EP1407056B1 - Procede de production d'une piece moulee realisee en matiere gamma-ti-al intermetallique - Google Patents

Procede de production d'une piece moulee realisee en matiere gamma-ti-al intermetallique Download PDF

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Publication number
EP1407056B1
EP1407056B1 EP02759850A EP02759850A EP1407056B1 EP 1407056 B1 EP1407056 B1 EP 1407056B1 EP 02759850 A EP02759850 A EP 02759850A EP 02759850 A EP02759850 A EP 02759850A EP 1407056 B1 EP1407056 B1 EP 1407056B1
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EP
European Patent Office
Prior art keywords
preparing
accordance
atom
moulded part
alloy
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Expired - Lifetime
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EP02759850A
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German (de)
English (en)
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EP1407056A2 (fr
Inventor
Andreas Dr. Hoffmann
Heinrich Dr. Kestler
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Plansee SE
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Plansee SE
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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C14/00—Alloys based on titanium
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
    • C22F1/18—High-melting or refractory metals or alloys based thereon
    • C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12014—All metal or with adjacent metals having metal particles
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12736—Al-base component
    • Y10T428/12743—Next to refractory [Group IVB, VB, or VIB] metal-base component
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12806—Refractory [Group IVB, VB, or VIB] metal-base component

Definitions

  • the invention relates to a method for producing a molded part from an intermetallic ⁇ -TiAl Material ( ⁇ -titanium aluminide) with 41-49 atom% Al.
  • ⁇ -TiAl materials are often referred to as "near- ⁇ -titanium aluminides".
  • the metal structure consists mainly of TiAl phase ( ⁇ -phase) with a small proportion of Ti 3 Al ( ⁇ 2 -phase).
  • ⁇ -phase TiAl phase
  • Ti 3 Al ⁇ 2 -phase
  • individual groups of advantageous alloying elements in ⁇ -TiAl alloys can be generally as follows (in atom%): Ti-Al 45-48 - (Cr, Mn, V) 0-3 - (Nb, Ta, Mo, W) 0-5 - (Si, B) 0-1 .
  • Niobium, tungsten, molybdenum and, to a lesser extent, tantalum improve oxidation resistance, while chromium, manganese and vanadium have a ductile effect.
  • intermetallic ⁇ -TiAl materials are of interest for a variety of applications. These include, for example, turbine components, as well as engine or transmission components of automobiles.
  • the prerequisite for large-scale application of ⁇ -TiAl is the availability of a technically reliable forming method that enables the cost-effective production of molded parts with requirements-oriented properties.
  • No. 5,429,796 describes a cast molding made of a titanium aluminide material consisting of 44-52 atom% aluminum, 0.05-8 atom% of one or more elements of the group chromium, carbon, gallium, molybdenum, manganese, niobium , Nickel, silicon, tantalum, vanadium and tungsten and at least 0.5% by volume of a boride phase having a yield strength of 55 ksi and an ultimate elongation of at least 0.5%.
  • Powder metallurgically produced moldings are much finer-grained than after Casting manufactured.
  • powder metallurgically produced material has filled with gas pores on - usually in the spraying Powder production used inert gas argon.
  • the pores have an effect disadvantageous both on the creep behavior, as well as on the Fatigue behavior.
  • ⁇ -TiAl casting molds In the case of ⁇ -TiAl casting molds, a satisfactory grain refinement can be achieved by means of specially developed forming processes, such as extrusion, forging, rolling and combinations of these processes.
  • ⁇ -TiAl alloys are therefore usually made of VAR (Vacuurn-Arc-Remelting) starting material, which is converted by forming and annealing in a feinkömigen state, the actual shaping following the hot working by means of complex mechanical, predominantly machining processing takes place.
  • VAR Vauurn-Arc-Remelting
  • the processing of an alloy in the solidus-liquidus phase state is a semi-solid process.
  • a semi-solid process typically, in a semi-solid process, partially liquid masses are processed in a thixotropic state.
  • Thixotropy is the property of a material to behave highly viscous in the absence of external forces, but under the action of shear forces to assume a viscosity several orders of magnitude lower. Thixotropic behavior is limited to certain alloy compositions and those temperature ranges where both solid and liquid phase portions are present in the alloy.
  • a semi-solid phase is sought, in which regular, that is as globular as possible grains in the solid phase portion, which are uniformly surrounded by melt.
  • the shaping of an alloy by means of a semi-solid process as such is known.
  • molten alloys are slowly cooled to a temperature in the solidus-liquidus two-phase region using one of the known stirring techniques, such as MHD (Magneto-Hydrodynamic Stirring) or mechanical stirring. Stirring destroys dendrites leaving the melt. Thixotropic properties are imparted to the material and the formation of globular primary crystals in the solid phase is promoted.
  • MHD Magnetic-Hydrodynamic Stirring
  • Stirring destroys dendrites leaving the melt.
  • Thixotropic properties are imparted to the material and the formation of globular primary crystals in the solid phase is promoted.
  • This method is described in US Pat. No. 5,358,687 for intermetallic materials, mention being made, inter alia, of TiAl, but in contrast to the present invention, there is no mention of further shaping involving mechanical hot forming steps.
  • the achievable grain size was> 50 microns.
  • this technique, applied to ⁇ -TiAl does not allow for economical production. With TiAl the mechanical stir
  • ⁇ -TiAl alloys formed into semifinished products in a first hot forming process section exhibit thixotropic behavior after being heated to a temperature in the solidus-liquidus phase region for the further shaping processing.
  • the alloy formed as a flowable suspension which could be used to form complex designed components.
  • This impressions must be made slowly and free of flow turbulence in the material, so that the material propagates free of pores and voids in the mold.
  • a mechanical, machining could be omitted or greatly reduced, so that in addition to excellent microstructural and mechanical properties of the moldings according to the invention also high efficiency was given in their production.
  • the advantage according to the invention lies in the substantially finer-grained microstructure and the high degree of freedom from pores.
  • the particle size distribution was determined by means of the linear section method and the d 95 value.
  • the d 95 grain size gives a significantly higher numerical value than is the case with the indication in the form of the mean grain size.
  • the d 95 value is the more meaningful value especially for structures with a high particle size distribution range.
  • the achievable d 95 grain sizes are values of ⁇ 100 ⁇ m to ⁇ 300 ⁇ m. Such, for comparison purposes manufactured by investment casting and not further treated by hot forming moldings show an at least a factor of 5 coarse-grained structure than inventively produced moldings.
  • alloys are used with a niobium content between 1.5 and 12 atom%. These alloys show a finer grain size by a factor of 7 up to a factor of 16 than in conventional precision casting. The best results were achieved with ⁇ -TiAl alloys with a niobium content of 5 to 10 atom%. An additional refining effect was achieved by the alloying elements carbon and boron in amounts of up to 0.4 atom% each.
  • thixoforging and thixocross extrusion molding each of which is a well-known and well-proven technique, have been proven.
  • Thixoschmieden the partially liquid bolt is inserted into an open tool, or die tool. The shaping takes place by a subsequent tool movement, for example in a forging press.
  • the Thixoquerf beaupressen represents a modification of Thixogie calls. The pushed by a punch bolt is deflected on its way from the casting chamber to the mold or the forming tool by an angle of 90 °.
  • the production of the primary casting of an alloy of the composition titanium - 46.5 at% Al - 2 at% Cr - 1.5 at% Nb - 0.5 at% Ta - 0.1 at% Boron was achieved by vacuum arc melting (VAR) , To achieve satisfactory homogeneity, the ingot was remelted twice. The ingot diameter was 210 mm, the ingot length 420 mm. The ingot was extruded in the known state according to previously known process conditions, wherein the degree of deformation was 83%. A 110 mm length of stud was then heated to a solidus-liquidus phase temperature range of the 1460-1470 ° C alloy and, in this state, pressed in a servo-hydraulic press into a closed die cast molybdenum alloy die.
  • VAR vacuum arc melting
  • the molded part thus produced a cylindrical member having an average diameter of 40 mm, a length of 100 mm, a laterally mounted flange and a recess of dimensions 35 mm x 35 mm x 35 mm in the cylindrical part was examined metallographically.
  • the grain size d 95 was 120 ⁇ m.
  • the relative density was determined by buoyancy method and was 99.98%.
  • the grain size d 95 of the twice remelted investment casting was 1400 microns.
  • an ingot of the alloy composition titanium-45 atom% Al-5 atom% Nb-0.2 atom% C-0.2 atom% boron was produced by vacuum arc melting (VAR) and remelted twice.
  • the ingot diameter was 210 mm, the ingot length 420 mm.
  • the ingot was extruded in the known state by conventional methods, wherein the degree of deformation was 83%.
  • a 110 mm length of stud was heated to a temperature of 1460-1480 ° C, the alloy was thus brought into the solidus-liquidus phase region and, in this state, pressed in a servo-hydraulic press into a closed die-casting mold made of a molybdenum alloy.
  • the molded part thus produced a cylindrical member having an average diameter of 40 mm, a length of 100 mm, a laterally mounted flange and a recess of 35 mm ⁇ 35 mm ⁇ 35 mm in the cylindrical portion was examined metallographically.
  • the grain size d 95 was 75 microns.
  • the relative density was 99.99%.
  • the grain size d 95 of the initially produced investment casting had been 1200 ⁇ m.
  • a primary casting blank of the alloy titanium-46.5 at% Al-2 at% Cr-0.5 at% Ta-0.1 at% boron was produced by vacuum arc melting (VAR) and remelted twice.
  • the ingot diameter was 170 mm, the ingot length 420 mm.
  • the ingot was extruded in the known state, wherein the degree of deformation was 83%.
  • a 110 mm length of stud was heated to a temperature of 1440-1470 ° C and pressed in a servo-hydraulic press into a closed die casting tool made of a molybdenum alloy.
  • the molded part thus produced a cylindrical member having an average diameter of 40 mm, a length of 100 mm, a laterally mounted flange and a recess of 35 mm ⁇ 35 mm ⁇ 35 mm in the cylindrical portion was examined metallographically.
  • the grain size d 95 was 220 microns.
  • the relative density was 99.99%.
  • the grain size d 95 of the precision casting had been 1500 ⁇ m.
  • a primary cast ingot of the alloy titanium -46.5 at.% Al-10 at.% Nb was fabricated and remelted twice in accordance with the process steps of Example 1 by vacuum arc melting (VAR).
  • the ingot diameter was 170 mm, the ingot length 420 mm.
  • the ingot was extruded in the known state, wherein the degree of deformation was 83%.
  • a 110 mm length of stud was heated to a temperature of 1440-1470 ° C and pressed in a servo-hydraulic press into a closed die casting tool made of a molybdenum alloy.
  • the molded part thus produced a cylindrical member having an average diameter of 40 mm, a length of 100 mm, a laterally mounted flange and a recess of 35 mm ⁇ 35 mm ⁇ 35 mm in the cylindrical portion was examined metallographically.
  • the grain size d 95 was 90 microns.
  • the relative density was 99.98%.
  • the grain size d 95 of the precision casting had been 1300 ⁇ m.
  • the primary cast ingot of the alloy titanium - 46.5 at.% Al - 10 at.% Nb was manufactured in accordance with Example 1 by means of vacuum arc melting (VAR) and remelted twice.
  • the ingot diameter was 170 mm, the ingot length 420 mm.
  • the ingot was extruded in the known state, wherein the degree of deformation was 72%.
  • a 110 mm length of stud was heated to a temperature of 1440-1470 ° C and pressed in a servo-hydraulic press into a closed die casting tool made of a molybdenum alloy.
  • the molded part thus produced a cylindrical member having an average diameter of 40 mm, a length of 100 mm, a laterally mounted flange and a recess of 35 mm ⁇ 35 mm ⁇ 35 mm in the cylindrical portion was examined metallographically.
  • the grain size d 95 was 170 ⁇ m.
  • the relative density was 99.98%.
  • the grain size d 95 of the precision casting had been 1300 ⁇ m.
  • the invention is not limited to the aforementioned embodiments.
  • Preferred application areas for molded parts according to the invention are the Automotive industry, e.g. Transmission and engine parts, but also parts for stationary Gas turbines and aerospace, e.g. Turbine components.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Forging (AREA)
  • Powder Metallurgy (AREA)
  • Extrusion Of Metal (AREA)

Claims (15)

  1. Procédé de fabrication d'un corps façonné en alliage intermétallique y Ti Al à teneur atomique de 41 à 49 % en Al, à granulométrie d95 < 300 µm et à volume de pores < 0,2% en volume, qui contient au moins les étapes de procédé consistant à :
    fabriquer un demi-produit en incorporant un traitement de déformation à chaud dont le degré de déformation est > 65%
    déformer le demi-produit à l'état de phase solidus-liquidus de l'alliage dans un outil de formage en appliquant au moins temporairement des forces de déformation mécaniques.
  2. Procédé de fabrication d'un corps façonné selon la revendication 1, caractérisé en ce que l'alliage se trouve à l'état thixotrope lors de la déformation.
  3. Procédé de fabrication d'un corps façonné selon la revendication 1 ou 2, caractérisé en ce que le composant solide de l'alliage dans l'état de phase solidus-liquidus présente une structure globulaire lors de la déformation.
  4. Procédé de fabrication d'un corps façonné selon l'une quelconque des revendications précédentes, caractérisé en ce que la déformation du demi-produit par thixo-forgeage s'effectue dans une matrice d'estampage.
  5. Procédé de fabrication d'un corps façonné selon l'une quelconque des revendications 1 à 3, caractérisé en ce que la déformation s'effectue en coquille par thixo-fluage du demi-produit.
  6. Procédé de fabrication d'un corps façonné selon l'une quelconque des revendications précédentes, caractérisé en ce que la fabrication du demi-produit s'effectue en intégrant un traitement par extrusion.
  7. Procédé de fabrication d'un corps façonné selon l'une quelconque des revendications précédentes, caractérisé en ce que la granulométrie de ce corps d95 < 200 µm.
  8. Procédé de fabrication d'un corps façonné selon l'une quelconque des revendications précédentes, caractérisé en ce que la granulométrie de ce corps d95 < 150 µm.
  9. Procédé de fabrication d'un corps façonné selon l'une quelconque des revendications précédentes, caractérisé en ce que l'alliage contient une teneur atomique de 43 à 47% d'aluminium et une teneur atomique de 1,5 à 12% de niobium.
  10. Procédé de fabrication d'un corps façonné selon la revendication 9, caractérisé en ce que la teneur atomique en niobium est de 5 à 10%.
  11. Procédé de fabrication d'un corps façonné selon la revendication 9 ou 10, caractérisé en ce que l'alliage contient en outre les teneurs atomiques suivantes: bore 0,05 à 0,5%; carbone 0 à 0,5%; chrome 0 à 3%; Ta 0 à 2%.
  12. Procédé de fabrication d'un corps façonné selon la revendication 11, caractérisé en ce que la teneur atomique en carbone est de 0,1 à 0,4% et la teneur atomique en bore de 0,1 à 0,4%.
  13. Procédé de fabrication d'un corps façonné selon l'une quelconque des revendications 1 à 7, caractérisé en ce que le traitement de déformation à chaud atteint un degré de déformation > 80%.
  14. Procédé de fabrication d'un corps façonné selon l'une quelconque des revendications précédentes, à utiliser pour des composants de moteurs et de boítes de vitesse d'automobiles.
  15. Procédé de fabrication d'un corps façonné selon l'une quelconque des revendications précédentes à utiliser pour des composants dans des turbines à gaz stationnaires et non stationnaires.
EP02759850A 2001-07-19 2002-07-12 Procede de production d'une piece moulee realisee en matiere gamma-ti-al intermetallique Expired - Lifetime EP1407056B1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
AT02759850T ATE305526T1 (de) 2001-07-19 2002-07-12 Verahren zur herstellung eines formteiles aus einem intermetallischen gamma-ti-al-werkstoff

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
AT0057301U AT5199U1 (de) 2001-07-19 2001-07-19 Formteil aus einem intermetallischen gamma-ti-al-werkstoff
AT5732001 2001-07-19
PCT/AT2002/000205 WO2003008655A2 (fr) 2001-07-19 2002-07-12 Piece moulee realisee en matiere gamma-ti-al intermetallique

Publications (2)

Publication Number Publication Date
EP1407056A2 EP1407056A2 (fr) 2004-04-14
EP1407056B1 true EP1407056B1 (fr) 2005-09-28

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EP02759850A Expired - Lifetime EP1407056B1 (fr) 2001-07-19 2002-07-12 Procede de production d'une piece moulee realisee en matiere gamma-ti-al intermetallique

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Country Link
US (1) US6805759B2 (fr)
EP (1) EP1407056B1 (fr)
AT (1) AT5199U1 (fr)
DE (1) DE50204409D1 (fr)
WO (1) WO2003008655A2 (fr)

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DE102004056582B4 (de) * 2004-11-23 2008-06-26 Gkss-Forschungszentrum Geesthacht Gmbh Legierung auf der Basis von Titanaluminiden
DE102005022506B4 (de) * 2005-05-11 2007-04-12 Universität Stuttgart Verfahren zum Schmieden eines Bauteils aus einer Titanlegierung
FR2913898B1 (fr) * 2007-03-23 2009-05-08 Alcan Rhenalu Sa Element structural en alliage d'aluminium incluant un capteur optique.
TW200900541A (en) * 2007-06-29 2009-01-01 Jun-Yen Uan Method for making lithium-aluminum compound with high lithium content
AT509768B1 (de) * 2010-05-12 2012-04-15 Boehler Schmiedetechnik Gmbh & Co Kg Verfahren zur herstellung eines bauteiles und bauteile aus einer titan-aluminium-basislegierung
US9061351B2 (en) * 2011-11-10 2015-06-23 GM Global Technology Operations LLC Multicomponent titanium aluminide article and method of making
US9992917B2 (en) 2014-03-10 2018-06-05 Vulcan GMS 3-D printing method for producing tungsten-based shielding parts
FR3019561B1 (fr) * 2014-04-08 2017-12-08 Snecma Traitement thermique d'un alliage a base d'aluminure de titane
CN108034857A (zh) * 2017-11-23 2018-05-15 中国航发北京航空材料研究院 一种防钛火阻燃涂层及其制备方法
CN108559872B (zh) * 2018-06-05 2020-06-30 中国航发北京航空材料研究院 一种TiAl合金及其制备方法
JP7233659B2 (ja) * 2019-03-18 2023-03-07 株式会社Ihi 熱間鍛造用のチタンアルミナイド合金材及びチタンアルミナイド合金材の鍛造方法並びに鍛造体
CN110643877A (zh) * 2019-09-09 2020-01-03 中国航发北京航空材料研究院 一种含W、Mn、Si、B、C及稀土元素的TiAl金属间化合物
CN116607048A (zh) * 2022-02-09 2023-08-18 中国科学院金属研究所 一种用于精密铸造的γ-TiAl合金及其制备方法

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Publication number Publication date
EP1407056A2 (fr) 2004-04-14
US6805759B2 (en) 2004-10-19
DE50204409D1 (de) 2006-02-09
WO2003008655A3 (fr) 2003-10-30
AT5199U1 (de) 2002-04-25
US20040094242A1 (en) 2004-05-20
WO2003008655A2 (fr) 2003-01-30

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