EP3146083B1 - Tôle d'acier doublement recuite a hautes caracteristiques mecaniques de resistance et de ductilite, procede de fabrication et utilisation de telles tôles - Google Patents

Tôle d'acier doublement recuite a hautes caracteristiques mecaniques de resistance et de ductilite, procede de fabrication et utilisation de telles tôles Download PDF

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Publication number
EP3146083B1
EP3146083B1 EP15730241.5A EP15730241A EP3146083B1 EP 3146083 B1 EP3146083 B1 EP 3146083B1 EP 15730241 A EP15730241 A EP 15730241A EP 3146083 B1 EP3146083 B1 EP 3146083B1
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Prior art keywords
metal sheet
temperature
rolled
annealing
cold
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EP15730241.5A
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German (de)
English (en)
French (fr)
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EP3146083A1 (fr
Inventor
Artem ARLAZAROV
Jean-Christophe HELL
Frédéric KEGEL
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ArcelorMittal SA
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ArcelorMittal SA
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Priority to PL15730241T priority Critical patent/PL3146083T3/pl
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0405—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing of ferrous alloys
    • C—CHEMISTRY; METALLURGY
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/0463—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 following hot rolling
    • C—CHEMISTRY; METALLURGY
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/0478—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 involving a particular surface treatment
    • C—CHEMISTRY; METALLURGY
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/0478—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 involving a particular surface treatment
    • C21D8/0489—Application of a tension-inducing coating
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
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    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
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    • 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
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    • 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
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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    • 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
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • 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
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
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    • 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
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • C23C2/0224—Two or more thermal pretreatments
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    • 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
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    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
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    • C23C2/26—After-treatment
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    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
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    • C23F—NON-MECHANICAL REMOVAL OF METALLIC MATERIAL FROM SURFACE; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL; MULTI-STEP PROCESSES FOR SURFACE TREATMENT OF METALLIC MATERIAL INVOLVING AT LEAST ONE PROCESS PROVIDED FOR IN CLASS C23 AND AT LEAST ONE PROCESS COVERED BY SUBCLASS C21D OR C22F OR CLASS C25
    • C23F17/00—Multi-step processes for surface treatment of metallic material involving at least one process provided for in class C23 and at least one process covered by subclass C21D or C22F or class C25
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the present invention covers the manufacture of double-annealed steels with high strength, simultaneously having a mechanical strength and a deformation capacity for carrying out cold forming operations.
  • the invention more specifically relates to steels having a mechanical strength greater than or equal to 980 MPa, having a yield strength greater than or equal to 650 MPa, a uniform elongation greater than or equal to 15%, an elongation at break greater than or equal to 20%.
  • the microstructure of this steel comprises in terms of surface proportions 0-10% of ferrite, 0-10% of martensite, and 60-95% of martensite returned and containing, in proportions determined by X-ray diffraction: 5-20% d residual austenite. Nevertheless, the ductilities achieved by the steels according to this invention are low and it affects the shaping of the piece from the product obtained from the teachings of this application.
  • the microstructure of this steel has a TRIP effect with a high content of metastable residual austenite which suppresses the pre-cracks and their propagation because of plastic de-stressing and martensite formation during transformation from austenite
  • This article discloses a method for the production of steels with excellent resistance-ductility trade-offs, but the chemical compositions disclosed as well as the methods of production are not only not compatible with industrial production but they will give rise to difficulties of coating.
  • the object of the present invention is to solve the problems mentioned above. It aims to provide a cold-rolled steel having a mechanical strength greater than or equal to 980 MPa, a yield strength greater than or equal to 650 MPa together with a uniform elongation greater than or equal to 15%, a higher breaking elongation or equal to 20% and its manufacturing process.
  • the invention also aims to provide a steel with an ability to be produced stably.
  • the subject of the invention is a steel sheet whose composition comprises, the contents being expressed as a percentage of the weight, 0.20% ⁇ C ⁇ 0.40%, preferentially 0.22% ⁇ C ⁇ 0 , 32%, 0.8% ⁇ Mn ⁇ 1.4%, preferably 1.0% ⁇ Mn ⁇ 1.4%, 1.60% ⁇ Si ⁇ 3.00%, preferentially 1.8% ⁇ Si ⁇ 2 , 5%, 0.015 ⁇ Nb ⁇ 0.150%, preferably 0.020% ⁇ Nb ⁇ 0.13%, Al ⁇ 0.1%, Cr ⁇ 1.0%, preferentially Cr ⁇ 0.5%, S ⁇ 0.006%, P ⁇ 0.030%, Ti ⁇ 0.05%, V ⁇ 0.05%, Mo ⁇ 0.03%, B ⁇ 0.003%, N ⁇ 0.01%, the remainder of the composition consisting of iron and unavoidable impurities resulting from the elaboration, the microstructure being constituted, in surface proportions, of 10 to 30% residual austenite
  • the steel sheet according to the invention comprises a coating of zinc or zinc alloy or a coating of Al or Al alloy.
  • These coatings may or may not be alloyed with iron, it will be called galvanized sheet (GI / GA)
  • the sheets according to the invention have a mechanical behavior such that the mechanical strength is greater than or equal to 980 MPa, the elastic limit is greater than or equal to 650 MPa, the uniform elongation greater than or equal to 15% and the elongation at break greater than or equal to 20%.
  • a so-called base annealing of said wound hot-rolled sheet is carried out before cold rolling so that the sheet is heated and then maintained at a temperature of between 400 ° C. and 700 ° C. for a period of between and 24 hours,
  • the sheet is maintained at the end of cooling temperature T OA isothermally between 420 and 480 ° C between 5 and 120 seconds.
  • the double annealed cold-rolled sheet is then cold-rolled with a cold rolling ratio of between 0.1 and 3% before depositing a coating.
  • the doubly annealed sheet is finally heated to a holding temperature T base of between 150 ° C and 190 ° C for a hold time t basis between 10h and 48h.
  • the sheet is coated by dipping in a liquid bath of one of the following elements: Al, Zn, Al alloy or Zn alloy.
  • the sheet according to the invention cold-rolled, doubly annealed and coated, or manufactured by a method according to the invention is used for the manufacture of parts for land motor vehicles.
  • the carbon content by weight, is between 0.20 and 0.40%. If the carbon content of the invention is below 0.20% by weight, the mechanical strength becomes insufficient and the residual austenite fraction is still insufficient and not stable enough to achieve a uniform elongation greater than 15%. Beyond 0.40%, the weldability becomes more and more reduced because low-tenacity microstructures are formed in the heat-affected zone (ZAT) or in the melted zone in the case of resistance welding. In a preferred embodiment, the carbon content is between 0.22 and 0.32%. Within this range, the weldability is satisfactory, the stabilization of the austenite is optimized and the fresh martensite fraction is within the target range of the invention.
  • Manganese is, according to the invention between 0.8 and 1.4%, it is a hardening element with a solid solution of substitution, it stabilizes the austenite and lowers the transformation temperature Ac3. Manganese therefore contributes to an increase in mechanical strength. According to the invention, a a minimum of 0.8% by weight is necessary to obtain the desired mechanical properties. However, beyond 1.4%, its gammagenic character leads to a slowing down of the bainitic transformation kinetics taking place during the maintenance at the end of cooling temperature T OA and the bainite fraction is still insufficient to reach a resistance. elasticity greater than 650 MPa.
  • a range of manganese content of between 1.0% and 1.4% is chosen, thus combining a satisfactory mechanical strength without increasing the risk of reducing the bainite fraction and thus reducing the elastic resistance, neither increase quenchability in welded alloys, which would adversely affect the weldability of the sheet according to the invention.
  • the silicon must be between 1.6 and 3.0%. In this range, the stabilization of the residual austenite is made possible by the addition of silicon, which considerably slows the precipitation of the carbides during the annealing cycle and more particularly during the bainitic transformation. This is because the solubility of silicon in cementite is very low and this element increases the carbon activity in the austenite. Any formation of cementite will therefore be preceded by a step of rejection of Si at the interface. The enrichment of carbon austenite therefore leads to its stabilization at room temperature on the double-annealed and coated steel sheet. Subsequently, the application of an external constraint, shaping for example, will lead to the transformation of this austenite martensite. This transformation has the result of also improving the resistance to damage.
  • Silicon is also a strongly hardening element with a solid solution and thus makes it possible to achieve the elastic and mechanical resistances targeted by the invention.
  • an addition of silicon in an amount greater than 3.0% will substantially promote the ferrite and the target strength would not be reached, in addition strongly adherent oxides would form which would lead to defects surface and non-adherence of the Zinc or Zinc alloy coating.
  • the minimum content must also be set at 1.6% by weight to obtain the stabilizing effect on the austenite. So preferentially, the silicon content will be between 1.8 and 2.5% in order to optimize the aforementioned effects.
  • the chromium content must be limited to 1.0%, this element makes it possible to control the formation of pro-eutectoid ferrite during cooling during annealing from said holding temperature T soaking1 or T soaking2 , because this ferrite, in a high quantity decreases the mechanical strength required for the sheet according to the invention.
  • This element also makes it possible to harden and refine the bainitic microstructure. However, this element considerably slows down the kinetics of bainitic transformation. However, for contents above 1.0%, the bainite fraction is still insufficient to reach a yield strength greater than 650 MPa.
  • Nickel and copper have effects substantially similar to that of manganese. These two elements will be in residual contents namely 0.05% for each element but only because their costs are much higher than that of manganese.
  • the aluminum content is limited to 0.1% by weight, this element is a powerful alphagene favoring the formation of ferrite.
  • a high aluminum content would increase the Ac3 point and thus make the industrial process expensive in terms of energetic annealing.
  • high levels of aluminum increase the erosion of refractories and the risk of clogging of the nozzles during the casting of the steel upstream of the rolling.
  • aluminum segregates negatively and, it can lead to macro-segregations. In excessive amounts, aluminum reduces hot ductility and increases the risk of defects in continuous casting. Without a strong control of the casting conditions, micro and macro segregation defects ultimately result in central segregation on the annealed steel sheet. This central band will be harder than its surrounding matrix and will damage the formability of the material.
  • the sulfur must be less than 0.006%, beyond which the ductility is reduced due to the excessive presence of sulphides such as MnS, so-called manganese sulphides, which reduce the ability to deform.
  • Phosphorus should be less than 0.030%, it is a hardening element in solid solution but significantly reduces spot weldability and hot ductility, particularly because of its ability to segregate at grain boundaries or its tendency to co-segregation with manganese. For these reasons, its content should be limited to 0.030% in order to obtain a good spot welding ability.
  • the niobium must be between 0.015 and 0.150%, it is a micro-alloy element which has the particularity of forming precipitates hardening with carbon and / or nitrogen. These precipitates, already present during the hot rolling operation, delay the recrystallization during annealing and thus refine the microstructure, which contributes to the hardening of the material. It also makes it possible to improve the elongation properties of the product, by allowing high temperature annealing without lowering the elongation performance by a refinement effect of the structures.
  • the niobium content must nevertheless be limited to 0.150% to avoid excessively high hot rolling forces.
  • the niobium content must be greater than or equal to 0.015%, which makes it possible to harden the ferrite when it is present and such hardening is sought and also a sufficiently important refinement for greater stabilizing the residual austenite and thus ensuring a uniform elongation in the scope of the invention, preferably the Nb content is between 0.020 and 0.13 to optimize the aforementioned effects.
  • micro-alloy elements such as titanium and vanadium are limited to a maximum content of 0.05% because these elements have the same advantages as niobium but they have the particularity of reducing the ductility of the product more strongly.
  • the nitrogen is limited to 0.01% in order to avoid phenomena of aging of the material and to minimize the precipitation of aluminum nitrides (AlN) during solidification and thus to weaken the semi-finished product.
  • Boron and molybdenum are at levels of impurities or, at levels individually lower than 0.003 for boron and 0.03 for Mo.
  • the rest of the composition consists of iron and unavoidable impurities resulting from the elaboration.
  • the microstructure of the steel after the first annealing must contain, in surface proportion, less than 10% of polygonal ferrite, the remainder of the microstructure being composed of fresh or returned martensite. If the polygonal ferrite content is greater than 10%, the strength and yield strength of the steel after the second annealing will be less than 980 MPa and 650 MPa respectively. In addition, a polygonal ferrite content greater than 10% after the first annealing will result in a polygonal ferrite content at the end of the second annealing greater than 10% which would lead to a yield strength and too much mechanical strength. low compared to the scope of the invention.
  • the microstructure of the steel after the second annealing must contain, in surface proportions, 10 to 30% residual austenite. If the residual austenite content is less than 10%, the uniform elongation will be less than 15% because the residual austenite will be too stable and can not be transformed into martensite during mechanical stresses bringing a significant gain on the work hardening. the steel actually delays the appearance of the necking which results in an increase of the uniform elongation.
  • the residual austenite content is greater than 30%, the residual austenite will be unstable because not sufficiently enriched in carbon during the second annealing and maintenance at the end of cooling temperature T OA , and the ductility of the steel after the Second annealing will be reduced, which will lead to a uniform elongation of less than 15% and / or a total elongation of less than 20%.
  • the steel according to the invention after the second annealing must contain, in surface proportions, from 30 to 60% of annealed martensite, which is a martensite resulting from the first annealing, annealed during the second annealing and which is distinguished from a fresh martensite by a smaller quantity of crystallographic defects, and which is distinguished from a martensite returned by the absence of carbides within its laths. If the annealed martensite content is less than 30%, the ductility of the steel will be too low because the residual austenite content will be too low because not enough enriched in carbon and the fresh martensite content will be too much this leads to a uniform elongation of less than 15%.
  • the ductility of the steel will be too low because the residual austenite will be too stable and can not be transformed into martensite under the effect of mechanical stresses, which will have the effect of to reduce the ductility of the steel according to the invention, and will lead to a uniform elongation of less than 15% and / or a total elongation of less than 20%.
  • the microstructure of the steel after the second annealing must contain, in surface proportions, from 5 to 30% of bainite.
  • the presence of bainite in the microstructure is justified by the role it plays in the carbon enrichment of the residual austenite. Indeed, during the bainitic transformation and thanks to the presence of silicon in significant amount, the carbon is redistributed from bainite to austenite which has the effect of stabilizing the latter at room temperature. If the bainite content is less than 5%, residual austenite will not be sufficiently enriched in carbon and the latter will not be stable enough, which will favor the presence of fresh martensite which will cause a significant decrease in ductility. The uniform elongation will then be less than 15%.
  • bainite content is greater than 30%, this will lead to a residual austenite which is too stable and can not be converted into martensite under the effect of mechanical stresses, which will lead to a uniform elongation of less than 15%. and / or a total elongation of less than 20%.
  • the steel according to the invention and after the second annealing must contain, in surface proportions, 10 to 30% fresh martensite. If the fresh martensite content is less than 10%, the strength of the steel will be less than 980 MPa. If it is greater than 30%, the residual austenite content will be too low and the steel will not be sufficiently ductile, moreover, the uniform elongation will be less than 15%.
  • the sheet according to the invention may be manufactured by any suitable method.
  • a steel of composition according to the invention is supplied. Then, one proceeds to the casting of a half-product from this steel. This casting can be carried out in ingots or continuously in the form of slabs.
  • the reheating temperature should be between 1100 and 1280 ° C.
  • the cast semifinished products must be heated to a temperature T rech at 1100 ° C to obtain a semi-finished product warmed in order to reach at any point a temperature favorable for the large deformations that the steel will undergo during rolling.
  • This temperature range also makes it possible to be in the austenitic range and to ensure complete dissolution of the precipitates resulting from the casting.
  • T rech is greater than 1280 ° C, the austenitic grains grow undesirably and will lead to a coarser final structure and the risks of surface defects related to the presence of liquid oxide are increased. It is of course also possible to hot roll directly after casting without heating the slab.
  • the semi-finished product is then hot-rolled in a temperature range in which the structure of the steel is totally austenitic: if the end-of-rolling temperature T f is less than 900 ° C., the rolling forces are very large and may cause significant energy consumption or even breakages of rolling mill. Preferably, a rolling end temperature greater than 950 ° C. will be observed in order to guarantee rolling in the austenitic range and thus to limit the rolling forces.
  • the hot-rolled product is then rolled at a temperature T bob of between 400 and 600 ° C.
  • T bob of between 400 and 600 ° C.
  • This temperature range makes it possible to obtain ferritic, bainitic or pearlitic transformations during the quasi-isothermal maintenance associated with the winding followed by slow cooling to minimize the martensite fraction after cooling.
  • a winding temperature above 600 ° C leads to the formation of unwanted surface oxides.
  • the winding temperature is too low, below 400 ° C, the hardness of the product after cooling is increased, which increases the efforts required during the subsequent cold rolling.
  • the hot-rolled product is then cleaned if necessary by a process known per se.
  • This heat treatment makes it possible to have a mechanical strength of less than 1000 MPa at any point of the hot-rolled sheet, the difference in hardness between the center of the sheet and the banks thus being minimized. This greatly facilitates the next step of cold rolling by softening the formed structure.
  • the first annealing of the cold-rolled product is then carried out, preferably in a continuous annealing installation, with a mean heating rate V C of between 2 and 50 ° C. per second.
  • V C a mean heating rate
  • T soaking1 this heating rate range makes it possible to obtain a recrystallization and an adequate refinement of the structure.
  • Below 2 ° C per second the risks of surface decarburization are considerably increased.
  • Above 50 ° C per second traces of non-recrystallization and insoluble carbides would appear during the maintenance which would have the effect of reducing the residual austenite fraction and thus adversely affect the ductility.
  • T soaking1 is lower than TS1, it promotes the presence of polygonal ferrite beyond 10% and therefore outside the scope of the invention.
  • T soaking1 is above 950 ° C, the austenitic grain sizes increase considerably which is detrimental to the refinement of the final microstructure and therefore to the yield strength levels which would be below 650 MPa .
  • a holding time t soaking1 of between 30 and 200 seconds at the temperature T soaking1 allows the dissolution of the previously formed carbides, and especially a sufficient transformation to austenite. Below 30 seconds the dissolution of the carbides would be insufficient. On the other hand, a holding time greater than 200 s is hardly compatible with productivity requirements. continuous annealing installations, in particular the speed of travel of the reel. In addition, the same risk of austenitic grain enlargement as in the case of T soaking1 above 950 ° C appears, with the same risk of having a yield strength of less than 650 MPa. The duration of maintenance t soaking1 is therefore between 30 and 200 s.
  • the sheet is cooled to room temperature, the cooling rate V ref1 being fast enough to prevent the formation of ferrite.
  • this cooling rate is greater than 30 ° C./s, which makes it possible to obtain a microstructure with less than 10% ferrite, the rest being martensite.
  • a fully martensitic microstructure will be favored after the first annealing.
  • the second annealing of the cold-rolled product is then carried out and annealed a first time, preferably in a continuous galvanization annealing installation, with an average heating rate V C greater than 2 ° C. per second in order to avoid the risks of surface decarburization.
  • V C an average heating rate
  • the average heating rate must be less than 50 ° C per second to avoid the presence of insoluble carbides during maintenance which would have the effect of reducing the residual austenite fraction.
  • T soaking2 is less than Ac1, it is not possible to obtain the microstructure targeted by the invention since only the income from the martensite resulting from the first annealing would take place.
  • T soaking2 is greater than TS2 the annealed martensite content will be less than 30% which will favor the presence of a large amount of fresh degrading martensite de facto strongly the ductility of the product.
  • a holding time t soaking 2 of between 30 and 200 seconds at the soaking temperature T 2 allows the dissolution of the previously formed carbides, and especially sufficient transformation into austenite. Below 30 seconds the dissolution of the carbides may be insufficient.
  • a hold time greater than 200 s is hardly compatible with the productivity requirements of continuous annealing equipment, in particular the speed of travel of the reel.
  • the soaking time t soaking2 is therefore between 30 and 200 s.
  • this cooling rate is greater than 20 ° C per second.
  • the holding time t OA in the temperature range T OA1 (° C) to T OA2 (° C) must be between 5 and 120 seconds in order to allow the bainitic transformation and thus the stabilization of the austenite by carbon enrichment. of said austenite. It must also be greater than 5 s to ensure a bainite content according to the invention without which the yield strength would be less than 650 MPa. It must also be less than 120 seconds to limit the bainite content to 30% as referred to in the invention, otherwise the residual austenite content would be less than 10% and the ductility of the steel would be too low, which would be manifest by a uniform elongation of less than 15% and / or a total elongation of less than 20%.
  • the doubly annealed sheet is coated with a deposit of Zinc or Zinc alloy (the Zn content in mass percentage being predominant) by hot dip coating before cooling to room temperature.
  • Zinc or Zinc alloy the Zn content in mass percentage being predominant
  • zinc or zinc alloy may also be coated by any electrolytic or physicochemical process known in itself bare annealed sheet.
  • a coating based on aluminum or aluminum-based alloy (the Al content in weight percentage being the majority) can also be deposited by hot quenching.
  • a post annealing heat treatment is then preferably carried out on the cold-rolled and doubly annealed and coated sheet at a holding temperature T base of between 150 ° C. and 190 ° C. for a hold time t base of between 10h and 48h to improve the elasticity limit and the pliability.
  • This treatment will be called: post annealing base.
  • Table 1 shows the chemical composition of the steel used to manufacture the sheets of the examples.
  • Table 1 Chemical compositions (% wt) and critical temperatures Ae1, TS1 and TS2 being in ° C.
  • references D and E are not in accordance with the invention because their compositions are free of Niobium, which will limit the yield strength and the mechanical strength of the final sheet by the absence of precipitation hardening.
  • references D and E are not in accordance with the invention because their silicon contents are outside the target range. Beyond 3.00%, the silicon will promote a quantity of ferrite which is too great and the intended mechanical strength would not be reached. Below 1.60% by weight, the stabilization of residual austenite will not be large enough to achieve the desired ductility.
  • the reference E is not in accordance with the invention because the carbon content is lower than the target which will limit the final strength and ductility of the sheet.
  • the Mn content is too high, which will limit the final amount of bainite in the sheet, which will have the effect of limiting the ductility of the sheet by an excessive presence of fresh martensite.
  • References A5 to A6, B1 to B4, C2 to C5, D1 and D2, E1 to E6 of Table 2 denote steel sheets manufactured under conditions not in accordance with the invention from steels whose compositions are given in Table 1. The parameters not in accordance with the invention are underlined.
  • references A5, A6, B2 to B4, C2 to C4, D1 and D2 are not in accordance with the invention since the holding temperature at the first annealing T soaking1 is lower than the calculated temperature TS1, which would favor a large quantity of ferrite at the first annealing thus limiting the mechanical strength of the sheet after the second annealing.
  • references E2, E3 and E4 are not in accordance with the invention by their chemical composition and by the fact that the holding temperature at the second annealing T soaking2 is greater than the calculated temperature TS2, which will have the effect to reduce the amount of annealed martensite after the second annealing, limiting the final ductility of the sheet due to too much fresh martensite.
  • the reference B1 is not in accordance with the invention because the temperature T OA is outside the range 420 ° C - 480 ° C, which will limit the amount of residual austenite after the second annealing and therefore limit the ductility of the sheet.
  • the reference C5 is not in accordance with the invention because only a single annealing, in accordance with the invention and the claims of the second annealing, has been applied to the sheet.
  • the absence of the first annealing leads to the absence of martensite annealed in the microstructure which greatly limits the yield strength and the ultimate strength of the sheet.
  • the cooling rate at the second annealing V Ref2 is less than 30 ° C / s which promotes the formation of ferrite cooling, which will have the effect to reduce the elastic limit and the mechanical strength of the sheet.
  • Examples A1 to A4, C1 are those according to the invention.
  • the mechanical properties are then measured using an ISO 12.5 ⁇ 50 specimen and the contents of each of the phases present in the microstructures developed by cross section of the material from the chemical compositions given in Table 1 following the methods described in Table 2.
  • the uni-axial tractions to obtain these mechanical properties are made in the direction parallel to that of the rolling to cold.
  • References A5 and A6, B1 to B4, C2 to C5, D1 and D2, E1 to E6 of Table 3 denote steel sheets manufactured under conditions described in Table 2 from steels whose compositions are given in the table. 1. Mechanical properties and phase fractions not in accordance with the invention are underlined.
  • Examples A1 to A4 and C1 are those according to the invention.
  • references A5, A6, D1 and D2 are not in accordance with the invention because the elastic limit is less than 650 MPa, which is explained by a large amount of ferrite at the end of the first annealing and a small fraction of martensite annealed at the end of the second annealing, which is due to a holding temperature T soaking1 lower than the calculated temperature TS1.
  • references B2 to B4 and C2 to C4 are not in accordance with the invention because the mechanical strength is less than 980 MPa, which is explained by an amount of ferrite greater than 10% after the first annealing, which will limit the fresh martensite fraction at the end of the second annealing, which is due to a holding temperature T soaking1 lower than the calculated temperature TS1.
  • the B1 reference is not in accordance with the invention because the elastic limit is less than 650 MPa and the mechanical strength is less than 980 MPa, which is explained by a quantity of fresh martensite too low to the result of the second annealing, which is due to an end-of-cooling temperature T OA of less than 420 ° C.
  • references E1 to E6 are not in accordance with the invention since the elastic limit is less than 650 MPa and the mechanical strength is less than 980 MPa.
  • the non-compliance of these examples reflects an unsuitable chemical composition, in particular the content of elements that harden too low (carbon, silicon) and the lack of precipitation hardening due to the absence of Niobium. This effect is all the more marked for the references E2 to E6, because the process with respect to the invention has not been respected and the quantities of phases obtained are outside the target ranges.
  • the invention also makes it possible to provide a steel sheet capable of depositing a coating of Zinc or Zn alloy, in particular by a hot-quenching process in a liquid Zn bath followed or not by a heat treatment of alliation.
  • the steel sheets according to the invention will be used with advantage for the manufacture of structural parts, reinforcing elements, security, anti abrasive or transmission discs for applications in land motor vehicles.

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US20170101695A1 (en) 2017-04-13
KR20170002652A (ko) 2017-01-06
US10995386B2 (en) 2021-05-04
MX2016014990A (es) 2017-03-31
PL3146083T3 (pl) 2019-05-31
HUE039794T2 (hu) 2019-02-28
JP6433512B2 (ja) 2018-12-05
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KR101846116B1 (ko) 2018-04-05
UA114877C2 (uk) 2017-08-10
RU2667947C2 (ru) 2018-09-25
MA39417A1 (fr) 2017-04-28
KR20170126512A (ko) 2017-11-17
RU2016149784A (ru) 2018-06-21
CN106604999A (zh) 2017-04-26
BR112016026883B1 (pt) 2021-02-09
TR201815496T4 (tr) 2018-11-21
CA2949855C (fr) 2018-05-01
MA39417B1 (fr) 2017-12-29
CN106604999B (zh) 2018-04-10
EP3146083A1 (fr) 2017-03-29
WO2015177615A1 (fr) 2015-11-26
WO2015177582A1 (fr) 2015-11-26
CA2949855A1 (fr) 2015-11-26
KR101987572B1 (ko) 2019-06-10
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