EP3013988A1 - Procédé et équipement de fabrication d'un composant en tôle d'acier trempé sous presse - Google Patents

Procédé et équipement de fabrication d'un composant en tôle d'acier trempé sous presse

Info

Publication number
EP3013988A1
EP3013988A1 EP14725013.8A EP14725013A EP3013988A1 EP 3013988 A1 EP3013988 A1 EP 3013988A1 EP 14725013 A EP14725013 A EP 14725013A EP 3013988 A1 EP3013988 A1 EP 3013988A1
Authority
EP
European Patent Office
Prior art keywords
component blank
component
heating device
temperature
forming tool
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.)
Withdrawn
Application number
EP14725013.8A
Other languages
German (de)
English (en)
Inventor
Peter Feuser
Bohuslav Masek
Thomas Schweiker
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Mercedes Benz Group AG
Original Assignee
Daimler AG
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Daimler AG filed Critical Daimler AG
Publication of EP3013988A1 publication Critical patent/EP3013988A1/fr
Withdrawn legal-status Critical Current

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/06—Surface hardening
    • 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
    • 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
    • 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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • 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
    • C22C38/28—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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0452—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment with application of tension

Definitions

  • the invention relates to a method for producing a press-hardened
  • Press hardened sheet steel components are used in car bodyworks, which should have high stability and no or only very slight deformations in the event of an accident.
  • Deformability can therefore not be used fully hardened components made of 22MnB5.
  • Alternatives to this are currently hot-formed components made of micro-alloyed steel or Tailored Welded Blanks with areas of press-hardenable and micro-alloyed steel.
  • a disadvantage of this approach is the low strength of the microalloyed steel after hot working. For example, the strength after hot forming is only about 600 megapascals. Thereby larger sheet thicknesses are required compared to stronger materials with similar ductility.
  • Sheet steel components which have a high elongation or elongation at break of 10% or more - measured in accordance with ISO 6892-1 - and a high strength, for example in a range of from 1,200 to 2,000 inclusive
  • Elongation at break and due to the high strength of such components would have very good accident characteristics and offer for the realization of shell construction in lightweight construction, especially in the passenger car and commercial vehicle sector.
  • Such mechanical properties would allow a significantly greater absorption of impact energy in the event of an accident, which would be accompanied by a particularly high occupant protection.
  • the realization of a low carbon content is desirable compared to bulk forming components to ensure weldability.
  • US 2012/0273096 A1 discloses an apparatus and a method for producing a press-hardened sheet steel component, wherein a component blank formed from a hot-workable steel material from which the sheet steel component is produced is heated to at least the austenitizing temperature of the steel material by means of a heating device. Subsequently, the component blank is hot-worked by means of a forming tool. Subsequently, the component blank is cooled in a component area to at least 200 ° Celsius in the forming tool, wherein another component area is maintained by tooling measures at a temperature above 200 ° Celsius. In a further step, the component blank is transferred from the forming tool to a heating device.
  • the component blank is annealed to stabilize the austenite by the heater.
  • the processing route proposed in US 2012/0273096 A1 in combination with the proposed material does not provide a solution to the problem described at the outset of producing a homogeneous component with particularly high elongation and, at the same time, particularly high strength.
  • a disadvantage of US 2012/0273096 A1 is also that tool areas must be heated to 550 ° C in order to cause an increase in ductility by partial bainitic and / or pearlitic-ferritic phase transformations. Such a tool temperature has the consequence that special and relatively expensive tool materials must be used. In addition to the cost of heating energy, there is a further disadvantage in the extended cycle time for making such a component. Since the bainitic and / or pearlitic-ferritic phase transformations are significantly slower compared to the martensite transformation, the residence time of the component in the tool is prolonged. The cycle time is reduced by exactly this amount, which causes additional costs.
  • Sheet steel components with particularly high ductility and at the same time particularly high strength in a simple, time-consuming and cost-effective manner can be produced.
  • the component blank while avoiding cooling of the component blank less than the martensite finish temperature M f , preferably less than 200 ° C, directly from the forming tool to the
  • Heating device is spent. Through this immediate spending
  • the press-hardened steel sheet components produced by the method according to the invention have a very high energy absorption capacity due to plastic deformation, so that they can convert a particularly high amount of impact energy into deformation energy, for example in an accident of a motor vehicle.
  • the press-hardened sheet steel components have improved crashworthiness due to the improved ductility, resulting in a particularly advantageous accident behavior
  • the wall thickness can be further reduced, so that press-hardened sheet steel components with a very small wall thickness and thus with a very low weight can be realized.
  • the method according to the invention allows a further increase in strength through the use of martensitic steel.
  • the usual martensitic structure is the hardest structural variation in steels. At the same time a purely martensitic structure is very brittle and depending on
  • Carbon content allows only a slight deformation, so that elongation values or elongations at break are usually below 7%.
  • the invention is based on the idea and the knowledge that it is for a
  • the tension between the martensitic needles and thereby to provide better conditions for a plastic behavior of the sheet steel components is required.
  • One way to do this is to form thin austenitic films between the martensitic needles. This is technically possible, for example, due to an incomplete transformation from the austenite phase to martensite.
  • martensite finish temperature M f When the cooling is stopped above the so-called martensite finish temperature M f , the austenite converts to martensite, but a small portion of the austenite remains.
  • the martensite finish temperature M f is the temperature at which the martensitic transformation is largely completed. If immediately after the structure of the sheet steel component or the component blank is kept at a slightly elevated temperature, moves the
  • Hot forming process can be used when starting. Due to the direct transfer of the component blank from the hot forming tool into the heating device (used for starting the component), the austenite is stabilized in the component blank and remains at room temperature in the component structure even after further cooling of the component blank or of the finished sheet steel component. This so - called retained austenite reduces the tension between the
  • Martensitic needles and causes the structure at high strengths at the same time has a relation to the martensite significantly better elongation or ductility.
  • a steel alloy with the following
  • Chromium (Cr) ranging from 0.1 to 1.5% by weight
  • Titanium (Ti) in the range of 0.01 to 0.2% by weight inclusive,
  • B Boron (B) in a range of 0.01 to 0.03 wt% inclusive - and up to 0.025 wt .-% nitrogen (N).
  • the invention also includes a system according to the preamble of claim 6, wherein it is provided according to the invention that the heating device directly adjoins the forming tool, so that the component blank below
  • Mass production can be made.
  • the heating device is used as a further heating device for stabilizing the
  • the heating device is preferably a roller hearth or walking beam furnace.
  • the forming tool is preferably temperature-controlled in the method
  • Cooling of the component blank by measures such as radiant heaters and / or
  • Shielding be avoided or kept low, so that a cooling of the component blank is avoided to less than 200 ° Celsius.
  • the component blank or can In the heating device, the component blank or can be
  • Component blanks rest on goods carriers, by means of which the component blank
  • the product carrier can preferably counteract a thermal distortion of the component.
  • Fig. 1 is a schematic representation of a method and a system for
  • FIG. 2 shows a schematic time-temperature profile of the component blank during the implementation of the method according to a first embodiment
  • Fig. 3 is a schematic representation of the system according to a second
  • Fig. 4 is a schematic representation of the system according to a third
  • FIG. 5 shows a schematic time-temperature curve of the component blank in FIG.
  • Fig. 1 shows a schematic representation of the flow of a method for
  • a press-hardened sheet steel component in the form of a sheet metal component from a component blank, which is formed from a hot-workable steel material.
  • the component blank is also referred to as semifinished product.
  • the method is based on the production of a sheet steel component or
  • Sheet metal component described from a component blank is also very well suited for the mass production of such press-hardened sheet steel components.
  • a plant designated as a whole by 10 in FIG. 1 is provided.
  • the component blank is subjected to the process, wherein the component blank is heated and cooled in the course of the process. This heating and cooling is particularly well recognizable from Fig. 2.
  • Fig. 2 shows a
  • Diagram 12 in which a time-temperature curve 14 of the component blank is entered.
  • the time t is plotted on the abscissa 16 of the diagram 12, the temperature being plotted on the ordinate 18 of the diagram 16.
  • the system 10 comprises a heating device 12,
  • the component blank is heated in a first step S1 of the method by means of the heating device 20 at least to, preferably above the austenitizing, temperature of the steel material from which the component blank is formed.
  • the heater 20 serves to austenitize the component blank in the first step S1.
  • the component blank may be in the form of a circuit board, for example.
  • the component blank is heated to a temperature above 900 ° Celsius by means of the heating device 20, wherein in FIG. 2 the temperature of 900 ° Celsius is indicated by a dashed line 22.
  • the system 10 further comprises a forming tool 24, which is integrated, for example, in a hydraulic press.
  • the heated component blank is from the
  • Forming tool 24 hot-formed in a second step S2 of the method.
  • the hot-formed component blank is cooled in the forming tool 24, but not cooled below 200 ° C (step S3). It can be provided that the component blank is cooled to a temperature between 200 ° Celsius and 500 ° Celsius. In other words, the component blank is cooled so that the
  • Component temperature after forming has not less than 200 ° Celsius and not more than 500 ° Celsius.
  • the system 10 also includes a further heating device in the form of a heating device 26, which may be formed as a furnace.
  • a heating device 26 which may be formed as a furnace.
  • the heating device 20 and / or the heating device 26 may be a roller hearth furnace, a walking beam furnace, a chain conveyor furnace or a rotary hearth furnace.
  • the use of other heating devices is conceivable.
  • other options such as contact plate heating, heating by radiant heater, inductive heating, conductive heating, infrared heating are also possible to heat or heat the component blank.
  • the heater 26 by waste heat of the
  • Heating device 20 be heated.
  • step S3 After cooling of the component blank in the forming tool 24 (step S3), the component blank from the forming tool 24 to or in the
  • Heating device 26 spent step S4.
  • the heating device 26 adjoins the forming tool 24 directly, so that the component blank is transported directly from the forming tool 24 to or into the heating device 26 while avoiding cooling of the component blank to less than 200 ° C.
  • This transfer can preferably by multi-axis
  • the heating device 26 may in particular be designed as a continuous furnace, so that the component blank is conveyed through the heating device 26.
  • the component blank is tempered in a fifth step S5 of the process with stabilization of the austenite in the structure of the component blank.
  • the dew point in the heating device and in the heating device is preferably controlled and set to values below 5 ° C. Preferably to values below -5 ° C.
  • the component blank is again slightly heated in the course of the annealing of the temperature to which the component blank has been cooled in the third step S3.
  • the component blank is cooled to 250 ° Celsius, where it is heated in the fifth step S5 to more than 200 ° Celsius and less than 500 ° Celsius and is held for a period of between 2 and 15 minutes in this temperature range.
  • the component blank is moved by the heating device 26 to or into a cutting device 28 of the system 10, wherein the component blank, in particular in the form of a circuit board, is cut by means of the cutting device 28 and cooled therein to room temperature (sixth step S6).
  • the component blank is brought by the cutting device 28 as part of a chaining to a finished trimming device 30 and finished by this in a seventh step S7 of the process finished and cleaned.
  • the time-temperature curve 14 illustrates the method according to a first embodiment, wherein other temperatures may be adjustable. By means of the method is thus a direct or indirect press hardening of
  • Component blanks representable which is preferably formed from a boron manganese steel.
  • the component blank can be uncoated or coated.
  • the component blank is hot-dip or hot-dip galvanized.
  • the sheet thickness of the component blank may be in a range of from 0.5 millimeter to 3 millimeters inclusive.
  • Fig. 3 shows the system 10 according to a second embodiment.
  • a so-called passage direction of the component blank is illustrated in Fig. 3, in which the component blank passes through the system 10.
  • the system 10 comprises a feed pass 32, which is arranged in the direction of passage in front of the heating device 20 for austenitizing, by means of which the component blank is conveyed into the heating device 20.
  • Heater 20 is followed by a discharge passage 34, by means of which the
  • Component blank is conveyed out of the heater 20.
  • the feed roller 32 and the discharge roller 34 may be components of the heater 20.
  • system 10 according to the second embodiment comprises a
  • Feed roller 36 by means of which the component blank after cooling, that is, after the forming tool 24 is conveyed into the heater 26.
  • the heating device 26 is adjoined by a further discharge pass 36, by means of which the component blank is conveyed out of the heating device 26 after starting.
  • the feed tray 36 and the discharge tray 38 may be components of the heating device 26.
  • FIG. 4 shows the installation 10 according to a third embodiment, in which 38 additional presses 40, 42, 44 for processing the component blank are connected to the delivery passage 38.
  • the press 40 By means of the press 40, the component blank is punched, for example.
  • the press 42 By means of the press 42, the component blank is cut, whereby the component blank is cut once again by means of the press 44.
  • 5 shows the time-temperature curve 14 for the method according to a second embodiment.
  • the component blank is heated at a heating rate T SO IH for the austenitization to the austenitizing temperature designated A and kept at the austenitizing temperature A during an austenitizing time B.
  • T SO II 2 indicates a cooling rate at which the component cools during and / or after its transformation, that is, during the second step S2 and / or during the third step S3, where T MS indicates a critical cooling rate for the formation of Martensite is marked.
  • Heating device 26 transfers, this transfer takes a transfer time D2. During this transfer time D2 it is avoided that the component blank cools to less than 200 ° Celsius.
  • the component blank is heated at a heating rate T s oll3 3Uf an annealing temperature E and maintained at the tempering temperature E during an annealing time F. After annealing, the component blank is cooled at a rate T SO

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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)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Heat Treatment Of Articles (AREA)

Abstract

L'invention concerne un procédé et un équipement de fabrication d'un composant en tôle d'acier trempé sous presse, comprenant les étapes consistant à : a) chauffer (étape S1) une ébauche de composant formée dans une tôle d'acier façonnable à chaud au moins à la température d'austénisation de l'acier à l'aide d'un dispositif chauffant (20), b) façonner à chaud (étape S2) l'ébauche de composant à l'aide d'un outil de façonnage (24), c) refroidir (étape S3) l'ébauche de composant dans l'outil de façonnage (24) à une température supérieure à la température de fin de transformation martensitique, de préférence à une température minimale de 200 °C, d) transférer (étape S4) l'ébauche de composant de l'outil de façonnage (24) dans un dispositif de chauffe (26), e) recuire (étape S5) l'ébauche de composant en stabilisant l'austénite à l'aide du dispositif de chauffe (26). L'ébauche de composant est transférée directement de l'outil de façonnage (24) dans le dispositif de chauffe (26) en évitant un refroidissement de l'ébauche de composant à une température inférieure à la température de fin de transformation martensitique, de préférence inférieure à 200 °C, (étape S4).
EP14725013.8A 2013-06-28 2014-05-17 Procédé et équipement de fabrication d'un composant en tôle d'acier trempé sous presse Withdrawn EP3013988A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102013010946.9A DE102013010946B3 (de) 2013-06-28 2013-06-28 Verfahren und Anlage zum Herstellen eines pressgehärteten Stahlblechbauteils
PCT/EP2014/001337 WO2014206514A1 (fr) 2013-06-28 2014-05-17 Procédé et équipement de fabrication d'un composant en tôle d'acier trempé sous presse

Publications (1)

Publication Number Publication Date
EP3013988A1 true EP3013988A1 (fr) 2016-05-04

Family

ID=50736038

Family Applications (1)

Application Number Title Priority Date Filing Date
EP14725013.8A Withdrawn EP3013988A1 (fr) 2013-06-28 2014-05-17 Procédé et équipement de fabrication d'un composant en tôle d'acier trempé sous presse

Country Status (5)

Country Link
US (1) US20160145707A1 (fr)
EP (1) EP3013988A1 (fr)
CN (1) CN105358718B (fr)
DE (1) DE102013010946B3 (fr)
WO (1) WO2014206514A1 (fr)

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CN105358718B (zh) 2018-09-14

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