EP2655672B1 - Procédé pour produire des éléments de construction durcis pourvus de zones de différentes duretés et/ou ductilités - Google Patents

Procédé pour produire des éléments de construction durcis pourvus de zones de différentes duretés et/ou ductilités Download PDF

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Publication number
EP2655672B1
EP2655672B1 EP11807691.8A EP11807691A EP2655672B1 EP 2655672 B1 EP2655672 B1 EP 2655672B1 EP 11807691 A EP11807691 A EP 11807691A EP 2655672 B1 EP2655672 B1 EP 2655672B1
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European Patent Office
Prior art keywords
temperature
sections
plate
heated
cooling
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EP11807691.8A
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German (de)
English (en)
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EP2655672A2 (fr
Inventor
Andreas Sommer
Harald Schwinghammer
Thomas Kurz
Siegfried Kolnberger
Martin Rosner
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Voestalpine Stahl GmbH
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Voestalpine Stahl GmbH
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Publication date
Priority claimed from DE102010056265.3A external-priority patent/DE102010056265C5/de
Priority claimed from DE102010056264.5A external-priority patent/DE102010056264C5/de
Priority claimed from DE102011053939.5A external-priority patent/DE102011053939B4/de
Priority claimed from DE102011053941.7A external-priority patent/DE102011053941B4/de
Application filed by Voestalpine Stahl GmbH filed Critical Voestalpine Stahl GmbH
Publication of EP2655672A2 publication Critical patent/EP2655672A2/fr
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • C—CHEMISTRY; METALLURGY
    • 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
    • C23C2/26—After-treatment
    • C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
    • 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
    • C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
    • C23C2/29—Cooling or quenching

Definitions

  • the invention relates to a method for producing hardened components with areas of different hardness and / or ductility with the features of claim 1.
  • press-hardened components made of sheet steel are used, particularly in automobiles.
  • These press-hardened components made of sheet steel are high-strength components that are used in particular as safety components in the bodywork area.
  • a sheet steel blank is heated above the so-called austenitizing temperature and, if necessary, kept at this temperature until a desired degree of austenitizing is reached.
  • This heated blank is then transferred to a molding tool and in this molding tool it is formed into the finished component in a single-stage forming step and, in this case, by the cooled molding tool at a speed that exceeds the critical hardening speed is cooled.
  • the hardened component is thus produced.
  • the component is first formed almost completely, if necessary in a multi-stage forming process. This formed component is then likewise heated to a temperature above the austenitizing temperature and, if necessary, kept at this temperature for a required time.
  • This heated component is then transferred and inserted into a molding tool which already has the dimensions of the component or the final dimensions of the component, possibly taking into account the thermal expansion of the preformed component. After the particularly cooled tool has been closed, the preformed component is therefore only cooled in this tool at a speed above the critical hardening speed and thereby hardened.
  • the direct method is somewhat easier to implement here, but only allows shapes that can actually be produced with a single forming step, i.e. relatively simple profile shapes.
  • Zinc has the advantage that zinc not only provides a barrier protection layer like aluminum, but also a cathodic protection against corrosion.
  • zinc-coated press-hardened components fit better into the overall corrosion protection concept of the vehicle body, since these are fully galvanized in today's common construction. In this respect, contact corrosion can be reduced or excluded.
  • the zinc-iron phase diagram shows that above 782 ° C there is a large area in which liquid zinc-iron phases occur as long as the iron content is low, in particular less than 60%. However, this is also the temperature range in which the austenitized steel is hot worked. However, it is also pointed out that if the deformation takes place above 782 ° C, there is a high risk of stress corrosion due to liquid zinc, which presumably penetrates into the grain boundaries of the base steel, which leads to macro cracks in the base steel. In addition, if the iron content is less than 30% in the coating, the maximum temperature for forming a safe product without macro cracks is lower than 782 ° C. This is the reason why this is not a direct forming process, but an indirect forming process. This is to circumvent the problem described.
  • a method for hot forming a coated steel product wherein the steel material has a zinc or zinc alloy coating which is formed on the surface of the steel material and the steel base material with the coating is heated to a temperature of 700 ° C to 1000 ° C and hot worked wherein the coating has an oxide layer consisting mainly of zinc oxide before the steel base material with the zinc or zinc alloy layer is heated in order to then prevent the zinc from evaporating when heated.
  • a special procedure is provided for this.
  • a method for hot forming a steel in which a component made of a given boron-manganese steel is heated to a temperature at the Ac 3 point or higher, is kept at this temperature and then the heated steel sheet is formed into the finished component, wherein the molded component is quenched by cooling from the molding temperature during molding or after molding in such a way that the cooling rate to the MS point corresponds to at least the critical cooling rate and that the average cooling rate of the molded component from the MS point to 200 ° C is in the range of 25 ° C / s to 150 ° C / s.
  • the applicant is known a method for producing hardened components from sheet steel, in which case molded parts from a steel sheet provided with a cathodic corrosion protection are cold formed and a heat treatment for the purpose of austenitization follows, with an end trimming of the molded part before, during or after the cold forming Molded part and required punching or the creation of a hole pattern and the cold forming as well as the trimming and the punching and arrangement of the hole pattern on the component are 0.5% to 2% smaller than the dimensions that the finally hardened component should have, whereby the For heat treatment, cold-formed molded part is then heated to a temperature at least partially with the admission of atmospheric oxygen, which enables the steel material to be austenitized and the heated component is then transferred into a tool and a so-called formh Curing is carried out, in which the component is cooled and thereby hardened by applying and pressing (holding) the component using the form hardening tools and the cathodic corrosion protection coating consists essentially of zinc and also one or
  • an oxide skin is formed on the surface of the anti-corrosion coating from the elements with an affinity for oxygen during heating, which protects the cathodic anti-corrosion layer, in particular the zinc layer.
  • the method takes into account the thermal expansion of the component due to the scaling down of the component in relation to its final geometry, so that neither calibration nor reshaping is necessary during hot-stamping.
  • a method for producing partially hardened steel components is known to the applicant, in which a plate made of a hardenable steel sheet increases in temperature is subjected, which is sufficient for quench hardening and after reaching a desired temperature and possibly a desired holding time, the blank is transferred to a forming tool by forming the blank into a component and quenching it at the same time, or the blank is cold formed and that by the Cold forming component obtained is then subjected to a temperature increase, the temperature increase being carried out in such a way that a temperature of the component is reached that is necessary for quench hardening and the component is then transferred to a tool in which the heated component is cooled and thereby quenched is hardened, while during the heating of the circuit board or the component for the purpose of increasing the temperature to a temperature necessary for hardening in the areas that should have a lower hardness and / or higher ductility, absorption masses are present or with a low level Gap are spaced, the absorption mass with regard to its
  • the object of the invention is to create a method for producing sheet steel components, in particular provided with a corrosion protection layer, with areas of different hardness or ductility, with local stresses in the component as well as warpage and cracks such as those otherwise caused by "liquid metal assisted cracking" can be avoided.
  • the method according to the invention can be carried out successfully both in the so-called indirect process and in the direct process with regard to the mechanical properties.
  • the blanks are formed into the finished component before heating, possibly reduced in all three spatial axes by an expected thermal expansion.
  • the component obtained in this way is then heated in an oven, with absorption masses or insulating components or the like being provided in the areas of the component that are not to be hardened or are to be hardened to a lesser extent in order to achieve areas of different temperatures.
  • a temperature is reached in these areas which is below Ac 3 or possibly even Ac 1 and to this extent restricts or prevents quench hardening by converting the austenite into martensite.
  • the aim is to achieve complete austenitization, which leads to martensitic hardness during quenching.
  • the board is heated without being deformed and the areas of the board that are not to be hardened or to be hardened to a lesser extent are also brought into contact with absorption masses, which, due to their thermal conductivity and heat capacity, reduce the heating of the sheet metal or also arrange insulation components accordingly .
  • This board is then reshaped.
  • the temperature of the blank is made uniform. This means that the heated blank with the areas of different temperatures is subjected to an intermediate cooling step before being inserted into the forming tool, in which the hotter areas are actively cooled to the temperature or the temperature range of the colder areas. How this is done is explained later.
  • transformation-retarded steels are used according to the invention. This means that the conversion to martensite takes place later, so that the components have areas after the equalization of the temperature and the placement in the hardening tool or the hardening / forming tool, despite the uniform temperature, which due to the subsequent rapid cooling with a cooling rate above the critical Hardening speed are hardened, while the other areas, which have not been brought to the austenitizing temperature, are softer.
  • the advantage here is that the equalization of the temperature also results in uniform deformability, so that local stresses due to different temperatures or different thermomechanical properties are avoided and, in particular, thinning in the border areas between cold and hot areas is avoided.
  • the composition of the steel alloy is set within the scope of the usual composition of a manganese-boron steel (22MnB5) so that quench hardening is achieved through a delayed conversion of austenite into martensite and thus the presence of austenite even at the lower temperature is carried out below 780 ° C or lower, so that at the moment in which mechanical tension is applied to the steel, which in connection with a zinc melt and austenite would lead to the "liquid metal embrittlement", just no or very few liquid Zinc phases are present. It is thus possible to achieve sufficient quench hardening by means of a boron-manganese steel adjusted according to the alloying elements without provoking excessive or damaging crack formation.
  • intermediate cooling is necessary before forming for crack-free forming.
  • the intermediate cooling can take place in one or more stages, for example.
  • additional periods can be planned in order to equalize the temperature of the sheets that have differently heated areas, for example in order to not bring about any hardening in colder areas, in particular waiting until the Austenitizing heated areas have a temperature that has adjusted to the temperature of the less heated areas.
  • This adjustment of the temperature profile can in particular also take place through active cooling of the hotter areas, in particular by blowing on these areas or the like, with the cold or colder areas being covered, shielded or insulated during the cooling of the heated areas.
  • air nozzles for blowing in the special case of sheets of different temperature, can be controlled via pyrometers, which are, for example, outside the press and the furnace in a separate system, as are the corresponding nozzles.
  • the cooling options are not limited to air nozzles, cooled tables can also be used on which the circuit boards are positioned accordingly and which include cooled and non-cooled areas, so that the areas of the circuit board to be cooled come to rest on cooled areas of the table and, for example, through Pressing or sucking can be brought into heat-conducting contact.
  • cooling press in which the press geometry is extremely simple and inexpensive due to the flat blanks, the areas of the tool in which the blanks are to be cooled are correspondingly liquid-cooled, while the areas that are not to be cooled are opposite, for example
  • the cold metal of the press can be shielded by means of insulating layers that are inserted into the tools, or these areas are slightly heated or kept at temperature, for example by means of induction.
  • a conventional boron-manganese steel for use as a press-hardening steel material is adjusted with regard to the conversion of the austenite into other phases in such a way that the conversion shifts to deeper regions and martensite can be formed.
  • the alloying elements boron, manganese, carbon and optionally chromium and molybdenum are used as transformation retarders in such steels.
  • a holding phase can be provided according to the invention in the temperature range of the peritectic, so that the solidification of the zinc coating is promoted and driven before it is subsequently reshaped.
  • Figure 1 one recognizes a favorable temperature profile for an austenitized steel sheet, whereby it can be seen that after heating to a temperature above the austenitizing temperature and the corresponding transfer to a cooling device, a certain cooling already takes place. This is followed by a rapid intermediate cooling step.
  • the intermediate cooling step is advantageously carried out at cooling rates of at least 15 K / s, preferably at least 30 K / s, more preferably at least 50 K / s.
  • the blank is then transferred to the press and the forming, in the range from 450 ° C to 700 ° C, and below the peritectical temperature of the iron-zinc system, and hardening are carried out.
  • the temperature equalization is carried out in such a way that there are still differences in the temperatures of the (previously) hot areas and the (previously) colder areas that do not exceed 75 ° C, in particular 50 ° C ( in both directions).

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Oil, Petroleum & Natural Gas (AREA)
  • Heat Treatment Of Articles (AREA)
  • Coating With Molten Metal (AREA)
  • Shaping Metal By Deep-Drawing, Or The Like (AREA)

Claims (8)

  1. Procédé de fabrication d'un composant en acier trempé avec des zones ductiles ou trempées différemment, une platine étant découpée, et soit la platine découpée est chauffée par zones partielles à une température ≥Ac3 et, le cas échéant, maintenue à cette température pendant une durée déterminée afin de réaliser la formation d'austénite, puis la platine chauffée par zones partielles est transportée dans une matrice, façonnée dans la matrice et refroidie et donc trempée dans la matrice à une vitesse supérieure à la vitesse de trempe critique, soit façonnée à froid et la platine façonnée est chauffée par zones partielles à une température ≥Ac3 et, le cas échéant, maintenue à cette température pendant une durée déterminée afin de réaliser la formation d'austénite, puis la platine façonnée et chauffée par zones partielles est transportée dans un appareil de trempe, trempée dans l'appareil de trempe à une vitesse supérieure à la vitesse de trempe critique,
    le matériau en acier étant réglé pour ralentir à la transformation de telle sorte qu'un durcissement par trempe a lieu grâce à la transformation de l'austénite en martensite à une température de façonnage se trouvant dans la plage de 450 °C à 700 °C et en dessous de la température péritectique du système zinc-fer, un refroidissement actif ayant lieu après la chauffe et avant le façonnage pendant lequel la platine ou des pièces de la platine ou la platine façonnée ou des zones de celle-ci sont refroidies à une vitesse de refroidissement >15K/s, le matériau en acier comprenant comme retardateur de transformation les éléments bore, manganèse et carbone et en option le chrome et le molybdène, le matériau en acier étant utilisé avec l'analyse suivante (toutes les données en % massique) : Carbone (C) 0,08-0,6 Manganèse (Mn) 0,8-3,0 Aluminium (Al) 0,01-0,07 Silicium (Si) 0,01-0,5 Chrome (Cr) 0,02-0,6 Titane (Ti) 0,01-0,08 Azote (N) < 0,02 Bore (B) 0,002-0,02 Phosphore (P) < 0,01 Soufre (S) < 0,01 Molybdène (Mo) < 1
    le restant étant constitué de fer et d'impuretés issues de la fusion et pour les platines, qui présentent des plages correspondantes pour atteindre des plages de trempe différentes aux puissances de chauffe différentes, le refroidissement actif est effectué de telle sorte que les zones austénitisées préalablement chauffées soient adaptées au niveau de la température aux zones moins fortement chauffées (+/- 50 K), de manière à ce que la platine soit déposée dans la matrice à une température uniforme avec une différence de 75 °C maximale.
  2. Procédé selon la revendication 1, caractérisé en ce qu'un matériau en acier est utilisé avec l'analyse suivante (toutes les données sont en % massique) : Carbone (C) 0,08-0,30 Manganèse (Mn) 1,00-3,00 Aluminium (Al) 0,03-0,06 Silicium (Si) 0,01-0,20 Chrome (Cr) 0,02-0,3 Titane (Ti) 0,03-0,04 Azote (N) 0,007 Bore (B) 0,002-0,006 Phosphore (P) < 0,01 Soufre (S) < 0,01 Molybdène (Mo) < 1
    le restant étant constitué de fer et d'impuretés issues de la fusion.
  3. Procédé selon l'une des revendications précédentes, caractérisé en ce que la platine est chauffée dans un four à une température ≥Ac3 maintenue à cette température pendant une durée déterminée, la platine est ensuite refroidie à une température comprise entre 500 °C et 600 °C afin d'obtenir une solidification de la couche de zinc puis transportée dans la matrice pour y être façonnée.
  4. Procédé selon l'une des revendications précédentes, caractérisé en ce que le refroidissement actif est effectué de telle sorte que le taux de refroidissement soit >30 K/s.
  5. Procédé selon la revendication 4, caractérisé en ce que le refroidissement actif est effectué de telle sorte que le refroidissement a lieu avec plus de 50 K/s.
  6. Procédé selon l'une des revendications précédentes, caractérisé en ce que pour les platines, qui présentent des plages correspondantes pour atteindre des plages de trempe différentes aux puissances de chauffe différentes, le refroidissement actif est effectué de telle sorte que les zones austénitisées préalablement chauffées soient adaptées au niveau de la température aux zones moins fortement chauffées (+/- 50 K), de manière à ce que la platine soit déposée dans la matrice à une température essentiellement uniforme.
  7. Procédé selon l'une des revendications précédentes, caractérisé en ce que la progression du refroidissement et/ou la température d'enfournement dans la matrice est/sont surveillée(s) au moyen de capteurs, notamment des pyromètres, et en ce que le refroidissement est régulé en conséquence.
  8. Procédé selon l'une des revendications précédentes, caractérisé en ce qu'un matériau en acier revêtu de zinc ou d'un alliage de zinc est utilisé comme matériau en acier.
EP11807691.8A 2010-12-24 2011-12-22 Procédé pour produire des éléments de construction durcis pourvus de zones de différentes duretés et/ou ductilités Active EP2655672B1 (fr)

Applications Claiming Priority (5)

Application Number Priority Date Filing Date Title
DE102010056265.3A DE102010056265C5 (de) 2010-12-24 2010-12-24 Verfahren zum Erzeugen gehärteter Bauteile
DE102010056264.5A DE102010056264C5 (de) 2010-12-24 2010-12-24 Verfahren zum Erzeugen gehärteter Bauteile
DE102011053939.5A DE102011053939B4 (de) 2011-09-26 2011-09-26 Verfahren zum Erzeugen gehärteter Bauteile
DE102011053941.7A DE102011053941B4 (de) 2011-09-26 2011-09-26 Verfahren zum Erzeugen gehärteter Bauteile mit Bereichen unterschiedlicher Härte und/oder Duktilität
PCT/EP2011/073889 WO2012085253A2 (fr) 2010-12-24 2011-12-22 Procédé pour produire des éléments de construction durcis pourvus de zones de différentes duretés et/ou ductilités

Publications (2)

Publication Number Publication Date
EP2655672A2 EP2655672A2 (fr) 2013-10-30
EP2655672B1 true EP2655672B1 (fr) 2020-12-16

Family

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Family Applications (5)

Application Number Title Priority Date Filing Date
EP11808645.3A Active EP2655674B1 (fr) 2010-12-24 2011-12-22 Procédé de formage et de durcissement de tôles d'acier revêtues
EP11807691.8A Active EP2655672B1 (fr) 2010-12-24 2011-12-22 Procédé pour produire des éléments de construction durcis pourvus de zones de différentes duretés et/ou ductilités
EP11811025.3A Active EP2655675B1 (fr) 2010-12-24 2011-12-22 Procédé pour produire des éléments de construction durcis pourvus de zones de différentes duretés et/ou ductilités
EP11808211.4A Active EP2655673B1 (fr) 2010-12-24 2011-12-22 Procédé de fabrication de composants durcis
EP11811026.1A Active EP2656187B1 (fr) 2010-12-24 2011-12-22 Procédé de fabrication de composants durcis

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EP11808645.3A Active EP2655674B1 (fr) 2010-12-24 2011-12-22 Procédé de formage et de durcissement de tôles d'acier revêtues

Family Applications After (3)

Application Number Title Priority Date Filing Date
EP11811025.3A Active EP2655675B1 (fr) 2010-12-24 2011-12-22 Procédé pour produire des éléments de construction durcis pourvus de zones de différentes duretés et/ou ductilités
EP11808211.4A Active EP2655673B1 (fr) 2010-12-24 2011-12-22 Procédé de fabrication de composants durcis
EP11811026.1A Active EP2656187B1 (fr) 2010-12-24 2011-12-22 Procédé de fabrication de composants durcis

Country Status (8)

Country Link
US (2) US20140020795A1 (fr)
EP (5) EP2655674B1 (fr)
JP (2) JP5727037B2 (fr)
KR (3) KR20130132566A (fr)
CN (5) CN103547686B (fr)
ES (5) ES2858225T3 (fr)
HU (5) HUE054465T2 (fr)
WO (5) WO2012085256A2 (fr)

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Publication number Priority date Publication date Assignee Title
JP5808724B2 (ja) * 2012-10-31 2015-11-10 アイシン高丘株式会社 アルミニウム合金材のダイクエンチ装置およびダイクエンチ方法
DE102013100682B3 (de) * 2013-01-23 2014-06-05 Voestalpine Metal Forming Gmbh Verfahren zum Erzeugen gehärteter Bauteile und ein Strukturbauteil, welches nach dem Verfahren hergestellt ist
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KR101582922B1 (ko) 2016-01-07
US20140020795A1 (en) 2014-01-23
EP2655675A2 (fr) 2013-10-30
EP2656187A2 (fr) 2013-10-30
ES2848159T3 (es) 2021-08-05
US20140027026A1 (en) 2014-01-30
KR20130126962A (ko) 2013-11-21
ES2851176T3 (es) 2021-09-03
HUE053150T2 (hu) 2021-06-28
EP2655673A2 (fr) 2013-10-30
WO2012085253A2 (fr) 2012-06-28
CN103547686B (zh) 2016-11-23
JP2014507556A (ja) 2014-03-27
JP2014505791A (ja) 2014-03-06
JP5727037B2 (ja) 2015-06-03
EP2656187B1 (fr) 2020-09-09
CN103415630A (zh) 2013-11-27
EP2655672A2 (fr) 2013-10-30
HUE052381T2 (hu) 2021-04-28
ES2829950T8 (es) 2021-06-10
CN103384726B (zh) 2016-11-23
EP2655674A2 (fr) 2013-10-30
HUE055049T2 (hu) 2021-10-28
US10640838B2 (en) 2020-05-05
CN103415630B (zh) 2015-09-23
ES2858225T3 (es) 2021-09-29
WO2012085256A2 (fr) 2012-06-28
WO2012085247A2 (fr) 2012-06-28
WO2012085251A2 (fr) 2012-06-28
CN103384726A (zh) 2013-11-06
CN103392014A (zh) 2013-11-13
WO2012085247A3 (fr) 2012-08-16
CN103547686A (zh) 2014-01-29
HUE054867T2 (hu) 2021-10-28
ES2858225T8 (es) 2022-01-05
WO2012085251A3 (fr) 2012-08-16
EP2655674B1 (fr) 2021-02-03
WO2012085248A3 (fr) 2012-08-16
ES2829950T3 (es) 2021-06-02
WO2012085253A3 (fr) 2012-08-16
KR20130132566A (ko) 2013-12-04
WO2012085248A2 (fr) 2012-06-28
KR20130132565A (ko) 2013-12-04
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