EP0733716B1 - Intermetallische Gusslegierung auf Basis von Titan-Aluminid - Google Patents

Intermetallische Gusslegierung auf Basis von Titan-Aluminid Download PDF

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Publication number
EP0733716B1
EP0733716B1 EP96400598A EP96400598A EP0733716B1 EP 0733716 B1 EP0733716 B1 EP 0733716B1 EP 96400598 A EP96400598 A EP 96400598A EP 96400598 A EP96400598 A EP 96400598A EP 0733716 B1 EP0733716 B1 EP 0733716B1
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EP
European Patent Office
Prior art keywords
alloy
atoms
alloy according
phase
alloys
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EP96400598A
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English (en)
French (fr)
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EP0733716A1 (de
Inventor
Shigehisa Naka
Marc Thomas
Agnès Bachelier-Locq
Tasadduq Khan
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Office National dEtudes et de Recherches Aerospatiales ONERA
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Office National dEtudes et de Recherches Aerospatiales ONERA
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    • 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

Definitions

  • the invention relates to an intermetallic alloy based on of titanium aluminide for the production of foundry.
  • the transformation by foundry of intermetallic alloys derivatives of titanium aluminide ⁇ (TiAl) is considered with interest in the production of parts for turbomachinery aeronautics.
  • the foundry is indeed generally less more expensive than other shaping methods.
  • it has the advantage of preserving in principle the resistance hot mechanical of the castings because the size of the metallurgical grains obtained is relatively large.
  • the inventors Undertook a study on the influence of various refractory additions on the flowability. They analyzed many alloys based on TiAl in which 2 to 10% of the atoms were constituted by one or more of the addition elements Nb, Ta, Cr, Mo, W, Fe and Re, and in particular examined their microstructures both in the raw state of casting and after treatments thermal. They thus concluded that the solidification process is an important parameter for the quality of the foundry parts.
  • the different alloys examined can indeed be classified in two categories, for which are initially formed during solidification a phase of hexagonal crystal structure ⁇ and a phase of centered cubic structure ⁇ respectively.
  • the columnar character is on the other hand less pronounced, although the axis ⁇ 100> of the ⁇ phase remains the preferred direction of crystal growth during solidification.
  • the crystals of the ⁇ phase called initial grains, transform into crystals of the ⁇ phase. This transformation, which occurs according to the so-called Burgers orientation relationship (110) ⁇ // (0001) ⁇ and ⁇ 1 1 1> ⁇ // ⁇ 11 2 0> ⁇ , theoretically leads to the formation of twelve ⁇ variants.
  • the ⁇ phase precipitates in lamellar form in each variant ⁇ .
  • the resulting microstructure is characterized by the presence of numerous colonies (theoretically up to twelve orientation variants) inside each initial ⁇ grain. Each of these colonies is made up of numerous ⁇ platelets (or slats), these platelets (or slats) being sometimes delimited by residual ⁇ -phase borders. Each plate (or slat) finally has the lamellar structure ⁇ + ⁇ 2 .
  • Such a transformation sequence results in a minimization of the difficulties encountered in the alloys solidifying in ⁇ with the reduction in the frequency of the solidification defects and a less pronounced texture.
  • Solidification in ⁇ phase can be obtained for binary alloys sufficiently rich in Ti, as for example in the case of the composition Ti 60 Al 40 , whose Ti / Al atomic ratio of 1.5 is very far from that of the composition equiatomic Ti 50 Al 50 equal to 1.
  • alloys as rich in titanium are significantly heavier and less resistant to oxidation than the equiatomic alloy.
  • after preparation they have a two-phase structure ⁇ + ⁇ 2 in which the volume fraction of the slightly deformable ⁇ 2 phase is excessively large, which makes them extremely fragile.
  • the two-phase alloy of the composition T1 52 Al 48 with an atomic ratio equal to 1.08 which has optimal ductility thanks to a volume fraction of the phase ⁇ 2 of the order of 10%, cannot solidify only at ⁇ .
  • the invention relates in particular to an alloy of the kind defined in the introduction, and provides that its composition in atoms is included in the field defined below: Ti 48.5 to 52.5% Al 45.5 to 48.5% Re 0.5 to 2.5% W 0 to 2.0% Re + W 2.0 to 2.5% Nb 0 to 3.5% Re + W + Nb 2.0 to 5.5% Yes 0 to 1.0%
  • tungsten as an element promoting solidification in ⁇ , rather than rhenium alone, presents a economic interest due to the high cost of rhenium.
  • niobium provides good resistance to oxidation, as well as a good level of heat resistance.
  • silicon aims to obtain a beneficial effect on mechanical properties of use such as creep.
  • the invention also relates to a foundry piece made of an alloy as defined above, comprising the juxtaposition of a multiplicity of colonies within each initial ⁇ grain, colonies themselves comprising the juxtaposition of a multiplicity platelets each formed by an alternating stack of lamellas of crystallographic structure ⁇ and layers of crystallographic structure ⁇ 2 .
  • the platelets of the same colony are oriented according to one of the 12 ⁇ variants defined by the Burgers relationship from said ⁇ grain, the platelets of two neighboring colonies being oriented according to different variants.
  • Figures 1 and 2 show schematically two successive stages of the solidification of an intermetallic alloy based on aluminide titanium.
  • Figure 3 is a sectional view of an alloy according to that of figure 2.
  • FIGS 4 and 5 illustrate the structure of an alloy according to the invention.
  • FIG. 1 shows by way of example a cylindrical sample 1 of an alloy in the process of cooling in which columnar grains 2 of crystallographic structure ⁇ are formed. These grains are elongated in the crystallographic direction c, which coincides with the direction of the temperature gradient indicated by the arrow F, that is to say the radial direction of the cylinder 1.
  • FIG. 2 shows, on a larger scale, these same columnar grains 2 further cooled. Each of them contains lamellas 3 of crystallographic structure ⁇ oriented perpendicular to the longitudinal direction of the grain, separated from each other by layers 4 of crystallographic structure ⁇ 2 .
  • FIG. 3 highlights the structure of such an alloy of the "first generation”.
  • FIG. 5 is a section of the same alloy showing, on the one hand, the orientation of the plates 7 in each colony 6 and, on the other hand, the alternating stack of lamellae of crystallographic structure ⁇ and layers of structure crystallographic ⁇ 2 .
  • the alloys according to the invention can be produced and used used in the same way as intermetallic alloys based on known titanium aluminide, so that it is not no need to provide specific information for this respect.
  • the alloy of formula (1) above and the aforementioned alloy of formula Ti 48 Al 48 Cr 2 Nb 2 underwent the same heat treatments, four hours at 1250 ° C., then four hours at 900 ° C. After these treatments, the two alloys exhibited comparable tensile properties at 25 ° C., respectively 484 and 459 MPa for the elastic limit, 1.4% and 0.9% for the elastic elongation or ductility. On the other hand, a deformation of 0.5% in creep at 800 ° C. under 180 MPa was obtained in 145 hours for the alloy according to the invention against 5 hours for the known alloy. For the latter alloy, the resistance to hot creep could be improved by eliminating the aforementioned heat treatments, but this would result in a collapse of the ductility at room temperature due to the poor flowability associated with solidification in the ⁇ phase.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacture And Refinement Of Metals (AREA)
  • Continuous Casting (AREA)
  • Powder Metallurgy (AREA)
  • Turbine Rotor Nozzle Sealing (AREA)

Claims (8)

  1. Intermetallische Legierung auf Basis von Titan-Aluminid zur Herstellung von Gußteilen, deren Atomzusammensetzung auf 100% die folaende ist: Ti 48,5 bis 52,5% Al 45,5 bis 48,5% Re 0,5 bis 2,5% W 0 bis 2,0% Re + W 2,0 bis 2,5% Nb 0 bis 3,5% Re + W + Nb 2,0 bis 5,5% Si 0 bis 1,0%.
  2. Legierung nach Anspruch 1, dadurch gekennzeichnet, daß sie ungefähr 2 Atom-% Re + W enthält.
  3. Legierung nach Anspruch 2, dadurch gekennzeichnet, daß sie 1 bis 2 Atom-% Re enthält.
  4. Legierung nach einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, daß sie ungefähr 3 Atom-% Nb enthält.
  5. Legierung nach einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, daß sie 0,2 bis 0,8 Atom-% Si enthält.
  6. Legierung nach dem einem oder dem anderen der vorhergehenden Ansprüche, dadurch gekennzeichnet, daß ihre Atomzusammensetzung unter den folgenden gewählt ist: Ti50,6Al46,6Re2Si0,8 Ti52Al46Re1W1 Ti51,8Al46Re1W1Si0,2 Ti49Al46Nb3Re1W1 Ti48,8Al46Nb3Re1W1Si0,2.
  7. Legierung nach einem der vorhergehenden Ansprüche, dadurch gekennzeichnet, daß sie geeignet ist, bei ihrer Erstarrung eine Phase kubisch zentrierter Struktur β zu bilden.
  8. Gußteil, hergestellt aus einer Legierung nach Anspruch 7, umfassend die Nebeneinanderstellung einer Mehrzahl von Kolonien (6) im Inneren jedes anfänglichen β-Kornes, Kolonien, die selbst die Nebeneinanderstellung einer Mehrzahl von Plättchen (7) umfassen, deren jedes durch eine abwechselnde Aufschichtung von Lamellen der kristallographischen Struktur γ und von Schichten der kristallographischen Struktur α2 gebildet ist, wobei die Plättchen derselben Kolonie entsprechend einer der 12 Varianten α, definiert durch die Burgers-Relation ausgehend von dem genannten Korn β, orientiert sind und die Plättchen zweier benachbarter Kolonien entsprechend verschiedenen Varianten orientiert sind.
EP96400598A 1995-03-24 1996-03-21 Intermetallische Gusslegierung auf Basis von Titan-Aluminid Expired - Lifetime EP0733716B1 (de)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
FR9503511A FR2732038B1 (fr) 1995-03-24 1995-03-24 Alliage intermetallique a base d'aluminiure de titane pour la fonderie
FR9503511 1995-03-24
US08/622,668 US5846345A (en) 1995-03-24 1996-03-26 Intermetallic alloy based on titanium aluminide for casting

Publications (2)

Publication Number Publication Date
EP0733716A1 EP0733716A1 (de) 1996-09-25
EP0733716B1 true EP0733716B1 (de) 1999-10-20

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Country Status (5)

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US (1) US5846345A (de)
EP (1) EP0733716B1 (de)
JP (1) JP3913285B2 (de)
CA (1) CA2172476C (de)
FR (1) FR2732038B1 (de)

Families Citing this family (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE19710592A1 (de) * 1997-03-14 1998-09-17 Forschungszentrum Juelich Gmbh Oxidationsbeständige, TiAl-haltige Legierungen
BRPI0613493A2 (pt) * 2005-06-28 2011-01-11 Zbx Corp membrana matriz e dispositivo analìtico
FR3006696B1 (fr) 2013-06-11 2015-06-26 Centre Nat Rech Scient Procede de fabrication d'une piece en alliage en titane-aluminium
KR101614124B1 (ko) * 2014-11-24 2016-04-21 한국기계연구원 타이타늄-알루미늄계 합금
CN115466867B (zh) * 2022-09-14 2023-05-05 西北工业大学 一种能够改善其均匀变形能力的TiAl合金及其制备方法
CN115627386B (zh) * 2022-11-07 2023-10-24 西北工业大学 一种适用于轧制变形的TiAlRe合金及其轧制方法

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4783329A (en) * 1985-12-11 1988-11-08 Allied-Signal Inc. Hydriding solid solution alloys having a body centered cubic structure stabilized by quenching near euctectoid compositions
JP2569710B2 (ja) * 1988-04-04 1997-01-08 三菱マテリアル株式会社 常温靱性を有するＴｉ−Ａ▲ｌ▼系金属間化合物型鋳造合金
US4879092A (en) * 1988-06-03 1989-11-07 General Electric Company Titanium aluminum alloys modified by chromium and niobium and method of preparation
US5041262A (en) * 1989-10-06 1991-08-20 General Electric Company Method of modifying multicomponent titanium alloys and alloy produced
DE4304481A1 (de) * 1993-02-15 1994-08-18 Abb Research Ltd Hochtemperaturlegierung auf der Basis von legiertem gamma-Titanaluminid und Verwendung dieser Legierung

Also Published As

Publication number Publication date
CA2172476C (en) 2007-03-06
FR2732038A1 (fr) 1996-09-27
US5846345A (en) 1998-12-08
FR2732038B1 (fr) 1997-06-06
EP0733716A1 (de) 1996-09-25
JP3913285B2 (ja) 2007-05-09
JPH08269595A (ja) 1996-10-15
CA2172476A1 (en) 1996-09-25

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