EP2446064B1 - Procédé de fabrication d'une pièce trempée à chaud sous presse et utilisation d'un produit en acier pour la fabrication d'une pièce trempée à chaud sous presse - Google Patents

Procédé de fabrication d'une pièce trempée à chaud sous presse et utilisation d'un produit en acier pour la fabrication d'une pièce trempée à chaud sous presse Download PDF

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EP2446064B1
EP2446064B1 EP10725185.2A EP10725185A EP2446064B1 EP 2446064 B1 EP2446064 B1 EP 2446064B1 EP 10725185 A EP10725185 A EP 10725185A EP 2446064 B1 EP2446064 B1 EP 2446064B1
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Prior art keywords
steel
steel product
product
hot press
component
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German (de)
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EP2446064A1 (fr
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Evelin Ratte
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Outokumpu Nirosta GmbH
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Outokumpu Nirosta GmbH
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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
    • C21D6/00—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
    • 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
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/001—Heat treatment of ferrous alloys containing Ni
    • 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
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • 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
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese

Definitions

  • the invention relates to a method for producing a hot-press-hardened component and a use of a steel product for producing a hot-press-hardened component.
  • hot-pressed components made of high-strength steels are used in areas of the body that can be exposed to particularly high loads in the event of a crash.
  • steel blanks which are divided from cold or hot rolled steel strip, are heated to a deformation temperature which is generally above the austenitizing temperature of the respective steel and, when heated, are placed in the tool of a forming press.
  • the sheet metal blank or the component formed from it is rapidly cooled by contact with the cool tool.
  • the cooling rates are set so that the component Hardness structure results. It may be sufficient if the component cools down by active contact with the tool without active cooling. However, rapid cooling can also be supported by actively cooling the tool itself.
  • the DE 15 33 381 B1 describes the use of a steel for the production of razor blades, in particular thin ribbon-shaped razor blades with a maximum thickness of 0.038 mm were rolled down.
  • These blades are subjected to a heat treatment which involves an initial heating to a temperature between 1000 and 1150 ° C followed by cooling to room temperature, the cooling being carried out between water-cooled blocks.
  • a subsequent further cooling to below 0 ° C and a related tempering at temperatures between 100 and 450 ° C for a short time should lead to a maximum Vickers hardness. Only after such heat treatment is the cutting edge of the cold blade processed.
  • the object of the invention was to provide a method with which high-strength components protected against corrosive attacks can be manufactured more easily than with the known methods mentioned above.
  • this object has been achieved in that, according to the invention, the work steps specified in claim 1 are carried out when producing a high-strength component from a flat steel product.
  • the solution of the above-mentioned object according to the invention consists in that according to the invention a flat steel product is used for the production of a component.
  • the invention is based on the knowledge that a certain class of known stainless steels is suitable for hot press hardening.
  • the use according to the invention of such stainless steels for hot press hardening has the advantage that there is no risk of corrosion, neither during hot shaping nor during the hardening process, despite the high temperatures involved. Instead, the alloy components contained in the steel used according to the invention protect the processed steel product from corrosive attacks even during these process steps.
  • high-strength components which are optimally protected against corrosion can be produced by hot press hardening without the protective measures which are always necessary in the case of low-alloy steels of the type previously used for hot press hardening.
  • a first group of steels suitable for press hardening are the unstabilized ferrites, which include steel standardized under material number 1.4003. Ferritic steels can completely or partially convert to martensitic when quenching temperatures above the austenitizing temperature. These steels are particularly suitable for direct press hardening, but can also be formed in indirect processes.
  • a sheet metal blank made from a suitable flat steel product is formed in one go into the respective component and subjected to the heat treatment required to set the desired hardness.
  • Martensite Another group of stainless steels suitable for press hardening are Martensite. Above 900 to 1000 ° C, these steels have an austenitic structure with a high solubility for carbon. Martensite forms during their cooling.
  • the steels known under material numbers 1.4021 and 1.4034 are typical representatives of this type of steel.
  • Martensitic-ferritic steels in which the structure contains higher proportions of ferrite in addition to martensite, can also be press-hardened.
  • This group of steels includes, for example, steel standardized under material number 1.4006.
  • Typical martensitic steels have carbon contents of 0.08-1% by weight. They are hardened in air. However, their mechanical strength can be further increased by quenching with higher cooling rates.
  • Martensitic steels with low C contents up to max. 0.06% are partially alloyed with up to 6% nickel. This composition means that austenite is partially formed after quenching and tempering. Steels of this type are referred to as “nickel martensitic” or “supermartensitic”. Such steels are particularly suitable for direct press hardening, but can also be formed in indirect processes.
  • the use of a stainless steel product according to the invention allows for the manufacture of hot press hardened components and the resulting procedure a significantly simplified manufacture of components compared to the state of the art of hot press hardening, the mechanical properties and corrosion protection of which are ideally suited for demanding applications such as the construction of automobile bodies.
  • a component which is hot-press-hardened according to the invention is produced from a steel product which consists of a stainless steel which, as compulsory components (in% by weight), C: 0.010-1.200%, P: up to 0.1%, S: up to 0, 1%, Si: 0.10 - 1.5%, Cr: 10.5 - 20.0% and the balance contains iron and unavoidable impurities.
  • the martensite hardness of the steel can be controlled by the amount of carbon contained in a steel used according to the invention, which is in the range of 0.01-1.2% by weight.
  • Optimal properties of the component produced according to the invention by hot press hardening result in this regard if the steel used according to the invention contains 0.01-1.0% by weight of C, in particular 0.01-0.5% by weight.
  • Levels of 0.1 - 1.5% by weight of Si act as an antioxidant and increase the strength of the steel.
  • the high Cr content of steels used according to the invention contributes significantly to corrosion resistance, particularly in high-temperature use. It leads at room temperature as well as at high temperatures Formation of a Cr oxide layer on the surface, so that the steel product processed according to the invention does not require additional corrosion protection either during the heat treatment or in later practical use.
  • the Cr content in the material is more dimensionally stable at high temperatures, such as are present when the invention is heated to the respective austenitizing temperature TA, than with the corrosion-sensitive MnB grades conventionally used for hot press hardening. Accordingly, it is easier to process steel products used according to the invention at high temperatures.
  • the transport from the heating device to the insertion into the respective pressing tool can also take place without the risk of an oxidation of the surface in ambient air which affects the processing result.
  • An optimally balanced ratio of alloy costs and positive effects of the Cr content of a steel used according to the invention is obtained if its Cr content is between 11 and 19% by weight, in particular 11-15% by weight.
  • the P and S contents are each limited to 0.1% by weight in order to prevent negative effects of these elements on the mechanical properties of the steel processed according to the invention.
  • the steel used according to the invention can optionally include one or more elements from the group "Mn, Mo, Ni, Cu, N, Ti, Nb, B, V, Al, Ca, As, Sn, Sb, Pb, Bi "H” with the proviso that the relevant elements - if present - each is present in the following contents (figures in% by weight) Mn: 0.10 - 3.0%, Mo: 0.05 - 2.50%, Ni: 0.05 - 8.50%, Cu : 0.050 - 3.00%, N: 0.01 - 0.2%, Ti: up to 0.02%, Nb: up to 0.1%, B: up to 0.1%, V: up to 0.2%, Al: 0.001 - 1.5%, Ca: 0.0005 - 0.003%, As: 0.003 - 0.015%, Sn: 0.003 - 0.01%, Sb: 0.002 - 0.01%, Pb: up to 0.01%, Bi: up to 0.01% and H: up
  • Mn in contents of 0.10-3.0% by weight supports the desired austenite formation at high temperatures, so that the hardness structure sought according to the invention is formed.
  • Molybdenum in a content of 0.05 - 2.50% by weight helps to improve the corrosion resistance.
  • Nickel can be present in a stainless steel used according to the invention in a content of 0.05-8.50% by weight, in particular 0.05-7.0% by weight, in order to likewise increase the corrosion resistance and the austenite formation to support high temperatures, such as are achieved in the procedure according to the invention during the heat treatment preceding the press molding. This effect occurs with sufficient effectiveness even at contents of up to 1.5% by weight of nickel, so that the upper limit of the Ni content range can be limited to this value in a practical embodiment of the invention.
  • Cu can also be used in a steel used according to the invention to support the formation of the hardness structure desired austenite formation in contents of 0.050 - 3.00 wt .-% are added.
  • the martensite hardness of the steel used according to the invention can also be controlled via nitrogen contents of 0.01-0.2% by weight, in particular 0.01-0.02% by weight.
  • Ti in contents of up to 0.02% by weight minimizes the risk of cracking during the casting of the stainless steel required in the course of the production of a steel product processed according to the invention.
  • Contents of up to 0.1% by weight of niobium also contribute to improving the formability of the steel during the production of the steel product used according to the invention.
  • B in contents of up to 0.1% by weight, in particular 0.05% by weight also has a positive effect on the avoidance of cracks during the strip casting of a steel processed according to the invention and reduces the risk of surface ripping in conventional continuous casting.
  • the martensite hardness of the steel processed according to the invention can also be controlled by adding boron.
  • V in contents of up to 0.2% by weight, in particular 0.1% by weight, like Nb improves the formability during the casting of the steel used according to the invention.
  • Al in contents of 0.001-1.50% by weight, in particular 0.001-0.03% by weight, and Ca in contents of 0.0005-0.003% by weight contribute to optimizing the degree of purity Steel used according to the invention during its casting in strip or continuous casting.
  • Sn in contents of 0.003-0.01% by weight, Sb in contents of 0.002-0.01% by weight, Pb in contents of up to 0.01% by weight .-% and Bi in contents of up to 0.01% by weight are added to steel according to the invention in order to avoid crack formation during strip casting or to avoid surface defects when hot-rolling cast steel used according to the invention.
  • the contents of H in a steel processed according to the invention are finally limited to up to 0.0025% by weight in order to prevent the formation of so-called “delayed cracking", i.e. to avoid a delayed, hydrogen-induced crack formation under the conditions prevailing in practical use.
  • the steel product used according to the invention and assembled in the manner explained above can be a flat steel product produced by hot or cold rolling, that is to say, for example, a blank obtained from a hot or cold-rolled stainless steel sheet or strip.
  • a semi-finished product as a steel product which has been preformed from a corresponding flat steel product before it is processed in a manner according to the invention.
  • the steel product used according to the invention can be a so-called “tailored blank” made up of at least two interconnected Steel flat product blanks can be formed, which differ from each other in terms of their thickness or physical properties.
  • differently loaded sections of the component produced and procured according to the invention can be assigned optimally adapted materials to the loads that occur.
  • only a partial section of the flat steel product used according to the invention consists of a stainless steel of the composition specified according to the invention, while another section is produced from a conventional low-alloy and rust-sensitive steel, if this takes into account the respective local conditions and loads is indicated under which the component produced according to the invention is used in practice.
  • the formation of the hardness structure in the component obtained according to the invention after hot press hardening can be controlled by the level of the austenitizing temperature reached in each case.
  • the steel product processed according to the invention is heated in the course of step b) to an austenitizing temperature which is above the Ac3 temperature of the stainless steel (Ac3 temperature: temperature at which the conversion into Austenite is complete).
  • Ac3 temperature temperature at which the conversion into Austenite is complete.
  • the rapid cooling of the hot-press-hardened component according to the invention required to form the hardness structure can take place in a known manner in the pressing tool itself, which is provided with a suitable cooling device for this purpose.
  • the cooling can also take place in a separate working step after the hot press molding, if it is ensured that the component still has a sufficiently high temperature after the end of the hot press process.
  • both the heating of the steel product before hot press molding and the cooling after hot press molding can be restricted to certain sections of the steel product if zones with different mechanical properties are to be produced on the finished component.
  • the flat steel product is preferably heated in a closed oven. However, heating by induction or conduction is also conceivable.
  • a component that is highly resilient at any point can be produced in accordance with the invention by heating and cooling the shaped steel part in such a way that a hardness structure is formed over its entire volume.
  • cooling speeds of a maximum of 25 K / s, in particular a maximum of 20 K / s are sufficient in the procedure according to the invention, and particularly good work results are obtained when the cooling speed is at a maximum of 15 K / s is limited.
  • the cooling rate should be at least 0.1 K / s, in particular at least 0.2 - 1.3 K / s. Cooling rates above 25 K / s have shown that there is an unintentionally rapid hardening, which leads to limited formability. Cooling rates of between 5 and 20 K / s are preferably set, with increasing cooling rate higher strengths can be achieved in the component.
  • the formation of the individual zones of different characteristics can also be influenced by heating certain zones of the surfaces of the compression molding tool that come into contact with the steel product, so that cooling of the steel product that leads to a hardness structure, for example, is reliably avoided there.
  • Components produced in accordance with the invention regularly have a tensile strength of at least 900 MPa in the areas in which they have a hardness structure and there they have an elongation A80 of at least 2%.
  • components manufactured by hot press hardening of a steel product produced from a stainless steel are particularly suitable as parts of bodies for motor vehicles, commercial vehicles or rail vehicles, for airplanes or high-strength structural elements.
  • Fig. 1 shows a diagram in which the elongation at break A80 in% is plotted against the tensile strength Rm in MPa for various steels.
  • the strength of the press-hardened components is converted into a tensile strength Rm via the hardness and the tables given in DIN 50150.
  • the values for Vickers hardness HV10 and tensile strength shown in DIN 50150 are determined for unalloyed and low-alloy steels.
  • Sheet metal parts were formed from the blanks produced from steels S1 - S7 by direct, press hardening. The Vickers hardness HV10 was then measured for the sheet metal parts obtained in this way and the tensile strength was determined therefrom in the manner described in DIN 50150.
  • Table 4 HV10 Rm [MPa] Rm [MPa] A80 measured determined according to DIN 50150 measured DIN 10002 S1, S1 ' 335 1075 1030 8.8 S2 417 1120 S3 470 1520 S4, S4 ' 397 1278 1350 6.5 S5, S5 ' 500 1630 1621 4.1 S6 561 1848 S7 360 1155
  • Table 5 Steel S3 Steel S4 Steel S5 Steel S6 Steel S7 Steel S8 t8 / 5 [s] K [K / s] HV10 HV10 HV10 HV10 HV10 HV10 40 7.50 419 501 587 672 679 375 150 2.00 499 200 1.50 654 649 230 1.30 415 600 0.50 575 485 650 0.46 467 700 0.43 387 523 3500 0.09 250 5000 0.06 421
  • cooling rates are sufficient to form the hardness structure, which are clearly below the cooling rates usually used in press hardening.
  • the steels processed in accordance with the invention still convert martensitically with slow cooling. This has an advantageous effect on the production process, since the forming tool does not have to be cooled as much, particularly in the case of single-stage, direct mold hardening.
  • Components produced by direct die hardening often still undergo heat treatment in practice. This is particularly the case when the molded parts are components for motor vehicle bodies that are stove-enamelled in the course of their further processing.
  • the influence of such or a comparable tempering treatment on the strength and elongation values of the press-molded components in the manner according to the invention is on the basis of components made of one of the steels S2, S3 and S7, produced in the manner according to the invention by direct press-hardening, which have been tempered under the conditions given in Table 6 and for which, in the course of the tempering treatment, those shown in Table 6 likewise specified properties.
  • Table 6 stolen Tempering temperature [° C] HV10 Rm, determined according to DIN 50150 [MPa] S2 170 351 1130 250 350 1126 500 346 1110 S3 170 467 1510 250 467 1510 500 454 1470 S7 170 356 1145 250 341 1145 500 311 998
  • tempering in the temperature range of 170-500 ° C. covered by the tests leads at most to a very slight decrease in the strength of the components produced according to the invention.
  • a board made of S9 steel has been processed. After solution annealing, the board had a tensile strength Rm of 816 MPa.
  • the board obtained in this way was then formed into a component to simulate the compression molding process and held at 820 ° C. for a period of 30 minutes, and then in the tool depending on the area of the component or the time of contact to be quenched with a cooling rate of approx. 15 K / s.
  • the component had a hardness HV10 of 340, which corresponds to a tensile strength Rm of approximately 1015 MPa.
  • FIG. 1 The attached diagram shows the elongation A80 over the tensile strength Rm for components E1, E2, E3 produced in the manner according to the invention from blanks composed of steels S1, S4 and S5.
  • Fig. 1 for two components, which are made by conventional hot press hardening from the commonly used for this purpose, C ⁇ 0.2%, Si ⁇ 0.4%, Mn ⁇ 1.4%, P ⁇ 0.025%, S ⁇ 0.01%, Cr + Mo ⁇ 0.5%, Ti ⁇ 0.05% and B ⁇ 0.005% (data in% by weight) containing MBW 1500 steel, which indicate elongation values A80 above the respective tensile strength value Rm.
  • components E1, E2 produced from the ferritic steel S1 and the martensitic steel S4 have a combination of elongation value and tensile strength that is superior to that of conventionally produced components, while the third component produced according to the invention has better tensile strength with still good elongation values.
  • components produced according to the invention are more corrosion-resistant or do not require any additional corrosion protection coatings.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
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Claims (12)

  1. Procédé de fabrication d'une pièce trempée à chaud sous presse pour une carrosserie de voiture, pour des avions ou pour des éléments de construction à haute résistance, comportant les étapes de travail suivantes :
    a) mise à disposition d'un produit en acier qui est fabriqué au moins partiellement à partir d'un acier inoxydable ayant la composition suivante (% en poids)
    C : 0,010 - 1,200 %,
    P : jusqu'à 0,1 %,
    S : jusqu'à 0,1 %
    Si : 0,10 -1,5 %,
    Cr : 10,5 - 20,0 %
    ainsi qu'au choix un ou plusieurs éléments parmi le groupe constitué de « Mn, Mo, Ni, Cu, N, Ti, Nb, B, V, Al, Ca, As, Sn, Sb, Pb, Bi, H » à la condition que :
    Mn: 0,10 - 3,0 %,
    Mo : 0,05 - 2,50 %,
    Ni : 0,05 - 8,50 %,
    Cu : 0,050 - 3,00 %,
    N : 0,01 - 0,2 %,
    Ti : jusqu'à 0,02 %,
    Nb : jusqu'à 0,1 %,
    B : jusqu'à 0,1 %,
    V : jusqu'à 0,2 %,
    Al : 0,001 - 1,50 %,
    Ca : 0,0005 - 0,003 %,
    As : 0,003 - 0,015 %,
    Sn : 0,003 - 0,01 %,
    Sb : 0,002 - 0,01 %,
    Pb : jusqu'à 0,01 %,
    Bi : jusqu'à 0,01 %,
    H : jusqu'à 0,0025 %,
    le reste étant du fer et des impuretés inévitables ;
    b) Réchauffement du produit en acier à une température d'austénitisation supérieure à la température Ac3 de l'acier inoxydable ;
    c) Trempage à chaud sous presse du produit en acier réchauffé pour obtenir une pièce dans un outil de pressage ;
    d) Refroidissement au moins d'une section de la pièce obtenue à une vitesse de refroidissement qui est suffisamment élevée de sorte à ce qu'il se forme, dans la zone rapidement refroidie respectivement, une structure de trempe, la pièce obtenue comportant, dans les zones dans lesquelles elle présente une structure de trempe, une résistance à la traction d'au moins 900 MPa, et un allongement A80 d'au moins 2 %.
  2. Procédé selon la revendication 1, caractérisé en ce que la pièce en acier moulé est refroidie dans la matrice de moulage sous pression de sorte à former une structure de trempe.
  3. Procédé selon l'une des revendications précédentes, caractérisé en ce que les surfaces de la matrice de moulage sous pression en contact avec le produit en acier sont partiellement réchauffées.
  4. Procédé selon l'une des revendications 1 ou 2, caractérisé en ce que la pièce en acier moulé est refroidie de sorte à ce qu'il se forme sur l'ensemble de son volume une structure de trempe.
  5. Procédé selon l'une des revendications précédentes, caractérisé en ce que la vitesse de refroidissement avec laquelle le produit en acier est au moins partiellement refroidi, est tout au plus de 25 K/s.
  6. Procédé selon la revendication 5, caractérisé en ce que la vitesse de refroidissement avec laquelle le produit en acier est au moins partiellement refroidi, est au moins de 0,1 K/s.
  7. Procédé selon l'une des revendications précédentes, caractérisé en ce que le produit en acier est un produit plat en acier.
  8. Procédé selon l'une des revendications 1 à 6, caractérisé en ce que le produit plat en acier est un produit semi-fini préformé.
  9. Procédé selon l'une des revendications précédentes, caractérisé en ce que le produit en acier est formé à partir d'au moins deux découpes de produit plat en acier reliées l'une à l'autre qui se différencient par leur épaisseur ou leurs caractéristiques physiques.
  10. Procédé selon l'une des revendications précédentes, caractérisé en ce que la teneur en C de l'acier inoxydable est limitée à 0,5 % en poids.
  11. Procédé selon l'une des revendications précédentes, caractérisé en ce que la teneur en Cr de l'acier inoxydable est de 11 - 19 % en poids.
  12. Utilisation d'un produit en acier qui se compose au moins partiellement d'un acier inoxydable qui contient (en % en poids)
    C : 0,010 - 1,200 %,
    P: jusqu'à 0,1 %,
    S : jusqu'à 0,1 %,
    Si : 0,10 - 1,5 %,
    Cr : 10,5 - 20,0 %
    ainsi qu'au choix un ou plusieurs éléments parmi le groupe constitué de « Mn, Mo, Ni, Cu, N, Ti, Nb, B, V, Al, Ca, As, Sn, Sb, Pb, Bi, H » à la condition que :
    Mn : 0,10 - 3,0 %,
    Mo : 0,05 - 2,50 %,
    Cu : 0,050 - 3,00 %,
    Ni : 0,05 - 8,50 %,
    N : 0,01 - 0,2 %,
    Ti : jusqu'à 0,02 %,
    Nb : jusqu'à 0,1 %,
    B : jusqu'à 0,1 %,
    V : jusqu'à 0,2 %,
    Al : 0,001 - 1,50 %,
    Ca : 0,0005 - 0,003 %,
    As : 0,003 - 0,015 %,
    Sn : 0,003 - 0,01 %,
    Sb : 0,002 - 0,01 %,
    Pb : jusqu'à 0,01 %,
    Bi : jusqu'à 0,01 %,
    H : jusqu'à 0,0025 %,
    le reste étant du fer et des impuretés inévitables,
    pour la fabrication d'une pièce trempée à chaud sous presse pour une carrosserie de voiture, pour des avions ou pour des éléments de construction à haute résistance, la pièce obtenue présentant, dans les zones dans lesquelles elle présente une structure de trempe, une résistance à la traction d'au moins 900 MPa et un allongement A80 d'au moins 2 %.
EP10725185.2A 2009-06-24 2010-06-17 Procédé de fabrication d'une pièce trempée à chaud sous presse et utilisation d'un produit en acier pour la fabrication d'une pièce trempée à chaud sous presse Active EP2446064B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102009030489A DE102009030489A1 (de) 2009-06-24 2009-06-24 Verfahren zum Herstellen eines warmpressgehärteten Bauteils, Verwendung eines Stahlprodukts für die Herstellung eines warmpressgehärteten Bauteils und warmpressgehärtetes Bauteil
PCT/EP2010/058527 WO2010149561A1 (fr) 2009-06-24 2010-06-17 Procédé de fabrication d’une pièce trempée à chaud sous presse, utilisation d’un produit en acier pour la fabrication d’une pièce trempée à chaud sous presse et pièce trempée à chaud sous presse

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EP2446064A1 EP2446064A1 (fr) 2012-05-02
EP2446064B1 true EP2446064B1 (fr) 2020-04-22

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EP (1) EP2446064B1 (fr)
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CN (1) CN102803519B (fr)
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DE (1) DE102009030489A1 (fr)
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JP2012530847A (ja) 2012-12-06
CN102803519A (zh) 2012-11-28
US20120273092A1 (en) 2012-11-01
EP2446064A1 (fr) 2012-05-02
CN102803519B (zh) 2015-08-19
WO2010149561A1 (fr) 2010-12-29
DE102009030489A1 (de) 2010-12-30
US9534268B2 (en) 2017-01-03
MX2011013403A (es) 2012-04-11
KR20120039533A (ko) 2012-04-25
BRPI1011811B1 (pt) 2018-01-23
JP5755644B2 (ja) 2015-07-29
BRPI1011811A2 (pt) 2016-03-29
KR101708446B1 (ko) 2017-02-20
KR20170010090A (ko) 2017-01-25

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