132901A1 (de) * 2018-12-19 2020-06-25 Voestalpine Stahl Gmbh Verfahren zur Herstellung von konventionell warmgewalzten Warmbanderzeugnissen
DE102018132860A1 (de) * 2018-12-19 2020-06-25 Voestalpine Stahl Gmbh Verfahren zur Herstellung von konventionell warmgewalzten, profilierten Warmbanderzeugnissen
DE102018132908A1 (de) 2018-12-19 2020-06-25 Voestalpine Stahl Gmbh Verfahren zur Herstellung von thermo-mechanisch hergestellten Warmbanderzeugnissen
CN111575466B (zh) * 2020-06-29 2021-10-22 张家港联峰钢铁研究所有限公司 一种热强耐蚀钢的热处理制备方法
DE102023117976A1 (de) 2022-08-23 2024-02-29 Schaeffler Technologies AG & Co. KG Elektromechanischer Aktuator
CN119256107A (zh) 2022-08-23 2025-01-03 舍弗勒技术股份两合公司 机电致动器
CN116356233A (zh) * 2023-04-11 2023-06-30 重庆大学 一种利用形变孪晶提高锆合金抗氢脆性能的方法

Family Cites Families (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS6054374B2 (ja) * 1982-04-21 1985-11-29 新日本製鐵株式会社 オ−ステナイト鋼板および鋼帯の製造方法
FR2796083B1 (fr) * 1999-07-07 2001-08-31 Usinor Procede de fabrication de bandes en alliage fer-carbone-manganese, et bandes ainsi produites
EP1832667A1 (fr) * 2006-03-07 2007-09-12 ARCELOR France Procédé de fabrication de tôles d'acier à très hautes caractéristiques de résistance, de ductilité et de tenacité, et tôles ainsi produites
KR20090016480A (ko) * 2006-06-01 2009-02-13 혼다 기켄 고교 가부시키가이샤 고강도 강판 및 그 제조 방법
EP1990431A1 (fr) * 2007-05-11 2008-11-12 ArcelorMittal France Procédé de fabrication de tôles d'acier laminées à froid et recuites à très haute résistance, et tôles ainsi produites
KR100985298B1 (ko) * 2008-05-27 2010-10-04 주식회사 포스코 리징 저항성이 우수한 저비중 고강도 열연 강판, 냉연강판, 아연도금 강판 및 이들의 제조방법
US9267193B2 (en) * 2008-11-05 2016-02-23 Honda Motor Co., Ltd High-strength steel sheet and the method for production therefor
RU2493266C2 (ru) * 2009-03-11 2013-09-20 Зальцгиттер Флахшталь Гмбх Способ изготовления горячекатаной полосы и изготовленная из ферритной стали горячекатаная полоса
EP2383353B2 (fr) 2010-04-30 2025-12-31 ThyssenKrupp Steel Europe AG Acier à résistance élevée comprenant du Mn, produit plat en acier composé d'un tel acier et son procédé de fabrication
BR112013025015B1 (pt) * 2011-03-28 2018-11-06 Nippon Steel & Sumitomo Metal Corporation chapa de aço laminada a frio e método de produção da mesma
US9631265B2 (en) * 2011-05-25 2017-04-25 Nippon Steel Hot-rolled steel sheet and method for producing same
US9617614B2 (en) * 2011-10-24 2017-04-11 Jfe Steel Corporation Method for manufacturing high strength steel sheet having excellent formability
KR101382981B1 (ko) * 2011-11-07 2014-04-09 주식회사 포스코 온간프레스 성형용 강판, 온간프레스 성형 부재 및 이들의 제조방법
PL2907886T3 (pl) * 2013-02-26 2019-04-30 Nippon Steel & Sumitomo Metal Corp Blacha stalowa cienka walcowana na gorąco o dużej wytrzymałości mająca maksymalną wytrzymałość na rozciąganie wynoszącą 980 MPa lub więcej oraz mająca doskonałą utwardzalność przy wypalaniu i wiązkość w niskiej temperaturze

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
AUTORENKOLLEKTIV: "Spurenelemente im Stahl - Moeglichkeiten zur Beeinflussung im Smelzbetrieb", SPURENELEMENTE IN STAEHLEN, VERLAG STAHLEISEN, DUESSELDORF, DE, 1 January 1985 (1985-01-01), pages 19 - 22, XP002433212 *

Also Published As

Publication number Publication date
EP3332046A1 (fr) 2018-06-13
RU2018107257A3 (fr) 2019-09-05
RU2018107257A (ru) 2019-09-05
US20180230579A1 (en) 2018-08-16
DE102015112886A1 (de) 2017-02-09
WO2017021459A1 (fr) 2017-02-09
KR20180036731A (ko) 2018-04-09
RU2709560C2 (ru) 2019-12-18

Similar Documents

Publication Publication Date Title
EP3332046B1 (fr) Acier au manganèse à haute résistance contenant de l&#39;aluminium, procédé de fabrication d&#39;un produit plat en acier à partir de cet acier et produit plat en acier fabriqué d&#39;après celui-ci
EP3332047B1 (fr) Procédé de fabrication d&#39;un produit plat en acier laminé flexible et son utilisation
EP2383353B1 (fr) Acier à résistance élevée comprenant du Mn, produit plat en acier composé d&#39;un tel acier et son procédé de fabrication
EP3504349B1 (fr) Procédé de fabrication d&#39;une bande d&#39;acier à résistance très élevée présentant des propriétés améliorées lors du traitement ultérieur et une telle bande d&#39;acier
EP3535431B1 (fr) Produit d&#39;acier à teneur en manganèse intermédiaire pour application à basse température et son procédé de fabrication
EP2855717B1 (fr) Tôle d&#39;acier et méthode pour son obtention
EP2836614B1 (fr) Acier polyphasé à haute résistance et procédé de fabrication d&#39;une bande à partir dudit acier
EP2668302B1 (fr) Procédé de fabrication d&#39;une bande d&#39;acier à partir d&#39;un acier multiphasé à haute résistance mécanique présentant d&#39;excellentes propriétés de déformation
WO2019016041A1 (fr) Produit plat en acier possédant une bonne résistance au vieillissement et son procédé de fabrication
WO2015117934A1 (fr) Produit en acier plat de résistance élevée ayant une texture à base de bainite et de martensite et procédé de fabrication d&#39;un tel produit en acier plat
EP3512968B1 (fr) Procédé pour fabriquer un produit plat en acier à partir d&#39;un acier au manganèse et produit plat en acier résultant
EP3551776B1 (fr) Procédé de fabrication d&#39;une bande laminée à chaud ou à froid et/ou d&#39;un produit plat en acier laminé de manière flexible constitué par un acier contenant du manganèse, hautement solide et produit plat en acier ainsi obtenu
WO2019115551A1 (fr) Produit plat en acier laminé à chaud, à rigidité élevée, doté d&#39;une résistance à la fissuration de bords élevée ainsi que d&#39;une capacité de durcissement à la cuisson élevée, procédé de fabrication d&#39;un tel produit plat en acier
EP2690184A1 (fr) Cold rolled steel flat product and method for its production
EP3325678A1 (fr) Acier léger deformable de construction présentant des propriétés mécaniques améliorées et procédé de fabrication de produit semi-fini à partir de cet acier
DE102016115618A1 (de) Verfahren zur Herstellung eines höchstfesten Stahlbandes mit verbesserten Eigenschaften bei der Weiterverarbeitung und ein derartiges Stahlband
DE202015105104U1 (de) Warmband aus einem bainitischen Mehrphasenstahl mit einer Zn-Mg-Al-Beschichtung
EP3469108B1 (fr) Procédé de fabrication d&#39;une bande d&#39;acier laminée à froid présentant des propriétés trip à partir d&#39;un acier à résistance élevée contenant du manganèse
EP3964591A1 (fr) Produit en acier plat laminé à chaud et procédé de fabrication d&#39;un produit en acier plat laminé à chaud

Legal Events

Date Code Title Description
STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE INTERNATIONAL PUBLICATION HAS BEEN MADE

PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE

17P Request for examination filed

Effective date: 20180221

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

AX Request for extension of the european patent

Extension state: BA ME

DAV Request for validation of the european patent (deleted)
DAX Request for extension of the european patent (deleted)
STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: EXAMINATION IS IN PROGRESS

17Q First examination report despatched

Effective date: 20190509

REG Reference to a national code

Ref country code: DE

Ref legal event code: R079

Ref document number: 502016012450

Country of ref document: DE

Free format text: PREVIOUS MAIN CLASS: C22C0038000000

Ipc: C22C0038040000

RIC1 Information provided on ipc code assigned before grant

Ipc: C22C 38/06 20060101ALI20200910BHEP

Ipc: C22C 38/24 20060101ALI20200910BHEP

Ipc: C22C 38/04 20060101AFI20200910BHEP

Ipc: C23C 26/00 20060101ALI20200910BHEP

Ipc: C22C 38/30 20060101ALI20200910BHEP

Ipc: C21D 9/48 20060101ALI20200910BHEP

Ipc: C23C 2/04 20060101ALI20200910BHEP

Ipc: C21D 8/04 20060101ALI20200910BHEP

Ipc: C21D 8/02 20060101ALI20200910BHEP

Ipc: C22C 38/20 20060101ALI20200910BHEP

Ipc: C22C 38/22 20060101ALI20200910BHEP

Ipc: C23C 20/06 20060101ALI20200910BHEP

Ipc: C22C 38/38 20060101ALI20200910BHEP

Ipc: C23C 2/40 20060101ALI20200910BHEP

Ipc: C22C 38/26 20060101ALI20200910BHEP

Ipc: C22C 38/28 20060101ALI20200910BHEP

Ipc: C22C 38/12 20060101ALI20200910BHEP

Ipc: C22C 38/18 20060101ALI20200910BHEP

Ipc: C21D 6/00 20060101ALI20200910BHEP

Ipc: C22C 38/02 20060101ALI20200910BHEP

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: GRANT OF PATENT IS INTENDED

INTG Intention to grant announced

Effective date: 20201021

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE PATENT HAS BEEN GRANTED

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 1364529

Country of ref document: AT

Kind code of ref document: T

Effective date: 20210315

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

Free format text: LANGUAGE OF EP DOCUMENT: GERMAN

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 502016012450

Country of ref document: DE

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG9D

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20210224

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210224

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210524

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210624

Ref country code: NO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210524

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210525

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210224

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210224

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210224

Ref country code: NL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210224

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210224

Ref country code: PL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210224

Ref country code: RS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210224

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210624

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SM

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210224

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210224

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210224

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 502016012450

Country of ref document: DE

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210224

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210224

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210224

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: AL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210224

Ref country code: ES

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210224

26N No opposition filed

Effective date: 20211125

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210224

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210224

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20210831

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20210803

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210831

Ref country code: IT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210224

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210831

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210624

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210803

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210803

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210803

Ref country code: BE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210831

REG Reference to a national code

Ref country code: AT

Ref legal event code: MM01

Ref document number: 1364529

Country of ref document: AT

Kind code of ref document: T

Effective date: 20210803

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: AT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210803

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO

Effective date: 20160803

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210224

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210224

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210224

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20250820

Year of fee payment: 10

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 20250828

Year of fee payment: 10

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210224