EP1767659A1 - Herstellungsverfahren eines Stahlwerkstücks mit mehrphasigem Mikrogefüge - Google Patents

Herstellungsverfahren eines Stahlwerkstücks mit mehrphasigem Mikrogefüge Download PDF

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Publication number
EP1767659A1
EP1767659A1 EP05291958A EP05291958A EP1767659A1 EP 1767659 A1 EP1767659 A1 EP 1767659A1 EP 05291958 A EP05291958 A EP 05291958A EP 05291958 A EP05291958 A EP 05291958A EP 1767659 A1 EP1767659 A1 EP 1767659A1
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EP
European Patent Office
Prior art keywords
steel
microstructure
blank
ferrite
cooling
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.)
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EP05291958A
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English (en)
French (fr)
Inventor
Jacques Corquillet
Jacques Devroc
Jean-Louis Hochard
Jean-Pierre Laurent
Antoine Moulin
Nathalie Romanowski
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ArcelorMittal France SA
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Arcelor France SA
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Publication date
Application filed by Arcelor France SA filed Critical Arcelor France SA
Priority to EP05291958A priority Critical patent/EP1767659A1/de
Priority to KR1020127020882A priority patent/KR20120099526A/ko
Priority to JP2008531732A priority patent/JP5386170B2/ja
Priority to EP10010435A priority patent/EP2287344A1/de
Priority to BRPI0616261-4A priority patent/BRPI0616261B1/pt
Priority to AT06808157T priority patent/ATE513932T1/de
Priority to CN2006800393555A priority patent/CN101292049B/zh
Priority to EP06808157A priority patent/EP1929053B1/de
Priority to ES06808157T priority patent/ES2366133T3/es
Priority to KR1020117023104A priority patent/KR20110121657A/ko
Priority to CA2623146A priority patent/CA2623146C/fr
Priority to KR1020137001899A priority patent/KR101453697B1/ko
Priority to RU2008115444/02A priority patent/RU2403291C2/ru
Priority to KR1020087007005A priority patent/KR20080053312A/ko
Priority to UAA200805058A priority patent/UA96739C2/ru
Priority to PCT/FR2006/002135 priority patent/WO2007034063A1/fr
Priority to US12/067,533 priority patent/US8114227B2/en
Priority to PL06808157T priority patent/PL1929053T3/pl
Publication of EP1767659A1 publication Critical patent/EP1767659A1/de
Priority to ZA200802385A priority patent/ZA200802385B/xx
Priority to MA30763A priority patent/MA29790B1/fr
Priority to US13/343,896 priority patent/US10294557B2/en
Withdrawn legal-status Critical Current

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    • 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
    • C23C2/26—After-treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D1/185—Hardening; Quenching with or without subsequent tempering from an intercritical temperature
    • 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
    • C21D1/62—Quenching devices
    • C21D1/673—Quenching devices for die quenching
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
    • 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—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
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/12—Aluminium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/26—After-treatment
    • C23C2/261—After-treatment in a gas atmosphere, e.g. inert or reducing atmosphere
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets

Definitions

  • the present invention relates to a method of manufacturing a multi-phased microstructure steel piece homogeneous in each of the parts of said part, and having high mechanical characteristics.
  • TRIP steels the term meaning transformation induced plasticity
  • dual phase steels which combine a very high mechanical strength with very high possibilities of deformation.
  • TRIP steels have a microstructure composed of ferrite, residual austenite, and possibly bainite and martensite, which enables them to reach tensile strengths ranging from 600 to 1000 MPa.
  • the dual-phase steels have a microstructure composed of ferrite and martensite, which enables them to reach tensile strengths ranging from 400 MPa to more than 1200 MPa.
  • this type of parts it is cold forming, for example by stamping between tools, a blank cut in a cold rolled strip of dual phase steel or TRIP steel.
  • the microstructure of the steel is no longer homogeneous in each part of the room, and the behavior of the part in use is difficult to predict.
  • the residual austenite is transformed into martensite under the effect of the deformation.
  • the deformation is not homogeneous throughout the room, some parts of the room will still contain residual austenite not transformed into martensite and therefore having a significant residual ductility, while other parts of the room having undergone significant deformation will present a ferritic-martensitic structure optionally comprising ductile bainite.
  • the object of the present invention is therefore to overcome the aforementioned drawbacks, and to propose a method of manufacturing a steel part comprising ferrite and having a homogeneous multiphase microstructure in each part of said part, and not exhibiting resilient return after forming a blank from a steel strip whose composition is typical of that of multi-phase microstructure steels.
  • the area of the different phases is measured in a section made along a plane perpendicular to the plane of the strip (this plane may be parallel to to the rolling direction, or parallel to the direction transverse to the rolling).
  • the different phases sought are revealed by a chemical attack adapted according to their nature.
  • the invention has the second object a steel part comprising ferrite and having a homogeneous multi-phase microstructure in each of the parts of said part, obtainable by said method.
  • the third object of the invention is a motorized land vehicle comprising said part.
  • the method according to the invention consists in shaping hot, in a certain temperature range, a blank previously cut in a steel strip whose composition is typical of that of multi-phase microstructure steels, but which initially does not does not necessarily have a multi-phased structure, to form a steel part that acquires a multi-phased microstructure during its cooling between the formatting tools.
  • the inventors have furthermore demonstrated that, provided that the cooling rate is sufficient, a multi-phased structure could be obtained whatever the rate of cooling of the blank between the tools.
  • the advantage of this invention lies in the fact that it is not necessary to form the multi-phased microstructure at the stage of manufacture of the hot sheet, or of its coating, and that forming it at stage of manufacture of the part, by hot forming, ensures a homogeneous final multi-phase microstructure in each of the parts of the part, which is advantageous in the case of use for parts of absorption of energy, because the microstructure is not altered as it is the case when cold forming of dual-phase steel or TRIP steel parts.
  • the inventors have indeed verified that the energy absorbing capacity of a part, determined by the tensile strength multiplied by the elongation (Rm x A), is greater when the piece has been obtained according to the invention. invention that when it was obtained by cold forming a dual phase steel blank or TRIP steel. Indeed, cold forming consumes some of the energy absorption capacity.
  • Another advantage of the invention lies in the fact that the hot shaping leads to a much higher shaping ability than cold.
  • a variety of wider shapes can be accessed and new designs of parts can be envisaged while retaining steel compositions whose characteristics, such as weldability, are known.
  • the part obtained has a multi-phase microstructure comprising ferrite at a proportion preferably greater than or equal to 25% by surface, and at least one of the following phases: martensite, bainite, residual austenite.
  • a proportion of at least 25% ferrite surface area makes it possible to give the steel ductility sufficient for the formed parts to have a high energy absorption capacity.
  • the remainder of the composition is iron and other elements that are usually expected to be found as impurities resulting from steel making, in proportions that do not affect the properties of the steel. sought.
  • this metal coating is chosen from zinc or zinc alloy coatings (zinc-aluminum for example), and if it is also desired to withstand good heat resistance, the coatings of aluminum or aluminum alloy (aluminum-silicon for example). These coatings are deposited in a conventional manner either by hot dipping in a bath of liquid metal, by electrodeposition, or under vacuum.
  • the steel blank is heated to bring it to a holding temperature T1 greater than Ac1, and is maintained at this temperature T1 for a hold time M that adjusts so that the steel, after heating the blank, comprises a proportion of austenite greater than or equal to 25% by surface.
  • the heated blank is transferred into a forming tool to form a part, and cool it.
  • the cooling of the workpiece within the shaping tool is performed with a cooling rate V sufficient to prevent all of the austenite from becoming ferrite, and so that the microstructure of the steel after cooling the piece is a multi-phase microstructure comprising ferrite, and which is homogeneous in each of the areas of the room.
  • Homogeneous multi-phased microstructure in each of the zones of the part is understood to mean a microstructure having constancy in terms of proportion and morphology in each zone of the part, and in which the different phases are uniformly distributed.
  • the shaping tools can be cooled, for example by fluid circulation.
  • clamping force of the shaping tool must be sufficient to ensure intimate contact between the blank and the tool, and ensure efficient and homogeneous cooling of the room.
  • Cold pre-deformation of the blank for example by profiling or cold stamping of the blank, before hot forming is advantageous insofar as it allows access to parts that may have a more complex geometry .
  • the method according to the invention is used to manufacture a steel part having a multi-phase microstructure comprising either ferrite and martensite, or ferrite and bainite, again ferrite, martensite and bainite.
  • the remainder of the composition is iron and other elements that are usually expected to be found as impurities resulting from steel making, in proportions that do not affect the properties of the steel. sought.
  • the blank is heated to a holding temperature T1 preferably between Ac1 and Ac3, so as to control the proportion of austenite formed during the heating of the blank, and do not exceed the upper limit of 75% surface area of austenite.
  • T1 a holding temperature between Ac1 and Ac3
  • the inventors have demonstrated that, provided that the cooling rate is sufficient, a multi-phase microstructure comprising ferrite is obtained. whatever the rate of cooling of the blank between the tools.
  • a proportion of austenite in the steel heated to a holding temperature T1 during a holding time M of between 25 and 75% by weight offers a good compromise in terms of the mechanical strength of the steel after shaping and regularity. mechanical characteristics of the steel thanks to the robustness of the process. Indeed, beyond 25% of austenite surface, sufficient hardening phases are formed, as per example the martensite and / or the bainite, during the cooling of the steel, so that the elastic limit Re of the steel after shaping is sufficient.
  • the holding time of the steel blank at the holding temperature T1 depends essentially on the thickness of the strip.
  • the thickness of the strip is typically between 0.3 and 3 mm. Therefore, to form a proportion of austenite between 25 and 75% by surface, the holding time M is preferably between 10 and 1000 s. If the steel blank is maintained at a holding temperature T1 for a holding time M greater than 1000 s, the austenite grains increase and the elastic limit Re of the steel after forming will be limited. In addition, the hardenability of the steel is reduced and the surface of the steel oxidizes.
  • the proportion of austenite formed will be insufficient, and the proportion of martensite and / or bainite formed during the cooling of the part between the tool, will be insufficient. so that the elastic limit Re of the steel is sufficient.
  • the cooling rate V of the steel part in the forming tool depends on the deformation and the quality of the contact between the tool and the steel blank. However, when the part is at a temperature T2 between Ar3 and Ar1, the cooling rate V must be sufficiently high for the desired multi-phase microstructure to be obtained. Thus, when the part is at a temperature T2 between Ar3 and Ar1, the cooling rate V is preferably greater than 10 ° C./s.
  • a multiphase steel part comprising 25 to 75% ferrite surface area and 25 to 75% surface area of martensite and / or bainite is formed.
  • the method according to the invention is used to manufacture a TRIP steel part.
  • TRIP steel a multiphase microstructure comprising ferrite, residual austenite, and possibly martensite and / or bainite.
  • the remainder of the composition is iron and other elements that are usually expected to be found as impurities resulting from steel making, in proportions that do not affect the properties of the steel. sought.
  • the holding time of the steel blank at a holding temperature T1 greater than Ac1 depends essentially on the thickness of the strip.
  • the thickness of the strip is typically between 0.3 and 3 mm. Therefore, to form a proportion of austenite greater than or equal to 25% by surface, the holding time M is preferably between 10 and 1000 s. If the steel blank is maintained at a holding temperature T1 for a holding time M greater than 1000 s, the austenite grains increase and the elastic limit Re of the steel after forming will be limited. In addition, the hardenability of the steel is reduced and the surface of the steel oxidizes. On the other hand, if the blank is kept during a holding time M less than 10 s, the proportion of austenite formed will be insufficient, and will not be enough residual austenite and bainite when cooling the room between tool.
  • the cooling rate V of the steel part in the forming tool depends on the deformation and the quality of the contact between the tool and the steel blank. To obtain a steel part having a TRIP multi-phase microstructure, it is appropriate that when the part is at a temperature T2 between Ar3 and Ar1, the cooling rate V is between 10 ° C./s and 100 ° C./s . In fact, below 10 ° C / s, essentially ferrite and carbide will be formed, but no residual austenite or martensite, and above 100 ° C / s, essentially martensite will be formed. no residual austenite.
  • a multi-phase steel part is formed, in% by surface, of ferrite at a proportion greater than or equal to 25%, from 3 to 30% of austenite, and possibly martensite and / or or bainite.
  • the TRIP effect can advantageously be used to absorb energy in the event of high speed shocks. Indeed, during a significant deformation of a TRIP steel part, the residual austenite is gradually transformed into martensite by selecting the orientation of the martensite. This has the effect of reducing the residual stresses in the martensite, reducing the internal stresses in the part, and finally limiting the damage of the part, because the rupture thereof will take place for an elongation A more important than if it was not TRIP steel.
  • the inventors have carried out tests on both steels having on the one hand a composition typical of that of mutli-phased microstructure steels. comprising ferrite and martensite and / or bainite (point 1), and secondly a composition typical of that of multithreaded microstructure TRIP steels (point 2).
  • Blanks 400 x 600 mm in size are cut from a steel strip whose composition, indicated in Table I, is that of a steel grade DP780 (Dual Phase 780).
  • the strip has a thickness of 1.2 mm.
  • the Ac1 temperature of this steel is 705 ° C and the Ac3 temperature is 815 ° C.
  • the blanks are brought to a variable holding temperature T1, during a holding period of 5 minutes. Then, they are immediately transferred to a stamping tool in which they are both shaped and cooled with variable cooling rates V, keeping them in the tool for a period of 60 s.
  • the embossing achieved is similar to an Omega shape structure
  • the energy absorbing capacity of the parts obtained with heating of the steel at a temperature between Ac1 and Ac3 is greater than that of the parts obtained with heating to a temperature above Ac3.
  • the purpose of this test is to show the interest of a hot shaping compared to a cold shaping, and to evaluate the elastic return.
  • a piece of DP780 grade steel is manufactured by cold stamping a blank cut from a 1.2 mm thick steel strip, the composition of which is indicated in Table I, but which, unlike the strip used in point 1, already has before stamping a multi-phased microstructure comprising 70% ferrite surface, 15% martensite surface, and 15% bainite surface.
  • FIG. 1 clearly shows that the part formed by cold stamping (marked in the figure by the letter G) has a strong springback, with respect to the piece A (see Table II) formed by hot stamping (marked by the letter AT).
  • Blanks measuring 200 ⁇ 500 mm are cut from a steel strip whose composition, indicated in Table III, is that of a TRIP 800 grade steel.
  • the strip has a thickness of 1.2 mm.
  • the Ac1 temperature of this steel is 751 ° C and the Ac3 temperature is 875 ° C.
  • the blanks are brought to a variable holding temperature T1, during a hold time of 5 minutes, and then immediately transferred to a stamping tool in which they are both shaped and cooled with a cooling rate V of 45 ° C / s, keeping them in the tool for 60 s.
  • the embossing achieved is similar to an Omega shape structure.
  • Table III chemical composition of the steel according to the invention, expressed in% by weight, the balance being iron or impurities VS mn Yes al MB Cr P Ti Nb V 0.2 1.5 1.5 0.05 0,007 0.01 0,011 0.005 - - T1 (° C) Room Re (MPa) Rm (MPa) AT (%) Rm x A Microstructure (% surface area) 760 H 541 1174 12.4 14558 35% F + 17% A + 48% M 800 I 485 1171 12.8 14989 45% F + 11% A + 44% M 840 J 454 1110 14.3 15873 45% F + 15% A + 38% M + 2% B + 2% B

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Articles (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
  • Coating With Molten Metal (AREA)
EP05291958A 2005-09-21 2005-09-21 Herstellungsverfahren eines Stahlwerkstücks mit mehrphasigem Mikrogefüge Withdrawn EP1767659A1 (de)

Priority Applications (21)

Application Number Priority Date Filing Date Title
EP05291958A EP1767659A1 (de) 2005-09-21 2005-09-21 Herstellungsverfahren eines Stahlwerkstücks mit mehrphasigem Mikrogefüge
KR1020137001899A KR101453697B1 (ko) 2005-09-21 2006-09-18 다상 미세조직의 강편을 제조하는 방법
RU2008115444/02A RU2403291C2 (ru) 2005-09-21 2006-09-18 Способ получения стальной детали с многофазной микроструктурой
JP2008531732A JP5386170B2 (ja) 2005-09-21 2006-09-18 多相微構造の鋼部品を製造する方法
BRPI0616261-4A BRPI0616261B1 (pt) 2005-09-21 2006-09-18 Processo de fabricação de uma peça em aço de microestrutura de multifases
AT06808157T ATE513932T1 (de) 2005-09-21 2006-09-18 Verfahren zur herstellung eines stahlteils mit mehrphasiger mikrostruktur
CN2006800393555A CN101292049B (zh) 2005-09-21 2006-09-18 制备具有多相显微组织的钢零件的方法
EP06808157A EP1929053B1 (de) 2005-09-21 2006-09-18 Verfahren zur herstellung eines stahlteils mit mehrphasiger mikrostruktur
ES06808157T ES2366133T3 (es) 2005-09-21 2006-09-18 Procedimiento de fabricación de un pieza de ácero de microestructura multifásica.
KR1020087007005A KR20080053312A (ko) 2005-09-21 2006-09-18 다상 미세조직의 강편을 제조하는 방법
CA2623146A CA2623146C (fr) 2005-09-21 2006-09-18 Procede de fabrication d'une piece en acier de microstructure multi-phasee
KR1020127020882A KR20120099526A (ko) 2005-09-21 2006-09-18 다상 미세조직의 강편을 제조하는 방법
EP10010435A EP2287344A1 (de) 2005-09-21 2006-09-18 Herstellungsverfahren eines Stahlwerkstücks mit mehrphasigem Mikrogefüge
KR1020117023104A KR20110121657A (ko) 2005-09-21 2006-09-18 다상 미세조직의 강편을 제조하는 방법
UAA200805058A UA96739C2 (ru) 2005-09-21 2006-09-18 Стальная деталь с многофазной структурой, способ ее получения и применение детали
PCT/FR2006/002135 WO2007034063A1 (fr) 2005-09-21 2006-09-18 Procede de fabrication d’une piece en acier de microstructure multi-phasee
US12/067,533 US8114227B2 (en) 2005-09-21 2006-09-18 Method for making a steel part of multiphase microstructure
PL06808157T PL1929053T3 (pl) 2005-09-21 2006-09-18 Sposób wytwarzania części ze stali o mikrostrukturze wielofazowej
ZA200802385A ZA200802385B (en) 2005-09-21 2008-03-13 Method for making a steel part of multiphase microstructure
MA30763A MA29790B1 (fr) 2005-09-21 2008-03-19 Procede de fabrication d'une piece en acier de microstructure multi-phasee
US13/343,896 US10294557B2 (en) 2005-09-21 2012-01-05 Method for making a steel part of multiphase microstructure

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Cited By (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1939308A1 (de) * 2006-11-14 2008-07-02 ThyssenKrupp Steel AG Verfahren zum Herstellen eines Bauteils durch Wärmepresshärten und hochfestes Bauteil mit verbesserter Bruchdehnung
WO2008102012A1 (en) * 2007-02-23 2008-08-28 Corus Staal Bv Method of thermomechanical shaping a final product with very high strength and a product produced thereby
WO2009135776A1 (de) * 2008-05-06 2009-11-12 Thyssenkrupp Steel Ag Verfahren zum herstellen eines stahlformteils mit einem überwiegend ferritisch-bainitischen gefüge
US8864921B2 (en) 2007-07-19 2014-10-21 Tata Steel Ijmuiden B.V. Method for annealing a strip of steel having a variable thickness in length direction
WO2015039763A3 (en) * 2013-09-19 2015-08-20 Tata Steel Ijmuiden B.V. Steel for hot forming
WO2015144318A1 (en) * 2014-03-28 2015-10-01 Tata Steel Ijmuiden B.V. Method for hot forming a coated steel blank
WO2016016707A1 (fr) * 2014-07-30 2016-02-04 Arcelormittal Procédé de fabrication de tôles d'acier pour durcissement sous presse, et pièces obtenues par ce procédé
WO2016146581A1 (en) * 2015-03-16 2016-09-22 Tata Steel Ijmuiden B.V. Steel for hot forming
EP3093359A4 (de) * 2014-01-06 2017-08-23 Nippon Steel & Sumitomo Metal Corporation Warmgeformtes element und verfahren zu herstellung davon
US10774405B2 (en) 2014-01-06 2020-09-15 Nippon Steel Corporation Steel and method of manufacturing the same
CN112725687A (zh) * 2020-11-18 2021-04-30 邯郸钢铁集团有限责任公司 折弯及抗撞性能优良的边梁用750bl钢板及生产方法

Families Citing this family (63)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US9132567B2 (en) * 2007-03-23 2015-09-15 Dayton Progress Corporation Tools with a thermo-mechanically modified working region and methods of forming such tools
US8968495B2 (en) * 2007-03-23 2015-03-03 Dayton Progress Corporation Methods of thermo-mechanically processing tool steel and tools made from thermo-mechanically processed tool steels
EP2171102B1 (de) * 2007-07-19 2017-09-13 Muhr und Bender KG Metallstreifen mit veränderlicher dicke in längsrichtung
EP2025771A1 (de) * 2007-08-15 2009-02-18 Corus Staal BV Verfahren zur Herstellung eines beschichteten Stahlbandes zur Herstellung von Platinenzuschnitten zur thermomechanischen Formgebung, so hergestelltes Band und Verwendung eines solchen Bandes
DE102008004371A1 (de) * 2008-01-15 2009-07-16 Robert Bosch Gmbh Bauelement, insbesondere eine Kraftfahrzeugkomponente, aus einem Dualphasen-Stahl
EP2325435B2 (de) 2009-11-24 2020-09-30 Tenaris Connections B.V. Verschraubung für [ultrahoch] abgedichteten internen und externen Druck
JP5327106B2 (ja) 2010-03-09 2013-10-30 Ｊｆｅスチール株式会社 プレス部材およびその製造方法
DE102010012830B4 (de) * 2010-03-25 2017-06-08 Benteler Automobiltechnik Gmbh Verfahren zur Herstellung einer Kraftfahrzeugkomponente und Karosseriebauteil
EP2374910A1 (de) 2010-04-01 2011-10-12 ThyssenKrupp Steel Europe AG Stahl, Stahlflachprodukt, Stahlbauteil und Verfahren zur Herstellung eines Stahlbauteils
JP5126399B2 (ja) * 2010-09-06 2013-01-23 Ｊｆｅスチール株式会社 伸びフランジ性に優れた高強度冷延鋼板およびその製造方法
CN103154279B (zh) 2010-10-12 2015-09-23 塔塔钢铁艾默伊登有限责任公司 热成形钢坯的方法和热成形的部件
US9163296B2 (en) 2011-01-25 2015-10-20 Tenaris Coiled Tubes, Llc Coiled tube with varying mechanical properties for superior performance and methods to produce the same by a continuous heat treatment
KR101257166B1 (ko) * 2011-01-28 2013-04-22 현대제철 주식회사 자동차 사이드 멤버 및 그 제조 방법
IT1403689B1 (it) 2011-02-07 2013-10-31 Dalmine Spa Tubi in acciaio ad alta resistenza con eccellente durezza a bassa temperatura e resistenza alla corrosione sotto tensioni da solfuri.
MX338997B (es) 2011-03-28 2016-05-09 Nippon Steel & Sumitomo Metal Corp Placa de acero laminada en frio y metodo de produccion de la misma.
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US9567658B2 (en) 2011-05-25 2017-02-14 Nippon Steel & Sumitomo Metal Corporation Cold-rolled steel sheet
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TWI548756B (zh) * 2011-07-27 2016-09-11 Nippon Steel & Sumitomo Metal Corp High strength cold rolled steel sheet with excellent extension flangeability and precision punching and its manufacturing method
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JP5942560B2 (ja) * 2012-04-18 2016-06-29 マツダ株式会社 鋼板のプレス成形方法
RU2495141C1 (ru) * 2012-05-11 2013-10-10 Федеральное Государственное Бюджетное Образовательное Учреждение Высшего Профессионального Образования "Донской Государственный Технический Университет" (Дгту) Способ получения естественного феррито-мартенситного композита
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WO2014108756A1 (en) 2013-01-11 2014-07-17 Tenaris Connections Limited Galling resistant drill pipe tool joint and corresponding drill pipe
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WO2017144419A1 (en) 2016-02-23 2017-08-31 Tata Steel Ijmuiden B.V. Hot formed part and method for producing it
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DE102016117494A1 (de) * 2016-09-16 2018-03-22 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines umgeformten Bauteils aus einem mittelmanganhaltigen Stahlflachprodukt und ein derartiges Bauteil
JP6424195B2 (ja) * 2016-11-14 2018-11-14 株式会社豊田中央研究所 熱間プレス成形方法
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DE102016225833A1 (de) 2016-12-21 2018-06-21 Henkel Ag & Co. Kgaa Verfahren zur Dosierung von Reinigungsmitteln
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CN110551878B (zh) * 2019-10-12 2021-06-08 东北大学 一种超高强度超高韧性低密度双相层状钢板及其制备方法
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EP4153791A4 (de) * 2020-05-18 2024-04-10 Magna International Inc. Verfahren zur verarbeitung von fortschrittlichem hochfestem stahl
CN111647820B (zh) * 2020-06-15 2022-01-11 山东建筑大学 一种先进高强度钢及其分段制备方法与应用
CN114855071A (zh) * 2021-06-23 2022-08-05 宇龙精机科技（浙江）有限公司 一种h13合金模具钢及其制备方法

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4222796A (en) * 1979-02-05 1980-09-16 Ford Motor Company High strength dual-phase steel
JPS59211533A (ja) * 1983-05-16 1984-11-30 Nisshin Steel Co Ltd 延性の優れた低降伏比複合組織鋼板の製造方法
JPS6043430A (ja) * 1983-08-15 1985-03-08 Nippon Kokan Kk <Nkk> 高強度高加工性複合組織鋼板の製造方法
FR2671749A1 (fr) * 1991-01-17 1992-07-24 Creusot Loire Procede de fabrication d'une piece de forme metallique a tres haute durete, notamment en acier et piece obtenue.
EP1013785A1 (de) * 1998-12-24 2000-06-28 Sollac Herstellungsverfahren für Formteile aus warmgewalztem Stahlblech
US20040163439A1 (en) * 2003-02-20 2004-08-26 Benteler Automobiltechnik Gmbh Method of making a hardened motor-vehicle part of complex shape

Family Cites Families (18)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS62286626A (ja) * 1986-06-04 1987-12-12 Nippon Steel Corp 鋼板のプレス成形方法
US5531842A (en) 1994-12-06 1996-07-02 Exxon Research And Engineering Company Method of preparing a high strength dual phase steel plate with superior toughness and weldability (LAW219)
CA2225679A1 (en) 1995-07-11 1997-01-30 Kari Martti Ullakko Iron-based shape memory and vibration damping alloys containing nitrogen
JPH09143612A (ja) * 1995-11-21 1997-06-03 Kobe Steel Ltd 降伏比の低い高強度熱延鋼板部材
CN1072272C (zh) * 1997-01-29 2001-10-03 新日本制铁株式会社 冲击能吸收特性和成形良好的高强度钢板及其制造方法
FR2780984B1 (fr) * 1998-07-09 2001-06-22 Lorraine Laminage Tole d'acier laminee a chaud et a froid revetue et comportant une tres haute resistance apres traitement thermique
AU744962B2 (en) * 1999-02-22 2002-03-07 Nippon Steel & Sumitomo Metal Corporation High strength galvanized steel plate excellent in adhesion of plated metal and formability in press working and high strength alloy galvanized steel plate and method for production thereof
FR2807447B1 (fr) * 2000-04-07 2002-10-11 Usinor Procede de realisation d'une piece a tres hautes caracteristiques mecaniques, mise en forme par emboutissage, a partir d'une bande de tole d'acier laminee et notamment laminee a chaud et revetue
JP4524850B2 (ja) * 2000-04-27 2010-08-18 Ｊｆｅスチール株式会社 延性および歪時効硬化特性に優れた高張力冷延鋼板および高張力冷延鋼板の製造方法
JP3828466B2 (ja) * 2002-07-29 2006-10-04 株式会社神戸製鋼所 曲げ特性に優れた鋼板
JP2004160489A (ja) * 2002-11-13 2004-06-10 Nissan Motor Co Ltd パネル部品のプレス成形方法
US7314532B2 (en) * 2003-03-26 2008-01-01 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) High-strength forged parts having high reduction of area and method for producing same
DE10333165A1 (de) * 2003-07-22 2005-02-24 Daimlerchrysler Ag Pressgehärtetes Bauteil und Verfahren zur Herstellung eines pressgehärteten Bauteils
JP4288201B2 (ja) * 2003-09-05 2009-07-01 新日本製鐵株式会社 耐水素脆化特性に優れた自動車用部材の製造方法
JP4268535B2 (ja) * 2004-02-17 2009-05-27 株式会社神戸製鋼所 強度成形性バランスに優れた高強度冷延鋼板
JP4551694B2 (ja) * 2004-05-21 2010-09-29 株式会社神戸製鋼所 温熱間成形品の製造方法および成形品
WO2008110670A1 (fr) * 2007-03-14 2008-09-18 Arcelormittal France Acier pour formage a chaud ou trempe sous outil a ductilite amelioree
WO2012168564A1 (fr) * 2011-06-07 2012-12-13 Arcelormittal Investigación Y Desarrollo Sl Tôle d'acier laminée à froid et revêtue de zinc ou d'alliage de zinc, procédé de fabrication et utilisation d'une telle tôle

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4222796A (en) * 1979-02-05 1980-09-16 Ford Motor Company High strength dual-phase steel
JPS59211533A (ja) * 1983-05-16 1984-11-30 Nisshin Steel Co Ltd 延性の優れた低降伏比複合組織鋼板の製造方法
JPS6043430A (ja) * 1983-08-15 1985-03-08 Nippon Kokan Kk <Nkk> 高強度高加工性複合組織鋼板の製造方法
FR2671749A1 (fr) * 1991-01-17 1992-07-24 Creusot Loire Procede de fabrication d'une piece de forme metallique a tres haute durete, notamment en acier et piece obtenue.
EP1013785A1 (de) * 1998-12-24 2000-06-28 Sollac Herstellungsverfahren für Formteile aus warmgewalztem Stahlblech
US20040163439A1 (en) * 2003-02-20 2004-08-26 Benteler Automobiltechnik Gmbh Method of making a hardened motor-vehicle part of complex shape

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
PATENT ABSTRACTS OF JAPAN vol. 009, no. 078 (C - 274) 6 April 1985 (1985-04-06) *
PATENT ABSTRACTS OF JAPAN vol. 009, no. 171 (C - 291) 16 July 1985 (1985-07-16) *

Cited By (18)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1939308A1 (de) * 2006-11-14 2008-07-02 ThyssenKrupp Steel AG Verfahren zum Herstellen eines Bauteils durch Wärmepresshärten und hochfestes Bauteil mit verbesserter Bruchdehnung
US9481916B2 (en) 2007-02-23 2016-11-01 Tata Steel Ijmuiden B.V. Method of thermomechanical shaping a final product with very high strength and a product produced thereby
WO2008102012A1 (en) * 2007-02-23 2008-08-28 Corus Staal Bv Method of thermomechanical shaping a final product with very high strength and a product produced thereby
US8721809B2 (en) 2007-02-23 2014-05-13 Tata Steel Ijmuiden B.V. Method of thermomechanical shaping a final product with very high strength and a product produced thereby
US8864921B2 (en) 2007-07-19 2014-10-21 Tata Steel Ijmuiden B.V. Method for annealing a strip of steel having a variable thickness in length direction
WO2009135776A1 (de) * 2008-05-06 2009-11-12 Thyssenkrupp Steel Ag Verfahren zum herstellen eines stahlformteils mit einem überwiegend ferritisch-bainitischen gefüge
US8888934B2 (en) 2008-05-06 2014-11-18 Thyssenkrupp Steel Europe Ag Method for producing a formed steel part having a predominantly ferritic-bainitic structure
WO2015039763A3 (en) * 2013-09-19 2015-08-20 Tata Steel Ijmuiden B.V. Steel for hot forming
EP3093359A4 (de) * 2014-01-06 2017-08-23 Nippon Steel & Sumitomo Metal Corporation Warmgeformtes element und verfahren zu herstellung davon
US10266911B2 (en) 2014-01-06 2019-04-23 Nippon Steel & Sumitomo Metal Corporation Hot-formed member and manufacturing method of same
US10774405B2 (en) 2014-01-06 2020-09-15 Nippon Steel Corporation Steel and method of manufacturing the same
WO2015144318A1 (en) * 2014-03-28 2015-10-01 Tata Steel Ijmuiden B.V. Method for hot forming a coated steel blank
WO2016016676A1 (fr) * 2014-07-30 2016-02-04 ArcelorMittal Investigación y Desarrollo, S.L. Procédé de fabrication de tôles d'acier, pour durcissement sous presse, et pièces obtenues par ce procédé
WO2016016707A1 (fr) * 2014-07-30 2016-02-04 Arcelormittal Procédé de fabrication de tôles d'acier pour durcissement sous presse, et pièces obtenues par ce procédé
US9845518B2 (en) 2014-07-30 2017-12-19 Arcelormittal Method for fabricating steel sheet for press hardening, and parts obtained by this method
RU2667189C2 (ru) * 2014-07-30 2018-09-17 Арселормиттал Способ изготовления упрочняемых в штампе стальных листов и полученные этим способом детали
WO2016146581A1 (en) * 2015-03-16 2016-09-22 Tata Steel Ijmuiden B.V. Steel for hot forming
CN112725687A (zh) * 2020-11-18 2021-04-30 邯郸钢铁集团有限责任公司 折弯及抗撞性能优良的边梁用750bl钢板及生产方法

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EP1929053B1 (de) 2011-06-22
US20120211128A1 (en) 2012-08-23
ZA200802385B (en) 2009-01-28
BRPI0616261B1 (pt) 2014-02-04
KR101453697B1 (ko) 2014-10-22
CA2623146C (fr) 2011-03-22
US10294557B2 (en) 2019-05-21
ATE513932T1 (de) 2011-07-15
CN101292049A (zh) 2008-10-22
RU2008115444A (ru) 2009-10-27
KR20130017102A (ko) 2013-02-19
RU2403291C2 (ru) 2010-11-10
MA29790B1 (fr) 2008-09-01
CN101292049B (zh) 2011-12-14
UA96739C2 (ru) 2011-12-12
CA2623146A1 (fr) 2007-03-29
EP1929053A1 (de) 2008-06-11
KR20080053312A (ko) 2008-06-12
WO2007034063A1 (fr) 2007-03-29
KR20110121657A (ko) 2011-11-07
KR20120099526A (ko) 2012-09-10
JP5386170B2 (ja) 2014-01-15
US8114227B2 (en) 2012-02-14
ES2366133T3 (es) 2011-10-17
EP2287344A1 (de) 2011-02-23
JP2009508692A (ja) 2009-03-05
PL1929053T3 (pl) 2011-10-31
US20080308194A1 (en) 2008-12-18
BRPI0616261A2 (pt) 2011-06-14

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