EP2297367B9 - Procédé de production d'une pièce moulée en acier à structure à prédominance ferritique-bainitique - Google Patents

Procédé de production d'une pièce moulée en acier à structure à prédominance ferritique-bainitique Download PDF

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EP2297367B9
EP2297367B9 EP09741994.9A EP09741994A EP2297367B9 EP 2297367 B9 EP2297367 B9 EP 2297367B9 EP 09741994 A EP09741994 A EP 09741994A EP 2297367 B9 EP2297367 B9 EP 2297367B9
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max
temperature
steel
steel part
period
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EP2297367B1 (fr
EP2297367A1 (fr
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Jian Bian
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ThyssenKrupp Steel Europe AG
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ThyssenKrupp Steel Europe AG
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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
    • 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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C21D1/20—Isothermal quenching, e.g. bainitic 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
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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

Definitions

  • the invention relates to a method for producing a steel molding having a predominantly ferritic-bainitic structure.
  • hot-formed components which are made of high-strength steels .
  • steel moldings include the A and B pillars, the bumpers and door impact beams of a passenger car.
  • the sheet metal blanks concerned are heated to a deformation temperature generally above the austenitizing temperature of the respective steel and placed in the mold of a forming press in the heated state.
  • a rapid cooling In the course of the subsequent transformation undergoes the sheet metal blank or the molded part of it by the contact with the cool tool a rapid cooling, resulting in the component hardness structure. It may be sufficient if the component cools without active cooling alone by the contact with the tool. However, rapid cooling can also be supported by the fact that the tool itself is actively cooled.
  • a steel comparable to steel 22MnB5 is made of JP 2006104526 A known.
  • This known steel contains in addition to Fe and unavoidable impurities (in wt .-%) 0.05 - 0.55% C, max. 2% Si, 0.1-3% Mn, max. 0.1% P and max. 0.03% S.
  • additional amounts of 0.0002 - 0.005% B and 0.001 - 0.1% Ti can be added to the steel.
  • the respective Ti content serves for setting the nitrogen present in the steel. In this way, the boron present in the steel can develop its strength-increasing effect as completely as possible.
  • the JP 2006104526 A are made of the composite steel so first sheets, the then preheated to a temperature above the Ac 3 temperature, typically in the range of 850-950 ° C.
  • the martensitic microstructure ensuring the desired high strengths is formed in the component molded from the respective sheet metal blank.
  • the sheet metal parts heated to the stated temperature level can be shaped to complex-shaped components at relatively low forming forces. This is especially true for such sheet metal parts, which are made of high-strength steel and provided with a corrosion protection coating.
  • the components produced from boron-alloyed steels in the above-described manner achieve strengths of more than 1,500 MPa.
  • the required complete martensitic structure of the components has the result that the components have an insufficient residual elongation at break of 5-6% for many applications.
  • the relatively low residual elongation at break is associated with a low toughness. In applications where good deformation behavior is required in the event of a crash, this results in components which are produced from boron-alloyed steels in the known manner often no longer meet these requirements. This applies in particular when the components to be produced are parts for an automobile body.
  • a hardened metallic component is from the DE 102 08 216 C1 known.
  • a board or a preformed mold component each consisting of a steel of the above type, heated in a heating device to an austenitizing and then fed via a transport path to a curing process.
  • portions of the first type of board or die which are intended to have higher ductility properties in the final component are quenched from a predetermined cooling start temperature which is above the ⁇ - ⁇ transformation temperature. This quenching is terminated when a predetermined quench stop temperature is reached, before conversion to ferrite and / or perlite has taken place or after a low conversion in ferrite and / or perlite.
  • the board or the respective molded part is held isothermally to convert the austenite into ferrite and / or perlite.
  • the hardening temperature is kept just high enough for sufficient martensite formation to take place in the areas of the second type during a hardening process.
  • the cooling is carried out.
  • the resulting molded part is immersed in a separate operation in a quenching tank or the like to form the desired martensitic hardness structure.
  • This procedure also requires a process management that can be integrated into a modern production plant only with great effort.
  • there is also the problem with the components produced by this known method that while they have a high strength, they are at the same time so brittle that they do not meet the requirements for their deformability which are set in practice.
  • a process for the production of steel moldings is known, which is as a preform or board in the two-phase region, ie at a temperature between the Ac1 and the Ac3, is heated, and then formed in a (cooled) pressing tool and quenched at the same time.
  • the board preheated in each case to a temperature which is preheated in the two-phase mixing area in the thermoforming tool itself is cooled directly and so rapidly that after the Cooling in the component a multi-phase structure with a ferrite content is present.
  • the object of the invention was to provide a method with which it is possible to produce steel moldings in a process-technically simple manner, in which a high strength is combined with a good residual elongation at break.
  • a steel molding is produced with a predominantly ferritic-bainitic structure.
  • a starting material in the form of a steel plate or a preformed steel part is provided. If a hitherto undeformed steel plate is processed as a starting material, the entire process is referred to as a "one-step" process.
  • a preformed Processed steel part one speaks of a two-stage process, whereby in the first stage, a previously undeformed board is deformed so that the resulting steel component has not yet reached its final shape.
  • the respective starting material according to the invention consists of a steel of a known composition, which in addition to iron and unavoidable production-related impurities (in wt .-%) C: 0.02 - 0.6%, Mn: 0.5 - 2.0%, Al : 0.01 - 0.06%, Si: up to 0.4%, Cr: up to 1.2%, P: up to 0.035%, S: up to 0.035% and optionally one or more elements from the group "Ti, B, Mo, Ni, Cu, N", wherein - if present - Ti in a content of up to 0.05%, Cu in a content of up to 0.01%, B in contents of 0 , 0008 - 0.005%, Mo in contents of up to 0.3%, Ni in contents of up to 0.4%, N in contents of up to 0.01%.
  • the thus composed starting material (steel plate or preformed steel part) is so warmed at a lying between the Ac1 and the Ac3 temperature of the steel heating temperature that incomplete austenitization of the starting material occurs. Accordingly, at the end of the austenitizing phase, the microstructure of the starting material consists of ferrite and austenite.
  • the starting material is placed in a press mold and formed therein to the steel molding.
  • the press-hardening takes place in a temperature range in which the microstructure of the primary material in the two-phase region of ferrite and austenite is.
  • the steel molding is brought to a bainite formation temperature which is above the martensite start temperature but below the pearlite transformation temperature of the steel from which the steel sheet or the preformed steel part are respectively made.
  • the bainitization temperature to be set in each case depends on the bainite transformation temperature, which is differentiated upward in each case according to the chemical composition of the enriched austenite by the martensite start temperature and perlite transition temperature.
  • the cooling rate during press hardening is significantly influenced by the austenitizing and mold temperature. This must be so fast that the board cooled without conversion to the Bainitumwandlungstemperatur and kept constant at this temperature becomes.
  • This procedure it is achieved that at the end of the bainitization time in the steel mold part there is a structure which, in addition to the ferritic and bainitic parts of the structure, has minor amounts of retained austenite and possibly less than 5% of martensite.
  • the residual austenite contents in the resulting component which are essentially determined by the carbon content, can be up to 10%.
  • the steel mold After the end of the bainitization time, the steel mold is cooled to room temperature.
  • the temperature control with respect to the austenitizing process and the subsequent press hardening is controlled so that adjusts a mixed structure of ferrite, bainite and a proportion of retained austenite in the component.
  • the method according to the invention thus provides a steel component whose microstructure is characterized by a ferritic-bainitic microstructure.
  • This bainitic microstructure gives a component produced according to the invention improved deformation properties, in particular an improved residual elongation at break.
  • steel moldings produced according to the invention have an improved crash behavior, without the need for separate tempering treatment, since bainite can be regarded as a type of tempered martensite.
  • the method according to the invention makes it possible to cool the steel component more slowly than in the conventional methods in which the cooling takes place in the tool with the aim of martensitic To produce hardness structure. Therefore, in a method according to the invention the risk of the formation of component distortion is minimized and the components produced according to the invention are characterized by a particularly high dimensional accuracy.
  • the pressing tool can also be specifically heated to carry out the method according to the invention.
  • the ferrite and bainite in the structure of the steel molding at the end of Bainitmaschineszeit should be at least 90%, the ferrite and bainite each should be at least 30%.
  • the martensite portion of the steel molding is less than 1%, in particular limited to only traces.
  • the alloy of steel constituting the primary material to be processed in accordance with the present invention includes conventional MnB steels and temper steels alike.
  • a heat-treatment steel particularly suitable for carrying out the process according to the invention has C: 0.25-0.6%, Si: up to 0.4%, Mn: 0.5-2 , 0%, Cr: up to 0.6%, P: up to 0.02%, S: up to 0.01%, Al: 0.01-0.06%, Ti: up to 0.05% , Cu: up to 0.1% and B: 0.008 - 0.005%.
  • MnB steels which are suitable for the process according to the invention have C: 0.25-0.6%, Si: up to 0.4%, Mn: 0.5-2.0%, Cr: up to 1.2 %, P: up to 0.035%, S: up to 0.035%, Mo: up to 0.3%, Ni: up to 0.4% and Al: 0.01-0.06%.
  • the austenitizing temperature of the steels from which the starting material processed according to the invention is made is in the range of 750-810 ° C.
  • the heating time provided for the heating at the heating temperature is usually in the range of 6 to 15 minutes.
  • the starting material with a protective against corrosion metallic coating is provided.
  • This coating also protects the respective primary material (steel plate, preformed steel part) from the press mold during transport from the oven, where it is preheated to the austenitizing temperature.
  • the corrosion protection coating can be designed so that it protects an oxidation of the hot steel substrate with the ambient oxygen even when transported in air.
  • a particularly practical variant of the method according to the invention is characterized in that the press forming and the bainitization of the steel component produced in the course of the press molding takes place in the press forming tool.
  • a particularly advantageous variant of the invention provides that after the compression molding of the starting material, the steel mold part then obtained remains in the compression mold and brought there to the Bainitönstemperatur and held for the Bainitmaschineszeit.
  • the press-forming tool is preferably tempered such that the starting material, starting from a temperature above the bainitizing temperature, is already cooled to the bainitizing temperature during its compression deformation to the steel component.
  • the tool closing time of the pressing tool, within which the shaping, cooling and bainitization of the steel molding takes place is in this case usually 5 to 60 seconds, in particular 20 to 60 seconds.
  • the bainitization time is shorter by the time duration than the tool closing time, which is required to bring the respective starting material to the Bainitmaschinestemperatur.
  • bainitization in the press-forming tool, it is also conceivable, after the press-forming process, to remove the shaped steel part molded from the starting material from the press mold and to bring it to the bainite-forming temperature in a separate operation and to maintain it over the bainitization time.
  • Such a procedure can be displayed if a corresponding system technology is available.
  • such an approach can be used, for example, when a salt bath or a lead bath is available for heating up and holding at the bainitization temperature, into which the steel component can be brought after press molding.
  • the typical range of the bainitization temperature at which the baintization according to the invention is preferably carried out with the aim of forming a ferritic / bainitic structure is typically limited downwards by the martensite start temperature of the respective steel composition of the starting material, while being set lower than 500 ° C at the top can be used to avoid the formation of pearlite.
  • the technical complexity associated with carrying out the method according to the invention can also be reduced to a minimum by the fact that after the end of the Bainitmaschineszeit the cooling of the resulting steel molding is carried out in a simple manner in air.
  • suitable steel blanks which have been divided from a hot-rolled or cold-rolled flat product, such as tape or sheet. It is also possible to apply the method according to the invention to a steel part which has been preformed in a previous work step. The latter is useful, for example, when the shape of the steel component to be produced is so complex that several shaping steps are required for its production.
  • steel components produced according to the invention are particularly suitable for use as crash-relevant parts of an automobile body.
  • the inventive method is particularly suitable for the production of longitudinal and floor cross members, which should have a particularly good energy absorption capacity in practice.
  • a typical course of the temperature T during the performance of a method according to the invention is recorded over the time t.
  • a starting material to be deformed in each case to a steel component for example, with a prior to corrosion heated AlSi coating steel plate initially heated to an austenitizing temperature TA, which is below the Ac3 temperature but above the Ac1 temperature of the steel from which the steel plate is made in each case.
  • austenitizing temperature TA the steel plate is held for a time tA until the steel plate is completely heated so that there is a mixed structure of austenite and ferrite therein.
  • the area in which the steel has a structure is in Fig. 1 marked with A, while the area of the mixed structure of ferrite and austenite is marked with "A + F".
  • the steel plate After the end of the austenitizing time tA, the steel plate is transported to a press forming tool.
  • the transfer time required to close the press tool is in Fig. 1 denoted by tT.
  • the temperature TW at which the steel plate enters the die is still within the temperature range Ac3 - Ac1.
  • the press mold is equipped with a tempering device which keeps it at a constant temperature corresponding to the bainitization temperature TB.
  • the formed from the steel plate, with the press mold directly coming into contact steel mold part is cooled correspondingly over a cooling time tK to the bainitization temperature TB.
  • the bainitization temperature TB is above the martensite start temperature Ms but below the pearlite transformation temperature.
  • the area where perlite is formed is in Fig. 1 with P. characterized. Additionally is in Fig. 1 where F is the area in which pure ferrite is present and M is the area in which martensite is present.
  • the bainitization time t B is dimensioned so that at its end the structure of the steel component is essentially completely bainitic.
  • the cooling of the steel plate in the tempered pressing tool takes place within the cooling time tK so fast that the steel passes through the two-phase mixing A + F and a conversion in martensite M and perlite P is prevented, the martensite is avoided as completely as possible.
  • the tool closing time tW which comprises the cooling time tK and the bainitization time tB, is 5-60 seconds, depending on the complexity of the shaping of the steel component to be produced and the sheet thickness of the respectively processed steel plate.
  • the first steel plate SP1 was then heated to an austenitizing temperature TA of 780 ° C and held at this temperature TA for an austenitizing time tA of 6 minutes.
  • the steel plate SP1 has been transported in air for 6 to 12 s transfer time tT in air in a press mold, which has been heated to a bainitization temperature TB of 400 ° C and kept constant at this temperature TB.
  • the steel plate SP1 was then press-formed over a tool closing time tW of 40 seconds.
  • the total pressing time included the cooling time tK in which the steel board SP1 was cooled from the tool inlet temperature TW to the bainitizing temperature TB, and the bainitizing time tB in which the bainite structure was formed in the steel component thermoformed in the press forming tool.
  • the pressing tool has been opened and the steel component has been cooled to room temperature in still air.
  • the structure of the resulting steel molding had a ferrite content of 50%, a bainite content of 40%, a residual austenite content of 6% and a martensite content of 4%.
  • the second steel plate SP2 was so thoroughly heated at an austenitizing temperature TA of 800 ° C. that it, too, was only partially austenitized. After this partial austenitization, the second steel plate SP2 has undergone the same process steps as the first steel plate SP1.
  • the bainitic press hardening according to the invention is therefore a process for hot press hardening instead of the usually produced martensite structure, a structure consisting predominantly of ferrite and bainite is set by an isothermal conversion during press hardening on the respectively press-formed steel component.
  • the resulting ferritic / bainitic structure has improved residual elongation at high strength compared to martensite.

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Claims (15)

  1. Procédé de production d'une pièce moulée en acier à structure à prédominance ferritique-bainitique,
    - dans lequel on fournit un matériau précurseur, sous la forme d'une platine en acier ou d'une pièce d'acier préformée, fabriqué dans un acier qui contient (en % poids) C : 0,02 - 0,6 %, Mn : 0,5 - 2,0 %, Al : 0,01 - 0,06 %, Si : max. 0,4 %, Cr : max. 1,2 %, P : max. 0,035 %, S : max. 0,035 %,
    ainsi qu'éventuellement, un ou plusieurs éléments du groupe « Ti, Cu, B, Mo, Ni, N » avec les teneurs suivantes : Ti : max. 0,05 %, Cu : max. 0,01 %, B : 0,0008 - 0,005 % Mo : max. 0,3 %, Ni : max. 0,4 %, N : max. 0,01 %,
    ainsi que des teneurs résiduelles en fer et en impuretés inévitables,
    - dans lequel le matériau précurseur est chauffé à une température de chauffage (TA) située entre la température Ac1 et Ac3 de l'acier, de sorte qu'il se produit dans tous les cas une austénitisation incomplète du matériau précurseur,
    - dans lequel le matériau précurseur est placé dans un moule de compression et y est moulé pour former la pièce moulée en acier,
    - dans lequel la pièce moulée en acier est portée à une température de formation de bainite (TB) qui se situe au-dessus de la température de démarrage de la martensite (Ms), mais en-dessous de la température de transformation perlitique de l'acier dans lequel est fait le matériau précurseur,
    - dans lequel la pièce moulée en acier, après refroidissement, est maintenue, sur une période de bainitisation (tB), à la température de formation de bainite (TB) de manière essentiellement isotherme, jusqu'à ce qu'il se crée dans la pièce moulée en acier une structure composée principalement de ferrite et de bainite, dont la teneur en martensite s'élève à moins de 5 %, étant précisé qu'il peut subsister des teneurs résiduelles en austénite jusqu'à 10 %, et
    - dans lequel la pièce moulée en acier, au terme de la période de bainitisation (tB), est portée à température ambiante.
  2. Procédé conforme à la revendication 1, caractérisé en ce que l'acier contient (en % poids) : C : 0,25 - 0,6 %, Si : max. 0,4 %, Mn : 0,5 - 2,0 %, Cr : max. 0,6 %, P : max. 0,02 %, S : max. 0,01 %, Al : 0,01 - 0,06 %, Ti : max. 0,05 %, Cu : max. 0,1 %, B : 0,008 - 0,005 %
    ainsi que des teneurs résiduelles en fer et en impuretés inévitables.
  3. Procédé conforme à la revendication 1, caractérisé en ce que l'acier contient (en % poids) C : 0,25 - 0,6 %, Si : max. 0,4 %, Mn : 0,5 - 2,0 %, Cr : max. 1,2 %, P : max. 0,035 %, S : max. 0,035 %, Mo : max. 0,3 %, Ni : max. 0,4 %, Al : 0,01 - 0,06 %,
    ainsi que des teneurs résiduelles en fer et en impuretés inévitables.
  4. Procédé conforme à l'une des revendications précédentes, caractérisé en ce que la somme des proportions de ferrite et de bainite dans la structure de la pièce moulée en acier atteint au moins 90 % au terme de la période de bainitisation (tB).
  5. Procédé conforme à l'une des revendications précédentes, caractérisé en ce qu'au terme de la période de bainitisation (tB), la proportion en martensite de la pièce moulée en acier s'élève à moins de 1 %, et se limite notamment à des traces.
  6. Procédé conforme à l'une des revendications précédentes, caractérisé en ce que la température d'austénitisation (TA) atteint 750 à 810 °C.
  7. Procédé conforme à l'une des revendications précédentes, caractérisé en ce que le temps d'échauffement (Ta) prévu pour le chauffage du matériau à la température de chauffage (TA) atteint 6 à 15 minutes.
  8. Procédé conforme à l'une des revendications précédentes, caractérisé en ce que le matériau précurseur est pourvu d'un revêtement métallique anticorrosion.
  9. Procédé conforme à l'une des revendications précédentes, caractérisé en ce qu'après le moulage par compression du matériau précurseur, la pièce moulée en acier obtenue est portée à la température de formation de bainite (TB) dans le moule de compression et y est maintenue pendant la période de bainitisation (tB).
  10. Procédé conforme à la revendication 9, caractérisé en ce que le temps de pressage du moule à compression (tW) se situe entre 5 et 60 secondes, particulièrement entre 20 et 60 secondes.
  11. Procédé conforme à la revendication 10, caractérisé en ce que la période de bainitisation (tB) est plus courte que le temps de pressage du moule (tW).
  12. Procédé conforme à l'une des revendications 1 à 8, caractérisé en ce qu'après le moulage par compression, la pièce moulée en acier moulée par compression à partir du matériau précurseur est retirée du moule et lors d'une opération distincte, est portée à la température de formation de bainite (TB) et y est maintenue pendant la période de bainitisation (tB).
  13. Procédé conforme à l'une des revendications précédentes, caractérisé en ce que la température de bainitisation (TB) est supérieure à la température de démarrage de la martensite de la composition actuelle du matériau précurseur et inférieure à 500 °C.
  14. Procédé conforme à l'une des revendications précédentes, caractérisé en ce que le refroidissement de la pièce moulée en acier obtenue est effectué à l'air au terme de la période de bainitisation (tB).
  15. Procédé conforme à l'une des revendications précédentes, caractérisé en ce que la pièce moulée en acier est une pièce de carrosserie automobile.
EP09741994.9A 2008-05-06 2009-04-24 Procédé de production d'une pièce moulée en acier à structure à prédominance ferritique-bainitique Active EP2297367B9 (fr)

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DE102008022399A DE102008022399A1 (de) 2008-05-06 2008-05-06 Verfahren zum Herstellen eines Stahlformteils mit einem überwiegend ferritisch-bainitischen Gefüge
PCT/EP2009/054961 WO2009135776A1 (fr) 2008-05-06 2009-04-24 Procédé de production d'une pièce moulée en acier à structure à prédominance ferritique-bainitique

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WO2012169638A1 (fr) * 2011-06-10 2012-12-13 株式会社神戸製鋼所 Article moulé par pressage à chaud, procédé pour produire celui-ci, et tôle d'acier mince pour moulage à la presse à chaud
DE102012024626A1 (de) 2012-12-17 2014-06-18 GM Global Technology Operations LLC (n. d. Gesetzen des Staates Delaware) Fahrzeugkarosserie und Verfahren zur Fertigung eines Formteils dafür
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CN104498830B (zh) * 2014-12-30 2017-06-23 南阳汉冶特钢有限公司 一种合金结构钢及其生产方法
WO2017098302A1 (fr) * 2015-12-09 2017-06-15 Arcelormittal Structure de soubassement de carrosserie de véhicule comportant un élément de renfort entre une poutre longitudinale et une partie de bas de caisse côté inférieur
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EP2297367B1 (fr) 2017-06-07
EP2297367A1 (fr) 2011-03-23
CA2725210C (fr) 2016-05-31
US20110132502A1 (en) 2011-06-09
DE102008022399A1 (de) 2009-11-19
WO2009135776A1 (fr) 2009-11-12
US8888934B2 (en) 2014-11-18
CA2725210A1 (fr) 2009-11-12

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