EP3144077A1 - Procede destine a la fabrication d'un composant en acier haute resistance - Google Patents

Procede destine a la fabrication d'un composant en acier haute resistance Download PDF

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Publication number
EP3144077A1
EP3144077A1 EP16188522.3A EP16188522A EP3144077A1 EP 3144077 A1 EP3144077 A1 EP 3144077A1 EP 16188522 A EP16188522 A EP 16188522A EP 3144077 A1 EP3144077 A1 EP 3144077A1
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EP
European Patent Office
Prior art keywords
steel
forming
temperature
forming tool
product
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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EP16188522.3A
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German (de)
English (en)
Inventor
Peter Höfel
Maximilian Nagel
Overrath Jens Dr.
Tomitz Andreas Dr.
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ThyssenKrupp AG
ThyssenKrupp Hohenlimburg GmbH
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ThyssenKrupp AG
ThyssenKrupp Hohenlimburg GmbH
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Filing date
Publication date
Application filed by ThyssenKrupp AG, ThyssenKrupp Hohenlimburg GmbH filed Critical ThyssenKrupp AG
Publication of EP3144077A1 publication Critical patent/EP3144077A1/fr
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
    • B21D22/20—Deep-drawing
    • B21D22/208—Deep-drawing by heating the blank or deep-drawing associated with 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
    • 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
    • C21D6/005—Heat treatment of ferrous alloys containing Mn

Definitions

  • the invention relates to a method for producing a component from a flat steel product, which consists of a manganese steel, in which the flat steel product is inserted into a forming tool and deformed in the forming tool to the component.
  • Flat steel products can be formed particularly economically by deep drawing into components.
  • deep drawing forming tools which usually called a stamp, also called upper mold or male, and a counter-mold, also called die or drawing ring, and include a hold-down.
  • the punch and the hold-down are moved to a starting position so that the sheet metal blank to be formed can be inserted into the then accessible space between the punch and the die. Then the hold down braces the sheet metal blank on his Border area. Then the punch is lowered, so that the sheet metal blank is pressed into the die.
  • the hold-down machine has the task of holding the edge area clamped in such a way that no cracks or creases are formed as the sheet metal blank is pressed into the die as a result of the material flow that begins in the process.
  • the sheet material is loaded in the radial and axial directions relative to the axis of movement of the punch.
  • the drawing depth is the travel of the punch from the first contact with the sheet metal blank at the level of the blank holder to the end of the deep drawing process at the contact surface between the drawing part bottom and punch ( Doege, E., Behrens, B.-A: Manual Umformtechnik, Hannover, Springer Verlag, 2010, p. 319 ff .).
  • the maximum formability of the sheet material is referred to as "maximum limit ratio (ß max )" or "maximum deep drawing ratio". This is limited by the formation of wrinkles when the hold-down pressure is too low and the formation of cracks when the hold-down pressure is too high.
  • This limit drawing ratio (ß max ) can be achieved with exactly one exact hold-down force. Technologically, this ratio can be determined with reasonable effort only in approximation. As an approximate value for the maximum draw ratio ß is determined.
  • Ferritic materials of higher strength in particular micro-alloyed fine-grain steels with tensile strengths Rm of At least 650 MPa are only conditionally suitable for highly complex deep drawing operations, since such materials generally do not provide the drawing ratio required for the respective forming operation.
  • Rm tensile strengths
  • High manganese steels in which the high Mn contents can be combined with high Al and C contents, have a stacking fault energy of 20-60 mJ / m 2 have a stable austenitic structure. This structure undergoes no or only a negligible minor transformation into another microstructural phase in a deformation of the material, even if the transformation is carried out at temperatures of at most 400 ° C.
  • TWIP T winning I nduced P lasticity
  • the stacking fault energy can be adjusted specifically for steels of the type in question. This allows you to set a range of stable austenite.
  • the austenite can be further stabilized, which is why even at room temperature and below, the formation of martensite can be prevented by forming.
  • the dynamic Hall Petch effect leads to the emergence mechanical twins in the austenite grains which, like grain boundaries, prevent the dislocation slip.
  • materials with TWIP properties undergo their strong solidification during cold forming.
  • conventional high manganese steels exhibit a maximum draw ratio that is too low for the production of complex shaped components by deep drawing.
  • From the DE 10 2008 020 757 A1 is a method for forming sheet metal workpieces of iron-manganese steel with up to 40 wt .-% Mn, up to 15 wt .-% Al, up to 2 wt .-% C, up to 6 wt .-% Si and Optional contents of Ti, W, Nb, Cr, Ni and V known in which the respective sheet metal workpiece is inserted at a temperature of 50 - 1000 ° C in a mold and is formed by this mold, wherein the residence time of the workpiece in the mold. 1 to 20 s. It is considered crucial here that the workpiece has a temperature lying in the temperature range mentioned, when it comes into contact with the forming tool.
  • a method for the production of components from an austenitic austenitic lightweight structural steel in which a sheet material is formed in one or more stages, which has a temperature-dependent TRIP and / or TWIP effect during the forming.
  • the known method provides for reshaping the respective sheet material depending on the desired property profile in two variants. Namely, in order to achieve a particularly high toughness of the component, the forming is to be carried out at a temperature above room temperature avoiding the TRIP / TWIP effect, whereas the forming is carried out at a temperature below the room temperature in order to obtain the TRIP / TWIP Enhance effect, if a high component strength is desired.
  • a steel which, in addition to iron and unavoidable impurities (in% by weight), contains 0.04 to 1.0% C, 0.05 to less contains 4.0% Al, 0.05 to 6.0% Si and 9.0 to less than 18.0% Mn, and optionally additionally, depending on requirements, may have contents of Cr, Cu, Ti, Zr, V and Nb , Such a steel is in the DE 10 2004 061 284 A1 described.
  • the invention has achieved this object in that in the manufacture of components from a
  • a flat steel product consisting of a high Mn steel undergoing the operations specified in claim 1.
  • the flat steel product to be formed is consequently placed in a forming tool and deformed in the forming tool to form the component in accordance with the prior art set forth in the introduction.
  • the product temperature of the flat steel product now corresponds to the ambient temperature when placed in the forming tool, ie in the range of 15-35 ° C.
  • the product temperature of the flat steel product is only increased in the forming tool to a forming temperature of 100-350 ° C.
  • the thus heated flat steel product is formed in the forming tool to the component and finally removed the resulting component from the forming tool.
  • the invention is based on the knowledge that by heating the steel flat product to a relative to the ambient temperature increased, but 350 ° C, especially 300 ° C, not exceeding heating, the maximum draw ratio improved in proportion to the increase in temperature.
  • the maximum draw ratio even with high-manganese steels, which are insufficiently deformable at room temperature, to values of 2.20 and increase more, in which even complex component shapes by deep drawing of flat steel products can be generated reliably error-free, the Steels with high Mn contents exist.
  • this is possible in the inventive method also in the forming temperature range of up to 150 ° C, in which the high-manganese steels of each to be deformed flat steel products usually have pronounced TWIP properties.
  • the heating to the particular forming temperature occurs through the contact of the flat steel product with the components of the forming tool, via which the actual shaping takes place, ie the hold-down device, the punch or the die.
  • the method of conductive heating is preferably used for components with a high surface area in the hold-down of greater than or equal to 50%.
  • the flat steel product in the forming tool can also be heated inductively.
  • the inductive heating method is preferably used for components with a small surface area in the hold-down area of less than 50%.
  • the relevant components are selectively brought to the respective forming temperature, the energy required for this is low, since even during the forming process itself heat is generated, which contributes to the inventive tempering of the forming tool.
  • a complex cooling of the forming tool As is required in processes in which the reshaped boards are heated to temperatures of well above 350 ° C in front of the forming tool and then cooled in the forming tool, can account for inventive procedure.
  • the residence time is the time that elapses between the commencement of the heating process coinciding with the end of the insertion and the removal of the component obtained, the forming process taking place between the heating process and the removal of the component obtained.
  • the residence time is composed of a time required for the heating process, a time required for the forming process, and a holding time in which the formed part rests after forming in the forming tool. Dwell times, which must pass in the conventional high-temperature forming before the resulting component can be removed from the forming tool, are shortened so.
  • the procedure according to the invention makes it possible to reduce the holding times to less than one second, whereby residence times of less than 6 s can be achieved. This can be achieved in that the component can be removed from the forming tool immediately after completion of the forming process.
  • the steel of the flat steel product to be formed during the forming process has a maximum draw ratio ⁇ of at least 2.20, can with increased Reliability can be ensured by the fact that the forming temperature to which the flat steel product is brought in the forming tool is at least 100 ° C. Even in the temperature range of 100 ° -180 ° C., high-manganese steels according to the findings of the invention have markedly improved maximum draw ratios ⁇ , wherein forming temperatures of 150 ° -180 ° C. already lead to very good forming behavior with an optimum ratio of thermal energy input and deformability ,
  • thermoforming capability which enables process-reliable shaping by deep-drawing, even in the case of particularly complex and complex components, arises according to the findings of the invention when the forming temperature is at least 180 ° C., in particular limited to 260 ° C., wherein In practice, a forming temperature range of 180 - 250 ° C has been found to be particularly favorable. At above 180 ° C lying forming temperatures T u , as with reference to the attached Fig. 1 shown regularly maximum draw ratios ß of more than 2.26 achieved.
  • Carbon is present in the steel from which a flat steel product to be formed in accordance with the present invention may be present at levels of at least 0.37 weight percent to stabilize the austenite and adjust the corresponding stacking fault energy.
  • the presence of C contributes to the strength of the material. If the carbon contents are too low, this results in insufficient austenite stability before and during the forming process and a correspondingly insufficient maximum draw ratio. The insufficient austenite stability would lead to martensite formation and a concomitant increased risk of delayed cracking. In the presence of too much carbon, fine and coarse carbides can be formed which reduce the ductility and thus also the maximum Reduce the drawing ratio ß. The maximum content of C is therefore limited to 0.43 wt .-%.
  • Manganese is added to the steel from which a flat steel product to be formed according to the invention can be alloyed in order to sufficiently stabilize the austenite content in the initial state in the structure.
  • Mn increases the stacking fault energy together with carbon, aluminum and silicon. This must be brought to a minimum value of 15 mJ / m 2 in order to sufficiently stabilize the austenite at room temperature and above during deformation. Due to the stabilization of the austenite, this also remains after deformation and "twins" are formed, as a result of which the steel has an optimized hardening and elongation behavior during plastic deformation in the cold state.
  • TWIP effect winning induced plasticity
  • body components, chassis components, drive components, structural components and the like known that have to absorb high kinetic energy in the event of a crash and derive in deformation energy.
  • austenite has more slip-line systems than a cubic-centered phase, it offers much higher forming capacity.
  • the maximum draw ratio ß is directly dependent on the forming capacity. The austenite must therefore be stable even at elevated temperatures, since otherwise a second phase can be formed during the forming and the maximum draw ratio ⁇ would be lower.
  • the Mn content of steel flat products to be processed according to the invention is set to at least 18 wt .-%, is a sufficient Austenite stability and thus a sufficient draw ratio secured.
  • the Mn content can be limited to a maximum of 20% by weight in order to ensure reliable production with simultaneously optimized service properties. This can be achieved, in particular, by limiting the Mn content to a maximum of 19.2% by weight, with Mn contents of at least 18.8% by weight being found to be particularly advantageous in view of the positive effects of this alloying element to have.
  • Silicon is present in the steel from which a flat steel product to be formed according to the invention in amounts of 0.2-0.5% by weight in order to increase the stacking fault energy and to obtain stable austenite even after forming in the structure of the flat steel product. which contributes to a good maximum draw ratio of the flat steel product.
  • at least 0.2 wt .-% Si are required.
  • the Si content is more than 0.5% by weight, impurities may be generated in the structure, which would deteriorate the maximum draw ratio. To avoid this effect, the Si content can be reduced to max. 0.45 wt .-% be limited.
  • Aluminum is present in the steel from which a flat steel product according to the invention may consist in amounts of 1.1-1.35% by weight, with contents of at most 1.3% by weight being found to be particularly expedient in practice to have.
  • the effect of aluminum also consists in the stabilization of the austenite in the structure of the steel before and during the forming.
  • Al serves as a hydrogen sink to tilt of the steel to reduce hydrogen-induced retarded cracking. If the Al contents are too low, these effects will not be achieved.
  • thermoforming ie when the maximum drawing ratio ⁇ is utilized, the risk of delayed crack formation due to the addition of hydrogen is highest.
  • the upper limit of the Al content is limited to 1.35% by weight, in particular 1.3% by weight, in order to enable reliable steel production.
  • Chromium is present in the steel of a flat steel product according to the invention to be deformed in amounts of 1.4-2.4% by weight in order to stabilize the austenite in the structure of the steel at room temperature. This effect is achieved at levels of at least 1.4% by weight, in particular at least 1.5% by weight.
  • the Cr content of the steel is limited to at most 2.4% by weight, whereby negative effects of the desired presence of Cr in view of the austenite stabilization can be avoided particularly reliably in that the Cr content is limited to at most 1.7% by weight.
  • Titanium and niobium may be present in the steel from which the flat steel products to be formed in accordance with the present invention may be present in amounts of up to 0.05% by weight. Titanium and niobium contribute to the grain refinement through nitride, carbide and carbonitride formation, which contributes to the increase in strength. A niobium content above 0.05 wt .-% shows no further advantages in terms of increase in strength. For cost reasons, the niobium content is limited to 0.05 wt .-%. Titanium content above 0.05 wt .-% lead to coarse titanium carbides, which adversely affects the elongation at break, which is why the titanium content is limited to 0.05 wt .-%. The positive influence of Ti on the strength of the steel can be used in particular when the Ti content is at least 0.018 wt .-%, resulting here optimal effects with limited to 0.022 wt .-% Ti content.
  • vanadium in the steel from which the flat steel products to be formed according to the invention can be present in amounts of up to 0.15% by weight. After hot rolling on the cooling section and also in an annealing treatment, vanadium forms the finest carbides, which have a strong strength-increasing effect, without significantly reducing the elongation of the steel, since they have a grain-refining effect. The yield strength also increases sharply with these carbides, which is particularly useful for suspension applications.
  • Particularly suitable for the production of flat steel products, which are to be formed in the hot rolled state according to the invention are steels in which the V content is limited to 0.05 wt .-%.
  • V contents of .alpha 0.05 - 0.15 wt .-% proved to be advantageous.
  • the positive influence of the presence of V has a particular effect when the V content of the steel is at least 0.11% by weight.
  • An optimum ratio of alloying costs to the effect is obtained when the V content is limited to at most 0.13 wt .-%.
  • nitrogen leads to a reduction of the free V content and to the formation of aluminum nitrides.
  • Aluminum nitrides influence the material so that the material tends to brittle fracture behavior and the maximum achievable maximum draw ratio ß is reduced.
  • the N content of the steel is limited to at most 0.03 wt%, especially at most 0.015 wt%.
  • boron causes an increase in ductility at elevated temperatures of e.g. 800 - 1100 ° C, as given during hot rolling. This reduces the risk of edge cracking in the hot strip.
  • boron has a fine grain, which contributes to the increase in strength.
  • the steel provided according to the invention should contain at least 0.001 wt.% B. At levels greater than 0.005% by weight, on the other hand, no increase in the positive effect of B can be detected.
  • P, S and other elements are attributed according to the invention for a steel sheet according to the invention to be deformed steel the inevitable impurities inevitably enter the steel in the course of steel production or due to the selected Starting material (scrap) inevitably remain in it.
  • Phosphorus has an unfavorable effect on the weldability of a flat steel product to be processed according to the invention.
  • phosphorus promotes the formation of unwanted segregations in molten steel, which can lead to material inaccuracies.
  • the P content should therefore be as low as possible, in any case not exceed 0.03 wt .-%.
  • Sulfur also has a negative effect on the performance characteristics of the flat steel product. Its maximum content is therefore limited to 0.005 wt .-%.
  • the contents of other unavoidable impurities, even those not explicitly mentioned here, should be as low as possible, at least below the content limit, from which they could be alloyed with respect to the steel composition considered here.
  • the content of Mo, As and Sn is advantageously in each case not more than 0.05% by weight, the Cu content is not more than 0.2% by weight and the Ni Content limited to at most 0.7 wt .-%.
  • the inventively provided as a material for the invention to be deformed steel flat products and composite in the above-described manner steel has a temperature-independent temperature TWIP effect at a deformation in the temperature range of 20 - 400 ° C, such that at least 95% of the degree of deformation is characterized by twin formation ,
  • TWIP effect at a deformation in the temperature range of 20 - 400 ° C, such that at least 95% of the degree of deformation is characterized by twin formation
  • no detectable TRIP effect occurs, ie there is no deformation-induced transformation of austenite into the martensite instead.
  • the steel achieves a yield strength R p0.2 of typically 370-600 MPa, a tensile strength Rm of typically 700-900 MPa and an elongation at break A5 of more than 50%.
  • the stacking fault energy is in accordance with the invention composite flat steel products in the typical for steels with TWIP properties range of 20 - 60 [mJ / m 2 ].
  • the flat steel products have a stable austenitic structure at room temperature.
  • the maximum draw ratio ⁇ of high-manganese steels composed as described above is at room temperature, i. at 15-35 ° C, typically 2.12, well below the minimum of 2.20 typically required for the maximum draw ratio ⁇ of steels suitable for deep drawing. Due to the inventively provided and provided in the forming tool heating of each to be deformed steel flat product, however, the steel reaches maximum drawing ratios ß, which are in the range of 2.24 - 2.28 and thus safely above the critical limit of 2.20.
  • rounds R cut out from the respective flat steel product are provided with initial diameters D o of 90, 100, 110 and 120 mm and a thickness of 2.0 mm.
  • the blanks R are prepared according to the different test temperatures with a lubricant system.
  • a lubricant system in the temperature range between room temperature and 150 ° C inclusive drawing film made of PVC in a thickness of 75 microns in combination with oil, applied on both sides of the sample used.
  • 150 ° C ie at the temperatures investigated 200 ° C, 250 ° C and 300 ° C, the PVC film is replaced by a 100 micron thick PTFE film in combination with vegetable oil.
  • the punch 1 is pressed into the respective blank R at a speed of 1 mm / s.
  • the holding force NK can be set with an accuracy of 1 kN in the range between 5 kN and 400 kN.
  • the forming tools are heated 1,2,3 in the hot drawing device to the respective forming temperature T u .
  • a temperature sensor on the hot drawing device enables the temperature measurement or control of the temperature of the hot drawing device.
  • the respectively prepared round blank sample is placed in the hot drawing device and centered.
  • the round blank sample has room temperature (20 ° C). Subsequently, the hold-down is lowered to the rim edge.
  • thermocouple can be clamped between the respective round blank sample R and the die 3.
  • the blank R Due to the contact with the hold-down 2 and the die 3, the blank R is heated to the respective forming temperature T u .
  • the control of the machine and recording of the measured values is computer-aided by means of a suitable Software.
  • the test parameters pulling force, hold-down force, punch travel and test time are recorded continuously.
  • a further typical steel alloy for the production of flat steel products, which are shaped as hot strip in the manner according to the invention into components, is steel B, likewise indicated in Table 1, in which case the contents of P, S, N, Cu, which are inferior in alloying, to the impurities.
  • High-manganese steels of the type in question are usually melted in an electric steelworks since Here, the purity of the materials supplied is highest and ladle furnaces for secondary metallurgy are needed.
  • the melt produced in the electric arc furnace is distributed after tapping off and slagging in order to allow the high manganese content to be added to ladle furnaces, which have a sensible way of having a refining device.
  • a degassing device is provided in the ladle furnaces to adjust the required carbon and sulfur content.
  • the melt is cast in single or multi-strand continuous casting to slabs.
  • the melt is passed through a continuous casting mold.
  • Of the cast strands are divided by cutting slabs with the desired length of use.
  • hot wide strip slabs can also be used. These are also produced by continuous casting, as described above, and then longitudinally divided centrally or preferably off-center by flame cutting. By off-center flame cutting, the cut of the core segregation can be avoided. Subsequently, the fuel rods resulting from the flame cutting must be removed by means of grinding. If there is severe cracking on the burning surface, the burned surfaces can also be ground.
  • block molds can also be used.
  • the cast blocks can now be blocked by pre-blocking on a block-slab road to a rectangular and usable on the hot strip mill slab.
  • the respective slabs made of the respective high-manganese steel are placed in a lifting beam or other heating furnace for 2-5 hours and heated to a temperature of 1200-1300 ° C, the typical target heating temperature being 1280 ° C.
  • the slabs are descaled and fed into a hot rolling mill equipped with typically seven hot rolling stands.
  • the hot rolling then takes place in a temperature range of 1150 ° C to 850 ° C and provides hot strip with a thickness of 1.5 - 16 mm.
  • the width of the resulting hot strip is typically 300-690 mm in practice.
  • the emerging from the hot rolling mill hot strip is cooled on a cooling section by means of water jets to temperatures of 350 ° C to 650 ° C in order to prevent the formation of coarser precipitates and to conserve the grain sizes set by rolling.
  • the hot-rolled strip is wound into coils.
  • These coils are now placed in a shower storage to control scale buildup and to prevent waste growth.
  • cool the coils within max. 2 days at ambient temperature.
  • the coils can also Cool the air without a shower to show a slower cooling. As a result, the formation of internal stresses, which could occur in too fast cooling, can be avoided.
  • the coils can be transferred to a Salzklarebeize before reaching room temperature, but at the latest at this time in order to remove the remaining on the belt surface residual scale.
  • the pickling bath temperature is set at 50 to 89 ° C. The use of inhibitors is possible to control pickling.
  • a cold-rolled strip may be produced from the thus-obtained hot-rolled strip in one or more cold-rolling steps in a conventional manner, the strip obtained being subjected to annealing after cold-rolling or between the individual cold-rolling steps to reduce solidification during cold-rolling and to secure the deep-drawing suitability ,
  • Table 2 lists the results and conditions of tests performed on samples 1-10 consisting of melt A. Accordingly, samples 1 and 2 are not according to the invention because the minimum value of 2.20 required according to the invention for the maximum draw ratio ⁇ has not been reached. Although sample 10 has a very good maximum draw ratio ⁇ . However, there were problems in carrying out the experiment here because the vegetable oil used as the drawing oil already decomposed at the forming temperature selected there.
  • Fig. 1 illustrated diagram has been created, in which for the steel A, the maximum draw ratio ß is plotted on the forming temperature Tu.
  • Table 1 stolen C Si Mn P S al Cr Cu V N Ni Ti A 0,417 0.38 18.8 0,029 0.001 1.3 2.4 0.16 0.12 0.0077 0.68 0.02 B 0.40 0.35 18.9 0,022 0,002 1.29 2.37 0.05 0.01 0,008 0.08 0,012 Sample No. stolen forming temperature Achieved maximum pulling ratio ⁇ drawing depth Clamping force hold time dwell drawing oil According to the invention?

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
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  • Mechanical Engineering (AREA)
  • Crystallography & Structural Chemistry (AREA)
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  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)
EP16188522.3A 2015-09-17 2016-09-13 Procede destine a la fabrication d'un composant en acier haute resistance Withdrawn EP3144077A1 (fr)

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DE102015115726.8A DE102015115726B4 (de) 2015-09-17 2015-09-17 Verfahren zum Herstellen eines Bauteils aus einem Stahlflachprodukt

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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR3096908A1 (fr) * 2019-06-07 2020-12-11 Safran Aircraft Engines Procédé de realisation d’une pièce renforcée mecaniquement

Citations (6)

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Publication number Priority date Publication date Assignee Title
FR2829775A1 (fr) * 2001-09-20 2003-03-21 Usinor Procede de fabrication de tubes roules et soudes comportant une etape finale d'etirage ou d'hydroformage et tube soude ainsi obtenu
DE102004061284A1 (de) 2003-12-23 2005-07-28 Salzgitter Flachstahl Gmbh Verfahren zum Erzeugen von Warmbändern aus Leichtbaustahl
DE102008020757A1 (de) 2007-04-30 2008-11-06 Volkswagen Ag Verfahren zur Umformung von Blechwerkstücken aus Eisen-Mangan-Stahl
DE102007060612A1 (de) * 2007-12-13 2009-06-18 Schondelmaier Gmbh Presswerk Verfahren zum Umformen von Stahl
EP2641991A1 (fr) * 2010-11-18 2013-09-25 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) Plaque d'acier à haute résistance avec une excellente aptitude au formage, procédé de formage à chaud, et pièce automobile formée à chaud
DE102011121679B4 (de) 2011-12-13 2014-01-02 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung von Bauteilen aus Leichtbaustahl

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2829775A1 (fr) * 2001-09-20 2003-03-21 Usinor Procede de fabrication de tubes roules et soudes comportant une etape finale d'etirage ou d'hydroformage et tube soude ainsi obtenu
DE102004061284A1 (de) 2003-12-23 2005-07-28 Salzgitter Flachstahl Gmbh Verfahren zum Erzeugen von Warmbändern aus Leichtbaustahl
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