EP2020451A1 - Procédé de fabrication de tôles d'acier à hautes caractéristiques de résistance et de ductilité, et tôles ainsi produites - Google Patents

Procédé de fabrication de tôles d'acier à hautes caractéristiques de résistance et de ductilité, et tôles ainsi produites Download PDF

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Publication number
EP2020451A1
EP2020451A1 EP07290908A EP07290908A EP2020451A1 EP 2020451 A1 EP2020451 A1 EP 2020451A1 EP 07290908 A EP07290908 A EP 07290908A EP 07290908 A EP07290908 A EP 07290908A EP 2020451 A1 EP2020451 A1 EP 2020451A1
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EP
European Patent Office
Prior art keywords
steel
sheet
composition
hot
content
Prior art date
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EP07290908A
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German (de)
English (en)
French (fr)
Inventor
Pascal Drillet
Damien Ormston
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ArcelorMittal France SA
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ArcelorMittal France SA
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Application filed by ArcelorMittal France SA filed Critical ArcelorMittal France SA
Priority to EP07290908A priority Critical patent/EP2020451A1/fr
Priority to KR1020157029946A priority patent/KR20150123957A/ko
Priority to KR1020107003457A priority patent/KR20100037147A/ko
Priority to KR1020127034336A priority patent/KR20130010030A/ko
Priority to BRPI0814514A priority patent/BRPI0814514B1/pt
Priority to RU2010105699/02A priority patent/RU2451764C2/ru
Priority to PCT/FR2008/000993 priority patent/WO2009034250A1/fr
Priority to US12/669,188 priority patent/US20100221573A1/en
Priority to EP08830766A priority patent/EP2171112B1/fr
Priority to CN2008801040865A priority patent/CN101784688B/zh
Priority to JP2010516534A priority patent/JP5298127B2/ja
Priority to UAA201001690A priority patent/UA98798C2/ru
Priority to CA2694069A priority patent/CA2694069C/fr
Priority to KR1020147007669A priority patent/KR20140044407A/ko
Priority to PL08830766T priority patent/PL2171112T3/pl
Priority to KR1020187002754A priority patent/KR101892423B1/ko
Priority to ES08830766T priority patent/ES2375429T3/es
Priority to AT08830766T priority patent/ATE534756T1/de
Priority to ARP080103095A priority patent/AR067594A1/es
Publication of EP2020451A1 publication Critical patent/EP2020451A1/fr
Priority to ZA201000290A priority patent/ZA201000290B/xx
Priority to MA32523A priority patent/MA31525B1/fr
Priority to US14/575,475 priority patent/US10214792B2/en
Priority to US15/879,944 priority patent/US10428400B2/en
Withdrawn legal-status Critical Current

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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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • 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
    • 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 hot rolled sheets of so-called "multiphase" steels, simultaneously having a very high strength and a deformation capacity for carrying out cold forming 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
  • the present invention aims to solve the problems mentioned above. It aims to provide a hot-rolled steel having a mechanical strength greater than 800 MPa together with an elongation rate greater than 10% rupture, both in long direction and in cross-direction relative to rolling.
  • the invention also aims at providing a steel 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 in the uncoated, electrogalvanized or galvanized state. This therefore requires that the mechanical characteristics of this steel are insensitive to the thermal cycles associated with dipping zinc coating processes.
  • 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 microstructure of the steel preferably comprises, as a surface fraction, at least 80% of higher bainite, the optional complement being constituted by lower bainite, martensite and residual austenite, the sum of the martensite and residual austenite contents being lower. at 5%.
  • the invention also relates to a beam welded assembly with high energy density made from a steel sheet according to one of the above modes.
  • the subject of the invention is also a process for manufacturing a hot-rolled steel sheet with a resistance greater than 800 MPa and an elongation at break of greater than 10%, according to which a steel of the above composition is supplied, a semi-finished product is poured at 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 made by dipping.
  • 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 the slats of bainitic ferrite: the resistance thus obtained is high, but the elongation is then significantly reduced. it.
  • the carbon content is between 0.050 and 0.070%.
  • 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 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.
  • 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% vanadium, under the conditions of manufacture according to the invention, a saturation of the effect on the mechanical characteristics is noted. 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 has no primary or proeutectoid ferrite: it then has a great homogeneity since the property gap Mechanics between the matrix (upper bainite) and the other possible constituents (lower bainite and martensite) is weak. During a mechanical stress, the deformations are distributed homogeneously. Dislocation accumulation does not occur at the interfaces between the constituents and premature damage is avoided, contrary to what can be noted in structures with a significant amount of primary ferrite, a phase whose flow limit is very low. , or martensite with a very high level of resistance. In this way, the steel according to the invention has a particular aptitude for certain demanding deformation modes such as the expansion of holes, the mechanical stress of cut edges, the 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 so well. 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 prevents the formation of proeutectoid ferrite and perlite, while a speed V R of 200 ° C / s or less prevents formation excessive 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, associated 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. Depending on the use envisaged, 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. an alloy based on zinc, for example by electrogalvanizing or dip galvanizing.
  • electrogalvanizing or dip galvanizing it has been demonstrated that the particular microstructure of the steel, composed mainly 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 with dipping have a high 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 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.
  • Steel R1 with too high a carbon content and a too low vanadium content, has insufficient breaking elongation.
  • Steel R2 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 in a Zn bath at this temperature and finally cooled. at room temperature.
  • the invention allows the manufacture of steels 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.

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  • Chemical & Material Sciences (AREA)
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  • Physics & Mathematics (AREA)
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  • Crystallography & Structural Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)
EP07290908A 2007-07-19 2007-07-19 Procédé de fabrication de tôles d'acier à hautes caractéristiques de résistance et de ductilité, et tôles ainsi produites Withdrawn EP2020451A1 (fr)

Priority Applications (23)

Application Number Priority Date Filing Date Title
EP07290908A EP2020451A1 (fr) 2007-07-19 2007-07-19 Procédé de fabrication de tôles d'acier à hautes caractéristiques de résistance et de ductilité, et tôles ainsi produites
CA2694069A CA2694069C (fr) 2007-07-19 2008-07-09 Procede de fabrication de toles d'acier a hautes caracteristiques de resistance et de ductilite, et toles ainsi produites
UAA201001690A UA98798C2 (ru) 2007-07-19 2008-07-09 Горячекатанный стальной лист или ДЕТАЛЬ, СПОСОБ ИХ ИЗГОТОВЛЕНИя И ПРИМЕНЕНИЕ, Сварные соединения из стальных листов ИЛИ ДЕТАЛИ
KR1020127034336A KR20130010030A (ko) 2007-07-19 2008-07-09 높은 인장강도 및 연성을 갖는 강판의 제조 공정, 및 이렇게 제조된 판
BRPI0814514A BRPI0814514B1 (pt) 2007-07-19 2008-07-09 chapa ou peça de aço, conjunto soldado, processo para a produção de uma chapa de aço, processo para produção de uma peça e uso de uma chapa de aço
RU2010105699/02A RU2451764C2 (ru) 2007-07-19 2008-07-09 Способ изготовления стальных листов с высокими характеристиками прочности и пластичности и листы, изготовленные при помощи этого способа
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
KR1020107003457A KR20100037147A (ko) 2007-07-19 2008-07-09 높은 인장강도 및 연성을 갖는 강판의 제조 공정, 및 이렇게 제조된 판
EP08830766A EP2171112B1 (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
CN2008801040865A CN101784688B (zh) 2007-07-19 2008-07-09 具有高拉伸强度和延展特性的钢片材的制造方法以及由此获得的片材
JP2010516534A JP5298127B2 (ja) 2007-07-19 2008-07-09 高抵抗特性および延性特性を有する鋼板を製造する方法およびこのようにして得られた鋼板
KR1020157029946A KR20150123957A (ko) 2007-07-19 2008-07-09 높은 인장강도 및 연성을 갖는 강판의 제조 공정, 및 이렇게 제조된 판
US12/669,188 US20100221573A1 (en) 2007-07-19 2008-07-09 Process for manufacturing steel sheet having high tensile strength and ductility characteristics, and sheet thus produced
AT08830766T ATE534756T1 (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
KR1020187002754A KR101892423B1 (ko) 2007-07-19 2008-07-09 높은 인장강도 및 연성을 갖는 강판의 제조 공정, 및 이렇게 제조된 판
ES08830766T ES2375429T3 (es) 2007-07-19 2008-07-09 Procedimiento de fabricación de chapas de acero con elevadas caracter�?sticas de resistencia y de ductilidad, y chapas as�? producidas.
KR1020147007669A KR20140044407A (ko) 2007-07-19 2008-07-09 높은 인장강도 및 연성을 갖는 강판의 제조 공정, 및 이렇게 제조된 판
ARP080103095A AR067594A1 (es) 2007-07-19 2008-07-18 Lamina de acero laminada en caliente y procedimiento para la fabricacion de la lamina de acero.
ZA201000290A ZA201000290B (en) 2007-07-19 2010-01-15 Process for manufacturing steel sheet having high tensile strength and ductility characteristics, and sheet thus produced
MA32523A MA31525B1 (fr) 2007-07-19 2010-01-18 Procede de fabrication de toles d'acier à hautes caractéristiques de résistance et de ductilité, et toles ainsi produites
US14/575,475 US10214792B2 (en) 2007-07-19 2014-12-18 Process for manufacturing steel sheet
US15/879,944 US10428400B2 (en) 2007-07-19 2018-01-25 Steel sheet having high tensile strength and ductility

Applications Claiming Priority (1)

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EP07290908A EP2020451A1 (fr) 2007-07-19 2007-07-19 Procédé de fabrication de tôles d'acier à hautes caractéristiques de résistance et de ductilité, et tôles ainsi produites

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EP08830766A Active EP2171112B1 (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

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EP (2) EP2020451A1 (pt)
JP (1) JP5298127B2 (pt)
KR (5) KR20140044407A (pt)
CN (1) CN101784688B (pt)
AR (1) AR067594A1 (pt)
AT (1) ATE534756T1 (pt)
BR (1) BRPI0814514B1 (pt)
CA (1) CA2694069C (pt)
ES (1) ES2375429T3 (pt)
MA (1) MA31525B1 (pt)
PL (1) PL2171112T3 (pt)
RU (1) RU2451764C2 (pt)
UA (1) UA98798C2 (pt)
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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
WO2012127125A1 (fr) 2011-03-24 2012-09-27 Arcelormittal Investigatión Y Desarrollo Sl Tôle d'acier laminée à chaud et procédé de fabrication associé
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

Families Citing this family (23)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
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
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
WO2015037059A1 (ja) * 2013-09-10 2015-03-19 株式会社神戸製鋼所 プレス成形品の製造方法およびプレス成形品
RU2648104C2 (ru) * 2013-09-18 2018-03-22 Ниппон Стил Энд Сумитомо Метал Корпорейшн Горячештампованная деталь и способ ее изготовления
CN105874091A (zh) * 2014-01-06 2016-08-17 新日铁住金株式会社 热成形构件及其制造方法
ES2745428T3 (es) 2014-01-06 2020-03-02 Nippon Steel Corp Acero y método para fabricar el mismo
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
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
WO2016001702A1 (en) 2014-07-03 2016-01-07 Arcelormittal Method for producing a high strength coated steel sheet having improved strength, ductility and formability
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
KR102462210B1 (ko) † 2014-10-09 2022-11-03 티센크루프 스틸 유럽 악티엔게젤샤프트 냉간 압연되고 재결정 어닐링된 평강 제품 및 평강 제품의 제조 방법
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
JP7185555B2 (ja) 2019-02-18 2022-12-07 株式会社神戸製鋼所 鋼板
WO2021123877A1 (en) 2019-12-17 2021-06-24 Arcelormittal Hot rolled steel sheet and 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

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH04358022A (ja) * 1991-06-04 1992-12-11 Nippon Steel Corp 強靱鋼の製造方法
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
JP2003321739A (ja) * 2002-04-30 2003-11-14 Jfe Steel Kk 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
WO2005005670A1 (en) * 2003-06-26 2005-01-20 Nippon Steel Corporation High-strength hot-rolled steel sheet excellent in shape fixability and method of producing the same
EP1764423A1 (en) * 2004-07-07 2007-03-21 JFE Steel Corporation Method for producing high tensile steel sheet

Family Cites Families (14)

* 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
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
DE69834932T2 (de) * 1997-07-28 2007-01-25 Exxonmobil Upstream Research Co., Houston Ultrahochfeste, schweissbare stähle mit ausgezeichneter ultratief-temperaturzähigkeit
WO1999005328A1 (en) * 1997-07-28 1999-02-04 Exxonmobil Upstream Research Company Method for producing ultra-high strength, weldable steels with superior toughness
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
DE60224557T4 (de) * 2001-10-04 2015-06-25 Nippon Steel & Sumitomo Metal Corporation Ziehbares hochfestes dünnes Stahlblech mit hervorragender Formfixierungseigenschaft und Herstellungsverfahren dafür
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
KR101165166B1 (ko) 2003-09-30 2012-07-11 신닛뽄세이테쯔 카부시키카이샤 용접성과 연성이 우수한 고항복비 고강도 열연 강판 및 고항복비 고강도 용융 아연 도금 강판 및 고항복비 고강도 합금화 용융 아연 도금 강판
US20080118390A1 (en) 2004-03-31 2008-05-22 Jfe Steel Corporation High-Stiffness High-Strength Thin Steel Sheet and Method For Producing the 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

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH04358022A (ja) * 1991-06-04 1992-12-11 Nippon Steel Corp 強靱鋼の製造方法
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
JP2003321739A (ja) * 2002-04-30 2003-11-14 Jfe Steel Kk 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
WO2005005670A1 (en) * 2003-06-26 2005-01-20 Nippon Steel Corporation High-strength hot-rolled steel sheet excellent in shape fixability and method of producing the same
EP1764423A1 (en) * 2004-07-07 2007-03-21 JFE Steel Corporation Method for producing high tensile steel sheet

Cited By (12)

* 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
WO2012127125A1 (fr) 2011-03-24 2012-09-27 Arcelormittal Investigatión Y Desarrollo Sl Tôle d'acier laminée à chaud et procédé de fabrication associé
WO2012127136A2 (fr) 2011-03-24 2012-09-27 Arcelormittal Investigación Y Desarrollo Sl Tôle d'acier laminée à chaud et procédé de fabrication associé
RU2551727C2 (ru) * 2011-03-24 2015-05-27 Арселормитталь Инвестигасьон И Десарролло Сл Горячекатаный стальной лист и соответствующий способ изготовления
US9540719B2 (en) 2011-03-24 2017-01-10 Arcelormittal Investigacion Y Desarrollo Sl Hot-rolled steel sheet and associated production method
WO2016005780A1 (fr) 2014-07-11 2016-01-14 Arcelormittal Investigación Y Desarrollo Sl Tôle d'acier laminée à chaud et procédé de fabrication associé
WO2016005811A1 (fr) 2014-07-11 2016-01-14 Arcelormittal Tôle d'acier laminée à chaud et procédé de fabrication associé
US10858716B2 (en) 2014-07-11 2020-12-08 Arcelormittal Hot rolled steel sheet and associated manufacturing method
US11447844B2 (en) 2014-07-11 2022-09-20 Arcelormittal Manufacturing method for hot rolled steel sheet
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
EP3325684B1 (de) 2015-07-17 2020-03-04 Salzgitter Flachstahl GmbH Verfahren zum herstellen eines warmbandes aus einem bainitischen mehrphasenstahl mit einer zn-mg-al-beschichtung und ein entsprechendes warmband
US11512364B2 (en) 2015-07-17 2022-11-29 Salzgitter Flachstahl Gmbh Method for producing a hot strip of a bainitic multi-phase steel having a Zn—Mg—Al coating, and a corresponding hot strip

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CN101784688A (zh) 2010-07-21
KR20180014843A (ko) 2018-02-09
KR20140044407A (ko) 2014-04-14
MA31525B1 (fr) 2010-07-01
KR20150123957A (ko) 2015-11-04
UA98798C2 (ru) 2012-06-25
AR067594A1 (es) 2009-10-14
CN101784688B (zh) 2011-11-23
BRPI0814514B1 (pt) 2019-09-03
ES2375429T3 (es) 2012-02-29
KR20130010030A (ko) 2013-01-24
BRPI0814514A2 (pt) 2015-02-03
ZA201000290B (en) 2010-10-27
US20150203932A1 (en) 2015-07-23
CA2694069A1 (fr) 2009-03-19
US20180148806A1 (en) 2018-05-31
WO2009034250A1 (fr) 2009-03-19
JP5298127B2 (ja) 2013-09-25
KR101892423B1 (ko) 2018-08-27
EP2171112B1 (fr) 2011-11-23
EP2171112A1 (fr) 2010-04-07
US10428400B2 (en) 2019-10-01
ATE534756T1 (de) 2011-12-15
US20180163282A9 (en) 2018-06-14
CA2694069C (fr) 2013-05-21
RU2010105699A (ru) 2011-08-27
KR20100037147A (ko) 2010-04-08
JP2010533791A (ja) 2010-10-28
RU2451764C2 (ru) 2012-05-27
US10214792B2 (en) 2019-02-26
US20100221573A1 (en) 2010-09-02

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