EP2171112B1 - Verfahren zur herstellung eines stahlblechs mit sehr hohen festigkeits- und biegbarkeitseigenschaften und in diesem verfahren hergestellte bleche - Google Patents

Verfahren zur herstellung eines stahlblechs mit sehr hohen festigkeits- und biegbarkeitseigenschaften und in diesem verfahren hergestellte bleche Download PDF

Info

Publication number
EP2171112B1
EP2171112B1 EP08830766A EP08830766A EP2171112B1 EP 2171112 B1 EP2171112 B1 EP 2171112B1 EP 08830766 A EP08830766 A EP 08830766A EP 08830766 A EP08830766 A EP 08830766A EP 2171112 B1 EP2171112 B1 EP 2171112B1
Authority
EP
European Patent Office
Prior art keywords
steel
sheet
steel sheet
composition
hot
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
EP08830766A
Other languages
English (en)
French (fr)
Other versions
EP2171112A1 (de
Inventor
Pascal Drillet
Damien Ormston
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.)
ArcelorMittal France SA
Original Assignee
ArcelorMittal France SA
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 ArcelorMittal France SA filed Critical ArcelorMittal France SA
Priority to EP08830766A priority Critical patent/EP2171112B1/de
Priority to PL08830766T priority patent/PL2171112T3/pl
Publication of EP2171112A1 publication Critical patent/EP2171112A1/de
Application granted granted Critical
Publication of EP2171112B1 publication Critical patent/EP2171112B1/de
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • 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 by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—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
    • 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
    • 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
    • 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
    • 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
    • C23C2/024—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by cleaning or etching
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/12—Aluminium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D2211/002—Bainite
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12736—Al-base component
    • Y10T428/1275—Next to Group VIII or IB metal-base component
    • Y10T428/12757—Fe
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12785—Group IIB metal-base component
    • Y10T428/12792—Zn-base component
    • Y10T428/12799—Next to Fe-base component [e.g., galvanized]

Definitions

  • the invention relates to the manufacture of sheets or hot-rolled parts of so-called "multiphase" steels, simultaneously having a very high strength and a deformation capacity for performing cold or warm shaping operations.
  • the invention more specifically relates to predominantly bainitic microstructure steels having a strength greater than 800 MPa and an elongation rate greater than 10% rupture.
  • the automotive industry is in particular a preferred field of application for these hot-rolled steel sheets.
  • TRIP Transform Induced Plasticity
  • JP 2003 321739 A discloses a steel sheet with high characteristics of strength and ductility and the method of manufacturing this sheet.
  • the sheet composition comprises, the contents being expressed by weight: 0.03-0.1% C, 0.5-1.7% Mn, 0-0.1% Al, 0-2% Si, 0.1-0.5% Mo, 0-0.01% S, 0 -0.06% P, 0-0.006% N, 0.01-0.15% V, 0.007-0.2% Ti, 0.005-0.02% Nb, remains Fe and unavoidable impurities resulting from the elaboration.
  • the microstructure is composed of 5-70% bainite, the rest being essentially ferrite.
  • the present invention aims to solve the problems mentioned above. It aims to provide a hot-rolled steel sheet having a mechanical strength greater than 800 MPa together with an elongation rate greater than 10% fracture, both in long direction and in cross-direction relative to the rolling .
  • the invention also aims at providing a steel sheet that is not very sensitive to damage during cutting by a mechanical method.
  • the invention also aims to provide a method of manufacturing a steel sheet in the uncoated, electrogalvanized or galvanized, or aluminized state. This therefore requires that the mechanical characteristics of this steel are insensitive to the thermal cycles associated with continuous dipping zinc coating processes.
  • the invention also aims to have a sheet or piece of hot rolled steel available even in small thickness, that is to say for example between 1 and 5mm.
  • the hot hardness of the steel must not be too high to facilitate rolling.
  • composition of the steel preferably comprises the content being expressed by weight: 0.050% ⁇ C ⁇ 0.070%
  • the composition comprises, the content being expressed by weight: 0.070% ⁇ C ⁇ 0.090%
  • the composition comprises: 1.4% ⁇ Mn ⁇ 1.8%.
  • the composition comprises: 0.020% ⁇ Al ⁇ 0.040%.
  • the composition of the steel preferably comprises: 0.12% ⁇ V ⁇ 0.16%. In a preferred embodiment, the composition of the steel comprises 0.18% ⁇ Mo ⁇ 0.30%.
  • the composition comprises: Nb ⁇ 0.005%
  • the composition comprises: 0.20% ⁇ Cr ⁇ 0.45%
  • the sheet or the part is coated with a coating based on zinc or aluminum-based.
  • the subject of the invention is also a piece of steel with a composition and a microstructure defined above, characterized in that it is obtained by heating at a temperature T of between 400 and 690 ° C. and then a warm stamping in a temperature range between 350 ° C and (T-20 ° C), then a subsequent cooling to room temperature.
  • the invention also relates to a beam welded assembly with high energy density made from a sheet or piece of steel in one of the modes above.
  • the invention also relates to a method of manufacturing a sheet or piece of hot-rolled steel with a resistance greater than 800 MPa, elongation at break greater than 10%, according to which a steel of the above composition is supplied, a semi-product is cast which is heated to a temperature above 1150 ° C.
  • the semi-finished product is hot rolled to a temperature T FL in a temperature range where the microstructure of the steel is entirely austenitic so as to obtain a sheet.
  • This is then cooled to a cooling rate V R of 75 and 200 ° C./s, then the sheet is reeled at a temperature T bob of between 500 and 600 ° C.
  • the end of rolling temperature T FL is between 870 and 930 ° C.
  • the cooling rate V R is between 80 and 150 ° C / s.
  • the sheet is pickled, then optionally skin-passed, and then coated with zinc or zinc alloy.
  • the coating is carried out continuously by dipping.
  • the subject of the invention is also a process for manufacturing a hot-stamped part, according to which a steel sheet is supplied according to one of the above characteristics, or manufactured by a method according to one of the above-mentioned characteristics. above, then cutting said sheet to obtain a blank.
  • the blank is heated partially or completely to a temperature T of between 400 and 690 ° C., where a holding time of less than 15 minutes is carried out so as to obtain a heated blank, and then the blank heated to a temperature is pressed. between 350 and T-20 ° C to obtain a piece that is cooled to room temperature with a speed V ' R
  • the speed V ' R is between 25 and 100 ° C / s.
  • the invention also relates to the use of a hot-rolled steel sheet according to one of the above modes, or manufactured by a method according to one of the above modes for the manufacture of parts of structure or reinforcement elements, in the automotive field.
  • carbon plays an important role in the formation of the microstructure and in the mechanical properties.
  • the carbon content is between 0.050 and 0.090% by weight: Below 0.050%, sufficient strength can not be obtained. Beyond 0.090%, the microstructure formed consists mainly of lower bainite, this structure being characterized by the presence of carbides precipitated within bainitic ferrite slats: the mechanical strength thus obtained is high but the elongation is then significantly reduced.
  • the carbon content is between 0.050 and 0.070%.
  • the figure 1 illustrates the influence of carbon content on the long-term elongation of LASER beam splicing welds: a particularly high elongation at break of 17-23% is associated with a carbon content of 0.050 at 0.070%.
  • the carbon content is greater than 0.070% and less than or equal to 0.090%: even if this range does not lead to such a high ductility, the elongation at break of the LASER welds is greater than 15% and remains comparable to that of the base steel sheet.
  • manganese increases the quenchability and avoids the formation of ferrite cooling after rolling.
  • Manganese also helps to deoxidize steel during liquid phase processing.
  • the addition of manganese also contributes to effective solid solution hardening and increased strength.
  • the manganese is between 1.4 and 1.8%: thus forming a completely bainitic structure without risk of appearance of harmful band structure.
  • aluminum is an effective element for the deoxidation of steel. This efficiency is obtained in a particularly economical and stable manner when the aluminum content is between 0.020 and 0.040%.
  • silicon contributes to liquid phase deoxidation and hardening in solid solution.
  • An addition of silicon above 0.3% causes the formation of strongly adherent oxides and the possible appearance of surface defects, due in particular to a lack of wettability in dip galvanizing operations.
  • molybdenum retards bainitic transformation during cooling after rolling, contributes to hardening by solid solution and refines the size of bainitic slats.
  • the molybdenum content is less than or equal to 0.40% to prevent the excessive formation of quenching structures. This limited molybdenum content also makes it possible to lower the manufacturing cost.
  • the molybdenum content is greater than or equal to 0.18% and less than or equal to 0.30%. In this way, the level is ideally adjusted to avoid the formation of ferrite or perlite in the steel sheet on the cooling table after hot rolling.
  • Phosphorus is a known element to segregate at grain boundaries. Its content must be limited to 0.025% in order to maintain sufficient hot ductility.
  • the composition may comprise chromium in an amount of less than or equal to 0.45%. Thanks to the other elements of the composition and to the process according to the invention, its presence is however not absolutely necessary, which has the advantage of avoiding expensive additions.
  • chromium between 0.20 and 0.45% can be carried out in addition to the other elements increasing the quenchability: below 0.20%, the effect on the quenchability is not sufficiently marked. Above 0.45%, the coating can be reduced.
  • the steel contains less than 0.005% Ti and less than 0.020% Nb.
  • these elements fix too much nitrogen in the form of nitrides or carbonitrides. There is not enough nitrogen available to precipitate with vanadium. In addition, excessive precipitation of niobium would increase the hot hardness and would not easily allow the realization of thin-rolled hot-rolled sheets.
  • the niobium content is less than 0.005%
  • Vanadium is an important element according to the invention: the steel contains a vanadium content of between 0.12 and 0.22%. Compared to a vanadium-free steel, the increase in strength due to a hardening precipitation of carbonitrides can be up to 300 MPa. Below 0.12%, there is no significant effect on the mechanical tensile characteristics. Beyond 0.22% of vanadium, under the manufacturing conditions according to the invention, there is a saturation of the effect on the mechanical characteristics. A content of less than 0.22% thus makes it possible to obtain high mechanical characteristics in a very economical manner with respect to steels which contain higher levels of vanadium.
  • microstructure refinement and structural hardening are particularly effective.
  • the nitrogen content is greater than or equal to 0.003% in order to obtain a precipitation of vanadium carbonitrides in a sufficient quantity.
  • the nitrogen content is less than or equal to 0.009% to avoid the presence of solid solution nitrogen or the formation of larger carbonitrides, which would reduce ductility.
  • the rest of the composition consists of unavoidable impurities resulting from the preparation, such as for example Sb, Sn, As.
  • microstructural percentages above are surface fractions that can be measured on polished and etched sections.
  • the microstructure therefore does not include primary or proeutectoid ferrite: it then has a great homogeneity since the difference in mechanical properties between the matrix (upper bainite) and the other possible constituents (lower bainite and martensite) is small. During a mechanical stress, the deformations are distributed homogeneously. Accumulation of dislocations does not occur at the interfaces between the constituents and premature damage is avoided, as opposed to this can be noted in structures with a significant amount of primary ferrite, phase whose flow limit is very low, or martensite with a very high level of resistance. In this way, the steel sheet according to the invention has a particular aptitude for certain demanding deformation modes such as the expansion of holes, the mechanical stressing of cut edges, folding.
  • the cast semifinished products are first brought to a temperature higher than 1150 ° C. to reach at any point a temperature favorable to the high deformations which the steel will undergo during rolling.
  • the hot rolling step of these semi-finished products starting at more than 1150 ° C. can be done directly after casting. that an intermediate heating step is not necessary in this case.
  • the semi-finished product is hot-rolled in a temperature range where the structure of the steel is totally austenitic up to an end-of-rolling temperature T FL .
  • the temperature T FL is preferably between 870 and 930 ° C to obtain a grain size adapted to the bainitic transformation that follows.
  • Cooling is then carried out at a speed V R of between 75 and 200 ° C./s: a minimum speed of 75 ° C./s makes it possible to avoid the formation of proeutectoid ferrite and of perlite, whereas a lower speed V R or 200 ° C / s avoids excessive formation of martensite.
  • the speed V R is between 80 and 150 ° C / s:
  • a minimum speed of 80 ° C / s leads to the formation of upper bainite with a very small slat size, combined with excellent mechanical properties.
  • a speed of less than 150 ° C / s makes it possible to avoid, for the most part, the formation of martensite.
  • the sheet can be used in the bare state or coated.
  • the coating may be for example a coating based on zinc or aluminum.
  • the sheet is scoured after rolling according to a method known per se, so as to obtain a surface state suitable for promoting the implementation of the subsequent coating.
  • the sheet may be subjected to a slight cold deformation, usually less than 1% ("skin-pass").
  • the sheet is then coated with zinc or aluminum.
  • a zinc-based alloy for example by electrogalvanizing or continuous galvanizing dipping.
  • electrogalvanizing or continuous galvanizing dipping it has been demonstrated that the particular microstructure of the steel, mainly composed of higher bainite, is not very sensitive to the thermal conditions of the subsequent galvanizing treatment, so that the mechanical characteristics of the sheets coated continuously with dipping have a great stability even in case of untimely fluctuation of these conditions.
  • the sheet in the galvanized state therefore has mechanical characteristics very similar to those in the naked state.
  • the sheets are then cut by methods known in themselves from in order to obtain blanks suitable for shaping.
  • the microstructure of steel I1 illustrated in figure 2 comprises more than 80% higher bainite, the remainder being lower bainite and MA compounds.
  • the total content of martensite and residual austenite is less than 5%.
  • the size of the old austenitic grains and bainitic batten bundles is about 10 microns.
  • the limitation of the size of the batten packets and the strong disorientation between the adjacent packets results in a high resistance to the propagation of any microcracks. Due to the small difference in hardness between the various constituents of the microstructure, the steel is not very sensitive to damage during cutting by a mechanical process.
  • the steel sheet R1 having a carbon content too high and a vanadium content too low, has an elongation insufficient rupture.
  • the R2 steel has a carbon content and phosphorus too high, its winding temperature is also too low. As a result, its elongation at break is also significantly less than 10%.
  • LASER autogenous welded joints were made under the following conditions: power: 4.5kW, welding speed: 2.5m / min.
  • the lengthwise elongation of the LASER welds of I-1 steel is 17%, whereas it is 10 and 13% respectively for the R-1 and R-2 steels. These values lead, particularly for steel R1, to difficulties in stamping welded joints.
  • Steel sheets I1 according to the invention were also galvanized under the following conditions: after heating at 680 ° C., the sheets were cooled to 455 ° C. and then quenched continuously in a Zn bath at this temperature and finally cooled to room temperature.
  • a steel sheet I-1 manufactured using the parameters defined in Table 2 for this steel, was cut to obtain blanks. After heating at temperatures of 400 ° C. or 690 ° C., held at these temperatures for 7 or 10 minutes and hot-drawing at temperatures of 350 ° C. or 640 ° C. respectively, the parts obtained were cooled to a speed V 'R 25 ° C / sec 100 ° C / s to room temperature.
  • the speed V ' R denotes the average speed of cooling between the temperature T and the ambient temperature.
  • the mechanical strength Rm of the parts thus obtained is indicated in Table 4: Table 4: Resistance Rm obtained after hot stamping under various conditions Cooling 25 ° C / s 100 ° C / s cooling Heating: 400 ° C- 7 minutes 880 MPa 875MPa Heating: 400 ° C- 10 minutes 875 MPa 885MPa Heating: 690 ° C-10 minutes 810MPa 810MPa
  • the stamped parts according to the conditions of the invention thus have a low sensitivity to a variation of the manufacturing conditions: after heating at 400 ° C., the final resistance varies little (10 MPa) when the duration of the heating and / or the speed of the cooling are modified.
  • the resistance of the piece obtained is greater than 800 MPa.
  • the invention allows the manufacture of laminations or pieces of bainitic matrix steels without excessive addition of expensive elements. These combine high strength and high ductility.
  • the steel sheets according to the invention are used profitably for the manufacture of structural parts or reinforcement elements in the automotive field and general industry.

Landscapes

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

Claims (18)

  1. Warmgewalztes Stahlblech oder -teil mit einer Festigkeit von mehr als 800 MPa, einer Reißdehnung von mehr als 10%, wobei dessen Zusammensetzung die folgenden Gehalte, ausgedrückt nach Gewicht, umfasst:
    0,050 % ≤ C ≤ 0,090 %
    1 % ≤ Mn ≤ 2 %
    0,015 % ≤ Al ≤ 0,050 %
    0,1 % ≤ Si ≤ 0,3 %
    0,10 % ≤ Mo ≤ 0,40 %
    S ≤ 0,010 %
    P ≤ 0,025 %
    0,003 % ≤ N ≤ 0,009 %
    0,12 % ≤ V ≤ 0,22 %
    Ti ≤ 0,005 %
    Nb ≤ 0,020 %
    und, möglicherweise,
    Cr ≤ 0,45 %
    wobei Eisen und unvermeidbare herstellungsbedingte Verunreinigungen den Rest der Zusammensetzung ausmachen, wobei die Mikrostruktur des Blechs oder des Teils, nach Oberflächenanteilen, mindestens 80 % an oberem Bainit umfasst, wobei der ergänzende Anteil gegebenenfalls aus unterem Bainit, Martensit und Restaustenit besteht, wobei die Summe der Gehalte an Martensit und an Restaustenit geringer als 5 % ist.
  2. Stahlblech oder Teil nach Anspruch 1, dadurch gekennzeichnet, dass die Zusammensetzung des Stahls Folgendes umfasst, wobei der Gehalt nach Gewicht ausgedrückt ist:
    0,050 % ≤ C ≤ 0,070 %
  3. Stahlblech oder Teil nach Anspruch 1, dadurch gekennzeichnet, dass die Zusammensetzung des Stahls Folgendes umfasst, wobei der Gehalt nach Gewicht ausgedrückt ist:
    0,070 % < C ≤ 0,090 %
  4. Stahlblech oder Teil nach einem beliebigen der Ansprüche 1 bis 3, dadurch gekennzeichnet, dass die Zusammensetzung des Stahls Folgendes umfasst, wobei der Gehalt nach Gewicht ausgedrückt ist:
    1,4 % ≤ Mn ≤1,8 %
  5. Stahlblech oder Teil nach einem beliebigen der Ansprüche 1 bis 4, dadurch gekennzeichnet, dass die Zusammensetzung des Stahls Folgendes umfasst, wobei der Gehalt nach Gewicht ausgedrückt ist:
    0,020 % ≤ Al ≤ 0,040 %
  6. Stahlblech oder Teil nach einem beliebigen der Ansprüche 1 bis 5, dadurch gekennzeichnet, dass die Zusammensetzung des Stahls Folgendes umfasst, wobei der Gehalt nach Gewicht ausgedrückt ist:
    0,12 % ≤ V ≤ 0,16 %
  7. Stahlblech oder Teil nach einem beliebigen der Ansprüche 1 bis 6, dadurch gekennzeichnet, dass die Zusammensetzung des Stahls Folgendes umfasst, wobei der Gehalt nach Gewicht ausgedrückt ist:
    0,18 % ≤ Mo ≤ 0,30 %
  8. Stahlblech oder Teil nach einem beliebigen der Ansprüche 1 bis 7, dadurch gekennzeichnet, dass die Zusammensetzung des Stahls Folgendes umfasst, wobei der Gehalt nach Gewicht ausgedrückt ist:
    Nb ≤ 0,005 %
  9. Stahlblech oder Teil nach einem beliebigen der Ansprüche 1 bis 8, dadurch gekennzeichnet, dass die Zusammensetzung des Stahls Folgendes umfasst, wobei der Gehalt nach Gewicht ausgedrückt ist:
    0,20% ≤ Cr ≤ 0,45%
  10. Stahlblech oder -teil nach einem beliebigen der Ansprüche 1 bis 9, dadurch gekennzeichnet, dass das Blech oder das Teil mit einer Beschichtung auf Basis von Zink oder auf Basis von Aluminium beschichtet ist.
  11. Verfahren zur Herstellung eines warmgewalzten Stahlblechs mit einer Festigkeit von mehr als 800 MPa, einer Reißdehnung von mehr als 10 %, wobei
    - ein Stahl mit einer Zusammensetzung nach einem beliebigen der Ansprüche 1 bis 9 bereitgestellt wird,
    - ein Halbzeug aus diesem Stahl gegossen wird,
    - das Halbzeug auf eine Temperatur von mehr als 1150 °C gebracht wird,
    - das Halbzeug bis zu einer Temperatur TFL warmgewalzt wird, die in einem Temperaturbereich liegt, in welchem die Mikrostruktur des Stahls vollständig austenitisch ist, sodass ein Blech erhalten wird, woraufhin
    - das Blech derart abgekühlt wird, dass die Abkühlgeschwindigkeit VR im Bereich von 75 bis 200 °C/s liegt, woraufhin
    - das Blech bei einer Temperatur Tbob im Bereich von 500 bis 600 °C aufgewickelt wird.
  12. Verfahren zur Herstellung eines warmgewalzten Stahlblechs nach Anspruch 11, dadurch gekennzeichnet, dass die Endtemperatur des Walzvorgangs TFL im Bereich von 870 bis 930 °C liegt.
  13. Verfahren zur Herstellung eines warmgewalzten Stahlblechs nach Anspruch 11 oder 12, dadurch gekennzeichnet, dass die Abkühlgeschwindigkeit VR im Bereich von 80 bis 150°C/s liegt.
  14. Verfahren zur Herstellung, wobei ein Blech, das nach einem beliebigen der Ansprüche 11 bis 13 hergestellt ist, gebeizt und anschließend möglicherweise dressiert wird, woraufhin es mit Zink oder Zinklegierung oder auch mit Aluminium oder Aluminiumlegierung beschichtet wird.
  15. Verfahren zur Herstellung eines Stahlblechs nach Anspruch 14, dadurch gekennzeichnet, dass die Beschichtung im kontinuierlichen Schmelzbadverfahren durchgeführt wird.
  16. Verfahren zur Herstellung eines Teils, das bei mäßiger Wäremeeinwirkung tiefgezogen wurde, dadurch gekennzeichnet, dass
    - ein Stahlblech nach einem beliebigen der Ansprüche 1 bis 10 bereitgestellt oder mittels eines Verfahrens nach einem beliebigen der Ansprüche 11 bis 15 hergestellt wird, woraufhin
    - das Blech zugeschnitten wird, um einen Zuschnitt zu erhalten, woraufhin
    - der Zuschnitt teilweise oder vollständig auf eine Temperatur T im Bereich von 400 bis 690 °C erhitzt wird, bei welcher er weniger als 15 Minuten lang gehalten wird, sodass ein erhitzter Zuschnitt erhalten wird, woraufhin
    - der erhitzte Zuschnitt bei einer Temperatur im Bereich von 350 bis T-20 °C tiefgezogen wird, um ein Teil zu erhalten, woraufhin
    - das Teil mit einer Geschwindigkeit V'R bis auf Raumtemperatur abgekühlt wird.
  17. Herstellungsverfahren nach Anspruch 16, dadurch gekennzeichnet, dass die Geschwindigkeit V'R im Bereich von 25 bis 100 °C/s liegt.
  18. Verwendung eines warmgewalzten Stahlblechs nach einem beliebigen der Ansprüche 1 bis 10, oder welches nach einem beliebigen der Ansprüche 11 bis 17 hergestellt wurden, zur Herstellung von tragenden Teilen oder von Verstärkungselementen im Kraftfahrzeugwesen.
EP08830766A 2007-07-19 2008-07-09 Verfahren zur herstellung eines stahlblechs mit sehr hohen festigkeits- und biegbarkeitseigenschaften und in diesem verfahren hergestellte bleche Active EP2171112B1 (de)

Priority Applications (2)

Application Number Priority Date Filing Date Title
EP08830766A EP2171112B1 (de) 2007-07-19 2008-07-09 Verfahren zur herstellung eines stahlblechs mit sehr hohen festigkeits- und biegbarkeitseigenschaften und in diesem verfahren hergestellte bleche
PL08830766T PL2171112T3 (pl) 2007-07-19 2008-07-09 Sposób wytwarzania blach stalowych o dobrych własnościach wytrzymałościowych i plastycznych oraz blachy tak wytworzone

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
EP07290908A EP2020451A1 (de) 2007-07-19 2007-07-19 Verfahren zur Herstellung von Stahlblechen mit hoher Widerstandsfähigkeit und Duktilität und damit hergestellte Bleche
PCT/FR2008/000993 WO2009034250A1 (fr) 2007-07-19 2008-07-09 Procede de fabrication de tôles d'acier a hautes caracteristiques de resistance et de ductilite, et tôles ainsi produites
EP08830766A EP2171112B1 (de) 2007-07-19 2008-07-09 Verfahren zur herstellung eines stahlblechs mit sehr hohen festigkeits- und biegbarkeitseigenschaften und in diesem verfahren hergestellte bleche

Publications (2)

Publication Number Publication Date
EP2171112A1 EP2171112A1 (de) 2010-04-07
EP2171112B1 true EP2171112B1 (de) 2011-11-23

Family

ID=38775251

Family Applications (2)

Application Number Title Priority Date Filing Date
EP07290908A Withdrawn EP2020451A1 (de) 2007-07-19 2007-07-19 Verfahren zur Herstellung von Stahlblechen mit hoher Widerstandsfähigkeit und Duktilität und damit hergestellte Bleche
EP08830766A Active EP2171112B1 (de) 2007-07-19 2008-07-09 Verfahren zur herstellung eines stahlblechs mit sehr hohen festigkeits- und biegbarkeitseigenschaften und in diesem verfahren hergestellte bleche

Family Applications Before (1)

Application Number Title Priority Date Filing Date
EP07290908A Withdrawn EP2020451A1 (de) 2007-07-19 2007-07-19 Verfahren zur Herstellung von Stahlblechen mit hoher Widerstandsfähigkeit und Duktilität und damit hergestellte Bleche

Country Status (16)

Country Link
US (3) US20100221573A1 (de)
EP (2) EP2020451A1 (de)
JP (1) JP5298127B2 (de)
KR (5) KR20150123957A (de)
CN (1) CN101784688B (de)
AR (1) AR067594A1 (de)
AT (1) ATE534756T1 (de)
BR (1) BRPI0814514B1 (de)
CA (1) CA2694069C (de)
ES (1) ES2375429T3 (de)
MA (1) MA31525B1 (de)
PL (1) PL2171112T3 (de)
RU (1) RU2451764C2 (de)
UA (1) UA98798C2 (de)
WO (1) WO2009034250A1 (de)
ZA (1) ZA201000290B (de)

Families Citing this family (24)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101509102B (zh) * 2009-03-27 2011-01-05 攀钢集团研究院有限公司 热轧低碳冲压用钢及其生产方法
JP5672946B2 (ja) * 2010-10-22 2015-02-18 Ｊｆｅスチール株式会社 成形性および強度上昇能に優れた温間成形用薄鋼板およびそれを用いた温間成形方法
CN103249847B (zh) * 2010-11-10 2015-06-10 Posco公司 制造抗拉强度等级为590MPa、可加工性优异且力学性能偏差小的高强度冷轧/热轧TRIP钢的方法
WO2012127125A1 (fr) 2011-03-24 2012-09-27 Arcelormittal Investigatión Y Desarrollo Sl Tôle d'acier laminée à chaud et procédé de fabrication associé
PL2889395T3 (pl) * 2012-08-21 2018-03-30 Nippon Steel & Sumitomo Metal Corporation Materiał stalowy
CN103205636B (zh) * 2013-04-18 2015-08-26 内蒙古包钢钢联股份有限公司 低碳贝氏体连续屈服带钢的生产方法
KR101318060B1 (ko) * 2013-05-09 2013-10-15 현대제철 주식회사 인성이 향상된 핫스탬핑 부품 및 그 제조 방법
KR101716624B1 (ko) * 2013-09-10 2017-03-14 가부시키가이샤 고베 세이코쇼 프레스 성형품의 제조 방법 및 프레스 성형품
KR101753016B1 (ko) * 2013-09-18 2017-07-03 신닛테츠스미킨 카부시키카이샤 핫 스탬프 성형체 및 그 제조 방법
CA2935308C (en) * 2014-01-06 2018-09-25 Nippon Steel & Sumitomo Metal Corporation Hot-formed member and manufacturing method of same
MX2016008810A (es) 2014-01-06 2016-09-08 Nippon Steel & Sumitomo Metal Corp Acero y metodo para fabricarlo.
JP6177733B2 (ja) * 2014-01-28 2017-08-09 株式会社神戸製鋼所 加工硬化能が大きく一様伸びと溶接性に優れた低降伏比高強度鋼板およびその製造方法
EP2905348B1 (de) * 2014-02-07 2019-09-04 ThyssenKrupp Steel Europe AG Hochfestes Stahlflachprodukt mit bainitisch-martensitischem Gefüge und Verfahren zur Herstellung eines solchen Stahlflachprodukts
WO2016001710A1 (en) 2014-07-03 2016-01-07 Arcelormittal Method for producing a high strength coated steel having improved strength and ductility and obtained sheet
WO2016001700A1 (en) 2014-07-03 2016-01-07 Arcelormittal Method for producing a high strength steel sheet having improved strength, ductility and formability
WO2016001702A1 (en) 2014-07-03 2016-01-07 Arcelormittal Method for producing a high strength coated steel sheet having improved strength, ductility and formability
WO2016001706A1 (en) 2014-07-03 2016-01-07 Arcelormittal Method for producing a high strength steel sheet having improved strength and formability and obtained sheet
WO2016005780A1 (fr) 2014-07-11 2016-01-14 Arcelormittal Investigación Y Desarrollo Sl Tôle d'acier laminée à chaud et procédé de fabrication associé
WO2017012958A1 (de) * 2015-07-17 2017-01-26 Salzgitter Flachstahl Gmbh Verfahren zum herstellen eines warmbandes aus einem bainitischen mehrphasenstahl mit einer zn-mg-al-beschichtung und ein entsprechendes warmband
US10590615B2 (en) * 2016-06-28 2020-03-17 Vigor Industrial Llc Orthotropic deck
CN110643894B (zh) * 2018-06-27 2021-05-14 宝山钢铁股份有限公司 具有良好的疲劳及扩孔性能的超高强热轧钢板和钢带及其制造方法
WO2020065381A1 (en) 2018-09-28 2020-04-02 Arcelormittal Hot rolled steel sheet and a method of manufacturing thereof
CN114058942B (zh) * 2020-07-31 2022-08-16 宝山钢铁股份有限公司 一种扭力梁用钢板及其制造方法、扭力梁及其制造方法
CN112962021B (zh) * 2021-01-25 2022-06-10 唐山钢铁集团有限责任公司 激光拼焊后用于整体热冲压成形的强塑钢板及生产方法

Family Cites Families (19)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3807990A (en) * 1968-09-11 1974-04-30 Nippon Steel Corp Low-alloy high-tensile strength steel
SU1749307A1 (ru) * 1990-10-30 1992-07-23 Центральный научно-исследовательский институт черной металлургии им.И.П.Бардина Сталь
JP3015923B2 (ja) * 1991-06-04 2000-03-06 新日本製鐵株式会社 強靱鋼の製造方法
RU2016127C1 (ru) * 1991-06-22 1994-07-15 Эфрон Леонид Иосифович Сталь
US5545270A (en) * 1994-12-06 1996-08-13 Exxon Research And Engineering Company Method of producing high strength dual phase steel plate with superior toughness and weldability
JPH1096042A (ja) * 1996-09-24 1998-04-14 Sumitomo Metal Ind Ltd 表層部靭性の優れた高張力鋼板及びその製造方法
US6248191B1 (en) 1997-07-28 2001-06-19 Exxonmobil Upstream Research Company Method for producing ultra-high strength, weldable steels with superior toughness
ES2264572T3 (es) * 1997-07-28 2007-01-01 Exxonmobil Upstream Research Company Aceros soldables ultrarresistentes con una tenacidad excelente a temperaturas ultrabajas.
JP2000282175A (ja) * 1999-04-02 2000-10-10 Kawasaki Steel Corp 加工性に優れた超高強度熱延鋼板およびその製造方法
FR2807068B1 (fr) 2000-03-29 2002-10-11 Usinor Acier lamine a chaud a tres haute limite d'elasticite et resistance mecanique utilisable notamment pour la realisation de piece de vehicules automobiles
DE10130744A1 (de) 2001-06-26 2003-01-02 Carl Zeiss Vision Gmbh Verfahren zur Bestimmung des Gradienten nach Betrag und/oder Richtung eines skalaren Feldes und von Oberflächennormalen eines Objektes in einem Datenfeld
KR100627429B1 (ko) * 2001-10-04 2006-09-25 신닛뽄세이테쯔 카부시키카이샤 드로잉이 가능하고 형상 동결성이 우수한 고강도 박강판과 이를 제조하는 방법
JP3775341B2 (ja) * 2002-04-30 2006-05-17 Ｊｆｅスチール株式会社 加工性に優れた高張力熱延鋼板ならびにその製造方法および加工方法
JP4091894B2 (ja) 2003-04-14 2008-05-28 新日本製鐵株式会社 耐水素脆化、溶接性、穴拡げ性および延性に優れた高強度薄鋼板およびその製造方法
TWI248977B (en) * 2003-06-26 2006-02-11 Nippon Steel Corp High-strength hot-rolled steel sheet excellent in shape fixability and method of producing the same
KR101165168B1 (ko) 2003-09-30 2012-07-11 신닛뽄세이테쯔 카부시키카이샤 용접성과 연성이 우수한 고항복비 고강도 박강판 및 고항복비 고강도 용융 아연 도금 박강판 및 고항복비 고강도 합금화 용융 아연 도금 박강판과 그 제조 방법
CA2546003A1 (en) 2004-03-31 2005-10-13 Jfe Steel Corporation High-rigidity high-strength thin steel sheet and method for producing same
JP4358022B2 (ja) 2004-04-27 2009-11-04 シロキ工業株式会社 パワーウィンドの安全装置
US7648597B2 (en) * 2004-07-07 2010-01-19 Jfe Steel Corporation Method for manufacturing high tensile strength steel plate

Also Published As

Publication number Publication date
US20180148806A1 (en) 2018-05-31
ATE534756T1 (de) 2011-12-15
KR101892423B1 (ko) 2018-08-27
WO2009034250A1 (fr) 2009-03-19
EP2020451A1 (de) 2009-02-04
US10214792B2 (en) 2019-02-26
KR20180014843A (ko) 2018-02-09
US20150203932A1 (en) 2015-07-23
US10428400B2 (en) 2019-10-01
PL2171112T3 (pl) 2012-04-30
CN101784688B (zh) 2011-11-23
UA98798C2 (ru) 2012-06-25
RU2451764C2 (ru) 2012-05-27
KR20130010030A (ko) 2013-01-24
MA31525B1 (fr) 2010-07-01
KR20140044407A (ko) 2014-04-14
ZA201000290B (en) 2010-10-27
CN101784688A (zh) 2010-07-21
JP5298127B2 (ja) 2013-09-25
US20100221573A1 (en) 2010-09-02
KR20150123957A (ko) 2015-11-04
EP2171112A1 (de) 2010-04-07
CA2694069A1 (fr) 2009-03-19
BRPI0814514B1 (pt) 2019-09-03
ES2375429T3 (es) 2012-02-29
BRPI0814514A2 (pt) 2015-02-03
CA2694069C (fr) 2013-05-21
US20180163282A9 (en) 2018-06-14
AR067594A1 (es) 2009-10-14
JP2010533791A (ja) 2010-10-28
KR20100037147A (ko) 2010-04-08
RU2010105699A (ru) 2011-08-27

Similar Documents

Publication Publication Date Title
EP2171112B1 (de) Verfahren zur herstellung eines stahlblechs mit sehr hohen festigkeits- und biegbarkeitseigenschaften und in diesem verfahren hergestellte bleche
EP2155915B1 (de) Verfahren zur herstellung kaltgewalzter und geglühter stahlbleche von sehr hoher festigkeit und in diesem verfahren hergestellte bleche
EP3783116B1 (de) Vorbeschichtete blätter, die die herstellung von druckgehärteten und beschichteten stahlteilen erlauben
CA2680623C (fr) Acier pour formage a chaud ou trempe sous outil, a ductilite amelioree
EP2291547B1 (de) Verfahren zur herstellung von kaltgewalzten dualphasenstahlblechen mit sehr hoher festigkeit und so hergestellte bleche
CA2617879C (fr) Procede de fabrication de toles d&#39;acier presentant une haute resistance et une excellente ductilite, et toles ainsi produites
EP3024951B1 (de) Stahlblech mit sehr hohen mechanischen festigkeits- und dehnbarkeitseigenschaften, herstellungsverfahren und verwendung solcher bleche
EP3146083B1 (de) Doppelgeglühtes stahlblech mit hoher mechanischer festigkeit und duktilität, verfahren zur herstellung und verwendung solcher bleche
CA2834967C (fr) Procede de fabrication d&#39;acier martensitique a tres haute limite elastique et tole ou piece ainsi obtenue
WO2018220540A1 (fr) Procede de fabrication de pieces d&#39;acier a haute resistance mecanique et ductilite amelioree, et pieces obtenues par ce procede
WO2011104443A1 (fr) Procédé de fabrication d&#39;une pièce a partir d&#39;une tôle revêtue d&#39;aluminium ou d&#39;alliage d&#39;aluminium
JP2023507960A (ja) 表面品質と電気抵抗スポット溶接性に優れた高強度溶融亜鉛めっき鋼板及びその製造方法

Legal Events

Date Code Title Description
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

17P Request for examination filed

Effective date: 20100219

AK Designated contracting states

Kind code of ref document: A1

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

AX Request for extension of the european patent

Extension state: AL BA MK RS

RIN1 Information on inventor provided before grant (corrected)

Inventor name: ORMSTON, DAMIEN

Inventor name: DRILLET, PASCAL

17Q First examination report despatched

Effective date: 20100715

DAX Request for extension of the european patent (deleted)
GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

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

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

Free format text: NOT ENGLISH

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

Free format text: LANGUAGE OF EP DOCUMENT: FRENCH

REG Reference to a national code

Ref country code: RO

Ref legal event code: EPE

REG Reference to a national code

Ref country code: NL

Ref legal event code: T3

REG Reference to a national code

Ref country code: SE

Ref legal event code: TRGR

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602008011594

Country of ref document: DE

Effective date: 20120202

REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Ref document number: 2375429

Country of ref document: ES

Kind code of ref document: T3

Effective date: 20120229

REG Reference to a national code

Ref country code: SK

Ref legal event code: T3

Ref document number: E 10829

Country of ref document: SK

LTIE Lt: invalidation of european patent or patent extension

Effective date: 20111123

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: 20120323

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: 20111123

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: 20120223

REG Reference to a national code

Ref country code: PL

Ref legal event code: T3

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

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: 20120224

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: 20111123

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: 20111123

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: 20111123

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: 20120323

REG Reference to a national code

Ref country code: IE

Ref legal event code: FD4D

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: 20111123

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 FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20111123

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: 20120223

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: 20111123

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: 20111123

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

26N No opposition filed

Effective date: 20120824

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602008011594

Country of ref document: DE

Effective date: 20120824

REG Reference to a national code

Ref country code: HU

Ref legal event code: AG4A

Ref document number: E014740

Country of ref document: HU

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 NON-PAYMENT OF DUE FEES

Effective date: 20120731

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: LI

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

Effective date: 20120731

Ref country code: CH

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

Effective date: 20120731

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: 20111123

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

Ref country code: LU

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

Effective date: 20120709

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 9

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 10

REG Reference to a national code

Ref country code: FR

Ref legal event code: PLFP

Year of fee payment: 11

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

Ref country code: RO

Payment date: 20230630

Year of fee payment: 16

Ref country code: NL

Payment date: 20230622

Year of fee payment: 16

Ref country code: IT

Payment date: 20230620

Year of fee payment: 16

Ref country code: FR

Payment date: 20230621

Year of fee payment: 16

Ref country code: CZ

Payment date: 20230623

Year of fee payment: 16

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

Ref country code: TR

Payment date: 20230626

Year of fee payment: 16

Ref country code: SK

Payment date: 20230623

Year of fee payment: 16

Ref country code: SE

Payment date: 20230622

Year of fee payment: 16

Ref country code: PL

Payment date: 20230622

Year of fee payment: 16

Ref country code: FI

Payment date: 20230622

Year of fee payment: 16

P01 Opt-out of the competence of the unified patent court (upc) registered

Effective date: 20230727

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

Ref country code: BE

Payment date: 20230622

Year of fee payment: 16

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

Ref country code: GB

Payment date: 20230620

Year of fee payment: 16

Ref country code: ES

Payment date: 20230801

Year of fee payment: 16

Ref country code: AT

Payment date: 20230622

Year of fee payment: 16

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

Ref country code: HU

Payment date: 20230630

Year of fee payment: 16

Ref country code: DE

Payment date: 20230620

Year of fee payment: 16