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EP0554808A1 - Procédé de fabrication des pièces métalliques - Google Patents

Procédé de fabrication des pièces métalliques Download PDF

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Publication number
EP0554808A1
EP0554808A1 EP19930101454 EP93101454A EP0554808A1 EP 0554808 A1 EP0554808 A1 EP 0554808A1 EP 19930101454 EP19930101454 EP 19930101454 EP 93101454 A EP93101454 A EP 93101454A EP 0554808 A1 EP0554808 A1 EP 0554808A1
Authority
EP
European Patent Office
Prior art keywords
solidus
grain
grain refining
temperature
metal alloys
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.)
Granted
Application number
EP19930101454
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German (de)
English (en)
Other versions
EP0554808B1 (fr
Inventor
Gang Dr.-Ing. Wan
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Efu Gesellschaft fur Ur-/umformtechnik Mbh
Original Assignee
Efu Gesellschaft fur Ur-/umformtechnik Mbh
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
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Publication of EP0554808A1 publication Critical patent/EP0554808A1/fr
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Publication of EP0554808B1 publication Critical patent/EP0554808B1/fr
Anticipated expiration legal-status Critical
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Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D1/00—Treatment of fused masses in the ladle or the supply runners before casting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/12—Making non-ferrous alloys by processing in a semi-solid state, e.g. holding the alloy in the solid-liquid phase

Definitions

  • the invention relates to a process for the production of moldings from metal alloys, in which the metal alloys are brought into the molten state and cast into geometrically simple shapes by conventional casting processes and then by heating to a temperature between the solidus and the liquidus line from a solid - A liquid mixture of rounded, existing thixotropic slurries, homogeneously distributed in a melt matrix, is formed, which is fed to a molding system after a holding time.
  • the shaping in the semi-solid state is characterized as a method with energy saving potential.
  • a key advantage is the low casting temperature, which means that the rollers, molds etc. of subsequent molding systems are exposed to less thermal stress.
  • the material also solidifies much faster due to the proportionally lower heat of solidification and forms fewer voids, since the slurry is partially solidified and has a smaller volume jump during further solidification.
  • a thixotropic slip as a special raw material, which consists of a primary and a low-melting matrix phase.
  • this primary material is heated to a temperature between solidus and liquidus, hereinafter referred to as the processing temperature.
  • the matrix melts first, while the solid phase is dispersed in the form of rounded fine particles in the matrix.
  • This slip is then used for shaping afterwards System, hereinafter molding system, such as a die casting machine or a forging press, fed and brought into a final shape due to the thixotropic properties of the slip.
  • the primary material is referred to below as the rheo primary material.
  • the aim is to produce primary particles that are as fine and spherical as possible in the slip because the slip with fine particles not only has a high fluidity but also leads to a better surface quality.
  • the required fineness of the particles is mainly determined by the shaping process ⁇ component geometry and quality. There is no quantitative information about this. There are currently a number of processes that can be divided into three groups:
  • Group 1 procedures are characterized by forced convection during solidification. Mechanical or electromagnetic stirring breaks up the usually dendritically crystallizing primary phases in whole or in part into rounded solid particles which are in the melt. After it has solidified, a rheo pre-material is produced which is suitable for processing in the semi-solid state.
  • SIMA Strain Induced Melt Activated
  • the conventionally cast metal alloys are cold-formed, for example by stretching, rolling or upsetting.
  • the cold-formed primary material is transferred to the slip during the subsequent heating at a temperature between solidus and liquidus before further processing.
  • additional hot working is required before cold working, for example by extrusion.
  • the particle size that can be achieved is 30 ⁇ m, [EP 0090253].
  • Group 3 processes make use of a special heat treatment.
  • a conventionally cast alloy is heated to a temperature between solidus and liquidus, kept isothermal at the temperature for a few minutes to a few hours and then sent for further processing.
  • Achieving rounded solid particles for Al alloys takes several hours.
  • the particle size is between 100 and 400 ⁇ m.
  • Electromagnetic stirring for the production of the rheo pre-material has found industrial use, but the low energy efficiency can be regarded as a serious disadvantage. Part of the electromagnetic energy introduced is lost as electricity heat loss and leads to undesired heating. The power loss increases with increasing frequency, decreasing number of poles and decreasing mold conductivity. In addition, the structure is not homogeneous over the entire volume.
  • the edge layer is peeled off or a pre-chamber is installed in the press mold during molding [EP 0254437].
  • part of the primary material mainly from the core area, is pressed into the mold, while another part Part, mainly from the surface layer, remains in the antechamber and is later removed from the component. This reduces the use of the material.
  • the heat treatment process requires such long-term annealing at a temperature between solidus and liquidus that technical problems arise and the economics of the process are questioned. Above all, the strong oxidation of the slip during heating is very difficult or only with great technical effort, e.g. by heating in a vacuum chamber under vacuum or protective gas. In addition, the resulting structure is so coarse that it can have a negative effect both on the fluidity during further processing, in particular when filling the mold at thin-walled locations on the component, and on the mechanical properties.
  • the object of the present invention is to eliminate the disadvantages of the previous methods in a method of the type mentioned at the outset and to provide an economical method for producing rheovor material with a fine-grained and homogeneous structure on the basis of a sophisticated technology.
  • This object is achieved according to the invention in a process of the type mentioned at the outset by adding an increased amount of grain refining agent to the metal alloys in the molten state compared to the known grain refinement, this increased amount consisting of a strongly falling first known for the individual alloys and grain refining agents Branch and a second branch curve asymptotically against a final grain size curve of a graph in which the change in grain size in ⁇ m is plotted against the change in the addition of grain refining agent in percent is determined such that the addition of grain refining agent as a value the second branch of the curve is selected, that the metal alloys are then cooled to any temperature below the solidus line and are then heated to a holding temperature between the Solidus and Liquidus lines and are held for a holding time of less than 15 minutes.
  • the primary material formed with an increased amount of grain refining agents differs from the conventional rheo primary materials in that it shows a dendritic structure before further processing. Only when they are reheated to a temperature between the solidus and liquidus lines do the dendrites turn into isolated, rounded spherical particles. The time required to round off the particles is a few seconds to minutes, depending on the alloys and grain fineness.
  • the slip formed from the rheo preform according to the invention can then be fed directly to a shaping plant and brought into a final shape.
  • the process according to the invention can be carried out in such a way that the increased amount of grain refining agent lies in a range in which the grain refining effect ⁇ D2 / ⁇ C2 (change in the grain size / change in the addition quantity) is less than 1/20 of the amount of the mean slope ⁇ D1 / ⁇ C1 in the first Branch of the curve is.
  • the process according to the invention can be carried out in such a way that the increased amount of grain refining agent lies in a range in which the grain refining effect ⁇ D2 / ⁇ C2 (change in the grain size / change in the addition quantity) is less than 1/50 of the amount of the mean slope ⁇ D1 / ⁇ C1 in the first Branch of the curve is.
  • the process according to the invention can be carried out for the production of moldings from copper alloys in such a way that the elements which form a peritectic with aluminum are used alone or in combination as grain refining agents.
  • the process according to the invention can be carried out in such a way that Ti, B, Nb are used alone or in combination as grain refinement agents.
  • the inventive method can be carried out so that Ti is used together with C.
  • the process according to the invention can be carried out by using Zr alone or in combination with B as the grain refining agent.
  • the process according to the invention can be carried out in such a way that in the case of an aluminum alloy with 0 to 9% by weight of Si, 0 to 5% by weight of Cu, 0 to 5% by weight of Zn and 0 to 3% by weight of Mg as grain refiners Ti and B with a total proportion of 0.05 to 0.6% by weight can be used.
  • the process according to the invention can be carried out in such a way that an aluminum alloy AlSi7Mg is melted and degassed and that a Ti content of ⁇ 0.25% is set in the melt, the aluminum alloy is reheated and held for 5 minutes between the solidus and the liquidus line.
  • the process according to the invention can be carried out in such a way that an aluminum wrought alloy AlMg1SiCu is melted and degassed and that a Ti content of ⁇ 0.025% is set in the melt, the aluminum alloy is reheated and held between solidus and liquidus line for 5 minutes.
  • the process according to the invention can be carried out such that Zr and / or B and P as deoxidizing agents as grain refining agents be used.
  • the process according to the invention can be carried out by additionally adding Mg for desulfurization.
  • the process according to the invention can be carried out in such a way that in the case of a copper alloy with 0 to 30% by weight of Zn and 0 to 20% by weight of Sn as grain refining agent Zr and / or B with a total proportion of 0.05 to 1.0% by weight and P can be used.
  • the process according to the invention can be carried out in such a way that a copper alloy CuSn12 is melted and deoxidized, then adjusted to a Zr content of ⁇ 0.05% and then kept at a temperature between the Liqidus and Solidus lines for one minute.
  • the process according to the invention can be carried out in such a way that the temperature of the alloy is kept isothermally between the solidus and liquidus lines.
  • the method according to the invention can be carried out in such a way that the temperature of the alloy is stepped between the solidus and liquidus lines.
  • the process according to the invention can be carried out in such a way that the metal alloys provided with grain refining agent in the molten state are cast in precisely metered amounts in a metal mold cooled by a cooling medium in a quantity required for the shaping.
  • the method according to the invention can be carried out in such a way that the metal alloys between the solidus and liquidus lines are heated to a temperature above the holding temperature, the total duration within the solidus-liquidus range being 1 to 15 minutes.
  • the selection of the quantity of grain refining agent that is decisive for the method according to the invention uses a diagram known for the respective alloy and the associated grain refining agent, as is typically shown in FIG. 2.
  • the grain is refined in the area of the steeply falling branch of the curve in this diagram.
  • increasing the amount of the grain refining agent has a great effect on reducing the grain size.
  • the curve has a second branch, which approaches an end value of the grain size asymptotically.
  • leads the increase in The addition of the grain refining agent does not result in a noticeable reduction in the grain size.
  • the amounts of grain refining agent used according to the invention lie in the region of this second branch of the curve.
  • the cast cylinders were then heated in an induction system to a temperature of about 578 ° C. and held at this temperature for different lengths of time and then quenched. During the holding it was observed that at a Ti content below 0.18% the melt emerged from the cylinder and collected on the cylinder bottom. The cylinder was difficult to pierce with a 10 mm diameter graphite rod. Cracks were also found. In contrast, no melt escaped above 0.19% Ti and the cylinder is easily pierced with the graphite rod.
  • Figure 3b shows the structure with a Ti content of 0.01% after a holding time of 14 minutes.
  • Figure 3d shows the structure with a Ti content of 0.19% and a holding time of 10 minutes.
  • Isolated fine but not rounded primary particles were found between 0.19 and 0.25% Ti, the form factor decreasing with increasing Ti content. Isolated rounded primary particles were obtained within a holding time of 5 minutes above 0.25% Ti (Fig. 3f). The structure was homogeneous over the entire volume. The mean diameter of the rounded particles was 110 ⁇ m after 5 minutes of isothermal annealing. Extending the hold time resulted in an increase in the mean diameter and a decrease in the shape factor of the rounded particles. Refining with Sr only affected the eutectic and not the formation of the primary phase.
  • Figure 4 shows the structure according to this example, with 0.26% in Figure 4a, 0.34% in Figure 4b and 0.50% in Figure 4c.
  • the average diameter of the rounded particles was 95 ⁇ m.
  • Figure 5 shows the structure according to this example, whereby images arranged next to each other show the structure with the same Ti content, but on the left before reheating and on the right after reheating.
  • the Ti content was 0.01% according to Figures 5a and 5b, 0.15% according to Figures 5c and 5d and 0.36% according to Figures 5e and 5f.
  • the samples were quenched at 572 ° C.
  • the average diameter of the rounded particles was 100 ⁇ m.
  • Example 2 An aluminum wrought alloy AlZn6Mg2Cu with 6% Zn, 2% Mg and 1% Cu was melted as in Example 1 and grain-refined both in an oven and in a trough by the addition of pre-alloy wire made of AlTi5B.
  • the melt was cast in a vertical continuous caster into strands with a diameter of 100 mm.
  • the strands were then separated into cylinders with a length of 100 mm, which were reheated in an induction system as in Examples 1 and 2. With a holding time of 5 minutes, a minimum content of approx. 0.06% Ti was determined in order to achieve the desired structure.
  • Adjacent images show the structure with the same Ti content, left before reheating and right after reheating.
  • the Ti content was 0.04% according to Fig. 6a, b and 0.09% according to Fig. 6c, d.
  • Reheating was carried out at 610 ° C for 5 minutes. An average diameter of the rounded particles of 50 ⁇ m was achieved.
  • Example 4 The process according to Example 4 was carried out using an aluminum wrought alloy AlMg1SiCu with 0.6-1.2% Mg, 0.7-1.5% Si, 5.0% Cu, 0.4-1.0% Mn and 0.3 - 0.5% Fe carried out. A result similar to Example 4 was achieved. With a given holding time of 5 minutes, a minimum content of 0.025% Ti was determined to achieve the desired structure.
  • the average diameter of the rounded particles was approx. 70 ⁇ m after reheating.
  • a copper alloy CuSn12 was melted in a conventional manner at 1020 ° C. and deoxidized with CuP7 master alloy. The amount added was 1 to 2 kg / t based on the amount of melt.
  • the structure after casting with different Zr content was predominantly dendritic, as shown in Fig. 7a, c, e.
  • the cast cylinders were then heated in an induction system to a temperature of approximately 900 ° C., kept at that temperature isothermally and quenched at different times. Due to the rapid formation of a thick oxide layer during reheating a short stopping time was necessary in the atmosphere. During the heating it was observed that the Zr content below 0.03%, the melt emerged from the cylinder and collected on the cylinder bottom. The cylinder could not be pierced with a 10 mm diameter graphite rod without forming cracks. In contrast, no melt emerged above 0.04% Zr and the cylinder could be pierced with the graphite rod.
  • the primary phase with a Zr content below 0.04% consisted mainly of long dendrites.
  • Isolated rounded primary particles were obtained within a holding time of 1 minute above 0.05% Zr, as shown in Figure 7f.
  • the structure was homogeneous over the entire volume.
  • the minimum content was 0.05% Zr with a holding time of 1 minute.
  • the average diameter of the rounded particles was 70 ⁇ m.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacture And Refinement Of Metals (AREA)
  • Manufacture Of Metal Powder And Suspensions Thereof (AREA)
  • Forging (AREA)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)
EP93101454A 1992-01-30 1993-01-29 Procédé de fabrication des pièces métalliques Expired - Lifetime EP0554808B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE4202562 1992-01-30
DE4202562 1992-01-30

Publications (2)

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EP0554808A1 true EP0554808A1 (fr) 1993-08-11
EP0554808B1 EP0554808B1 (fr) 1997-05-02

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AT (1) ATE152378T1 (fr)
DE (1) DE59306300D1 (fr)

Cited By (17)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE19518127A1 (de) * 1994-05-17 1995-11-23 Honda Motor Co Ltd Legierungsmaterial zum Thixo-Gießen, Verfahren zum Zubereiten semi-geschmolzenen Legierungsmaterials zum Thixo-Gießen und Thixo-Gießverfahren
EP0692328A1 (fr) * 1994-06-14 1996-01-17 Salzburger Aluminium Aktiengesellschaft Procédé pour la fabrication de pièces moulées, en alliage d'aluminium
EP0701002A1 (fr) * 1994-09-09 1996-03-13 Ube Industries, Ltd. Procédé de fabrication d'alliages d'aluminium ou de magnésium à l'état semi-solide
WO1996038593A1 (fr) * 1995-05-31 1996-12-05 Reynolds Wheels S.P.A. Traitement d'alliages d'aluminium pour obtenir un etat semi-solide
EP0822994A1 (fr) * 1995-04-14 1998-02-11 Northwest Aluminum Company Transformation thermique et formation a l'etat semi-solide d'alliages d'aluminium
US5911843A (en) * 1995-04-14 1999-06-15 Northwest Aluminum Company Casting, thermal transforming and semi-solid forming aluminum alloys
US5968292A (en) * 1995-04-14 1999-10-19 Northwest Aluminum Casting thermal transforming and semi-solid forming aluminum alloys
WO2001009401A1 (fr) * 1999-07-28 2001-02-08 Sm Schweizerische Munitionsunternehmung Ag Procede de production d'une matiere premiere constituee d'un alliage metallique
US6200396B1 (en) * 1999-01-21 2001-03-13 Aluminium Pechinay Hypereutectic aluminium-silicon alloy product for semi-solid forming
WO2003064075A1 (fr) * 2002-01-31 2003-08-07 Tht Presses Inc. Procede de moulage semi-solide
WO2004061140A1 (fr) * 2003-01-03 2004-07-22 Singapore Institute Of Manufacturing Technology Traitement de metaux semi-solides transformables et recyclables
US6813547B2 (en) 2002-05-16 2004-11-02 Alcatel Method of providing protection against the effects of solar originating protons, so as to make it possible for a star sensor to be reconfigured, and an attitude control system implementing the method
WO2004099455A2 (fr) * 2003-05-01 2004-11-18 Spx Corporation Procede de moulage a l'etat semi-solide d'alliages d'aluminium au moyen d'un raffineur de grains
US6901991B2 (en) 2002-01-31 2005-06-07 Tht Presses Inc. Semi-solid molding apparatus and method
EP1628793A2 (fr) * 2003-05-01 2006-03-01 SPX Corporation Moulage a l'etat semi-solide d'alliages d'aluminium hypo-eutectiques
DE102005022506A1 (de) * 2005-05-11 2006-11-16 Universität Stuttgart Verfahren zum Schmieden eines Bauteils aus einer Titanlegierung
US7299854B2 (en) 2002-01-31 2007-11-27 T.H.T. Presses, Inc. Semi-solid molding method

Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0090253A2 (fr) * 1982-03-30 1983-10-05 Alumax Inc. Composition métallique à grains fins
GB2156855A (en) * 1984-04-06 1985-10-16 Nat Res Dev Alloying process

Patent Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0090253A2 (fr) * 1982-03-30 1983-10-05 Alumax Inc. Composition métallique à grains fins
GB2156855A (en) * 1984-04-06 1985-10-16 Nat Res Dev Alloying process

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
PATENT ABSTRACTS OF JAPAN vol. 2, no. 34 (C-005)8. März 1978 & JP-A-52 131 911 ( MITSUBISHI CHEM IND LTD ) 5. November 1977 *
PATENT ABSTRACTS OF JAPAN vol. 6, no. 127 (C-113)13. Juli 1982 & JP-A-57 054 235 ( MITSUBISHI KEIKINZOKU KOGYO KK ) 31. März 1982 *

Cited By (28)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5849115A (en) * 1994-05-17 1998-12-15 Honda Giken Kogyo Kabushiki Kaisha Alloy material for thixocasting, process for preparing semi-molten alloy material for thixocasting and thixocasting process
DE19518127A1 (de) * 1994-05-17 1995-11-23 Honda Motor Co Ltd Legierungsmaterial zum Thixo-Gießen, Verfahren zum Zubereiten semi-geschmolzenen Legierungsmaterials zum Thixo-Gießen und Thixo-Gießverfahren
DE19518127C2 (de) * 1994-05-17 1999-12-02 Honda Motor Co Ltd Verfahren zur Herstellung eines semi-geschmolzenen Legierungsmaterials zum Thixo-Gießen
EP0692328A1 (fr) * 1994-06-14 1996-01-17 Salzburger Aluminium Aktiengesellschaft Procédé pour la fabrication de pièces moulées, en alliage d'aluminium
EP0701002A1 (fr) * 1994-09-09 1996-03-13 Ube Industries, Ltd. Procédé de fabrication d'alliages d'aluminium ou de magnésium à l'état semi-solide
US5701942A (en) * 1994-09-09 1997-12-30 Ube Industries, Ltd. Semi-solid metal processing method and a process for casting alloy billets suitable for that processing method
US5911843A (en) * 1995-04-14 1999-06-15 Northwest Aluminum Company Casting, thermal transforming and semi-solid forming aluminum alloys
US5846350A (en) * 1995-04-14 1998-12-08 Northwest Aluminum Company Casting thermal transforming and semi-solid forming aluminum alloys
EP0822994A4 (fr) * 1995-04-14 1998-12-23 Northwest Aluminum Co Transformation thermique et formation a l'etat semi-solide d'alliages d'aluminium
US5968292A (en) * 1995-04-14 1999-10-19 Northwest Aluminum Casting thermal transforming and semi-solid forming aluminum alloys
EP0822994A1 (fr) * 1995-04-14 1998-02-11 Northwest Aluminum Company Transformation thermique et formation a l'etat semi-solide d'alliages d'aluminium
WO1996038593A1 (fr) * 1995-05-31 1996-12-05 Reynolds Wheels S.P.A. Traitement d'alliages d'aluminium pour obtenir un etat semi-solide
US6200396B1 (en) * 1999-01-21 2001-03-13 Aluminium Pechinay Hypereutectic aluminium-silicon alloy product for semi-solid forming
US6547896B2 (en) 1999-07-28 2003-04-15 Ruag Munition Process for the production of a material made of a metal alloy
WO2001009401A1 (fr) * 1999-07-28 2001-02-08 Sm Schweizerische Munitionsunternehmung Ag Procede de production d'une matiere premiere constituee d'un alliage metallique
US6901991B2 (en) 2002-01-31 2005-06-07 Tht Presses Inc. Semi-solid molding apparatus and method
WO2003064075A1 (fr) * 2002-01-31 2003-08-07 Tht Presses Inc. Procede de moulage semi-solide
US6808004B2 (en) 2002-01-31 2004-10-26 Tht Presses Inc. Semi-solid molding method
US7299854B2 (en) 2002-01-31 2007-11-27 T.H.T. Presses, Inc. Semi-solid molding method
US6813547B2 (en) 2002-05-16 2004-11-02 Alcatel Method of providing protection against the effects of solar originating protons, so as to make it possible for a star sensor to be reconfigured, and an attitude control system implementing the method
WO2004061140A1 (fr) * 2003-01-03 2004-07-22 Singapore Institute Of Manufacturing Technology Traitement de metaux semi-solides transformables et recyclables
WO2004099455A3 (fr) * 2003-05-01 2004-12-16 Spx Corp Procede de moulage a l'etat semi-solide d'alliages d'aluminium au moyen d'un raffineur de grains
EP1628793A2 (fr) * 2003-05-01 2006-03-01 SPX Corporation Moulage a l'etat semi-solide d'alliages d'aluminium hypo-eutectiques
US7025113B2 (en) 2003-05-01 2006-04-11 Spx Corporation Semi-solid casting process of aluminum alloys with a grain refiner
EP1628793A4 (fr) * 2003-05-01 2006-11-22 Spx Corp Moulage a l'etat semi-solide d'alliages d'aluminium hypo-eutectiques
WO2004099455A2 (fr) * 2003-05-01 2004-11-18 Spx Corporation Procede de moulage a l'etat semi-solide d'alliages d'aluminium au moyen d'un raffineur de grains
DE102005022506A1 (de) * 2005-05-11 2006-11-16 Universität Stuttgart Verfahren zum Schmieden eines Bauteils aus einer Titanlegierung
DE102005022506B4 (de) * 2005-05-11 2007-04-12 Universität Stuttgart Verfahren zum Schmieden eines Bauteils aus einer Titanlegierung

Also Published As

Publication number Publication date
EP0554808B1 (fr) 1997-05-02
DE59306300D1 (de) 1997-06-05
ATE152378T1 (de) 1997-05-15

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