EP4353855A1 - Tial-legierung, tial-legierungspulver, tial-legierungsbauteil und verfahren zu dessen herstellung - Google Patents

Tial-legierung, tial-legierungspulver, tial-legierungsbauteil und verfahren zu dessen herstellung Download PDF

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Publication number
EP4353855A1
EP4353855A1 EP22820205.7A EP22820205A EP4353855A1 EP 4353855 A1 EP4353855 A1 EP 4353855A1 EP 22820205 A EP22820205 A EP 22820205A EP 4353855 A1 EP4353855 A1 EP 4353855A1
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Prior art keywords
tial alloy
solidification
point
less
content
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English (en)
French (fr)
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Yutaro Ota
Yuto Miyazawa
Keiji Kubushiro
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IHI Corp
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IHI Corp
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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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/004—Filling molds with powder
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/12—Both compacting and sintering
    • B22F3/14—Both compacting and sintering simultaneously
    • B22F3/15—Hot isostatic pressing
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2301/00—Metallic composition of the powder or its coating
    • B22F2301/20—Refractory metals
    • B22F2301/205—Titanium, zirconium or hafnium
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their steps
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy

Definitions

  • the present disclosure relates to a TiAl alloy, TiAl alloy powder, a TiAl alloy component and a production method of the same.
  • TiAl (titanium aluminide) alloys are alloys formed of intermetallic compounds of Ti and Al. As the TiAl alloys show excellent heat resistance and have lighter in weight and greater in specific strength than Ni alloys, these alloys are applied to aeroplane engine components such as turbine vanes or blades. TiAl alloys including Cr and Nb are applied to these TiAl alloys (see the PTL 1).
  • PTL 1 Japanese Patent Application Laid-open No. 2013-209750
  • An object of the present disclosure is thus to provide a TiAl alloy, TiAl alloy powder, a TiAl alloy component and a production method of the same, which enables improvement of the mechanical strength and the ductility with balance.
  • a TiAl alloy related to the present disclosure consists of: 47 at% or more and 50 at% or less of Al; 1 at% or more and 2 at% or less of Nb; 2 at% or more and 5 at% or less of Zr; 0.05 at% or more and 0.3 at% or less of B; and the balance being Ti and inevitable impurities.
  • a content of Al may be 47 at% or more and 49 at% or less.
  • a content of Nb may be 1 at%
  • a content of Al may be 47 at% or more and 48 at% or less
  • a content of Zr may be 2 at% or more and 4 at% or less.
  • a content of Nb may be 1 at%
  • a content of Al may be 47 at% or more and 48 at% or less
  • a content of Zr may be 2 at% or more and 3 at% or less.
  • a content of Nb may be 2 at%
  • a content of Al may be 47 at% or more and 49 at% or less
  • a content of Zr may be 2 at% or more and 3 at% or less.
  • a content of Nb may be 2 at%
  • a content of Al may be 47 at% or more and 48 at% or less
  • a content of Zr may be 2 at% or more and 4 at% or less.
  • a content of Al may be 47 at% or more and 48 at% or less, and a content of Zr may be 2 at% or more and 4 at% or less.
  • a content of Al may be 47 at% or more and 48 at% or less, and a content of Zr may be 2 at% or more and 3 at% or less.
  • a room temperature ultimate tensile strength is 600 MPa or more, and a room temperature tensile fracture strain is 1.2 % or more.
  • a TiAl alloy powder related to the present disclosure is formed of the TiAl alloy as described above.
  • a TiAl alloy component related to the present disclosure is formed of the TiAl alloy as described above.
  • a production method of a TiAl alloy component related to the present disclosure is provided with: a sealing step of filling a metal sheath with a TiAl alloy powder formed of the TiAl alloy as described above; and a hot isostatic pressure step of treating the TiAl alloy powder sealed in the metal sheath with a hot isostatic pressure treatment under 1200 degrees C or higher and 1300 degrees C or lower and 150 MPa.
  • the aforementioned constitution enables improvement of the mechanical strength and the ductility of TiAl alloys with balance.
  • TiAl (titanium aluminide) alloys related to the present embodiments is constituted of 47 at% or more and 50 at% or less of Al (aluminum), 1 at% or more and 2 at% or less of Nb (niobium), 2 at% or more and 5 at% or less of Zr (zirconium), 0.05 at% or more and 0.3 at% or less of B (boron), and the balance being Ti (titanium) and inevitable impurities.
  • Reasons for limiting the composition ranges of respective alloy components constituting the TiAl alloy will be described next.
  • Al has a function to improve mechanical strength and ductility such as room temperature ductility.
  • the content percentage of Al is 47 at% or more and 50 at% or less. In a case where the content percentage of Al is less than 47 at%, specific strength decreases because the content percentages of Ti or such that are larger in density becomes greater. In a case where the content percentage of Al is larger than 50 at%, ductility decreases.
  • the content percentage of Al may be set to be 47 at% or more and 49 at% or less. This leads to improvement of mechanical strength and ductility of TiAl alloys.
  • Nb (niobium) has a function to improve oxidation resistance and mechanical strength.
  • the content percentage of Nb is 1 at% or more and 2 at% or less. In a case where the content percentage of Nb is less than 1 at%, there may be potential for reduction of oxidation resistance and high-temperature strength. In a case where the content percentage of Nb is more than 2 at%, specific strength is reduced as the density of Nb is larger than the densities of Al and Ti.
  • Zr zirconium has a function to improve oxidation resistance and mechanical strength.
  • Zr is a chemical element that stabilizes a ⁇ phase and contributes to improvement of ductility such as room temperature ductility. Zr further reduces diffusion speed, thereby contributing to improvement of creep strength.
  • the content percentage of Zr is 2 at% or more and 5 at% or less. In a case where the content percentage of Zr is less than 2 at%, there may be potential for reduction of oxidation resistance, ductility such as room temperature ductility, and mechanical strength such as high-temperature strength. In a case where the content percentage of Zr is more than 5 at%, it can causes segregation. If the segregation of Zr occurs, it gives rise to reduction of mechanical strength or ductility.
  • B (boron) has a function to refine crystal grains so as to increase ductility such as room temperature ductility.
  • the content percentage of B is 0.05 at% or more and 0.3 at% or less.
  • the content percentage of B becomes less than 0.05 at%, the crystal grains becomes coarsened and thus it gives rise to reduction of ductility.
  • the content percentage of B becomes more than 0.3 at%, there may be potential for reduction of impact resistance properties.
  • B has a function to cause precipitation of borides in each crystal grain by heat treatment, thereby improving mechanical strength.
  • Fine borides with those of 0.1 micrometers in grain diameter are formed.
  • the fine borides are constituted of TiB, TiB 2 and such.
  • mechanical strength such as tensile strength, fatigue strength, creep strength or such can be improved.
  • the balance of the TiAl alloy is constituted of Ti and inevitable impurities.
  • the term "inevitable impurity” means an impurity that has possibility of being mixed in any substance although it is not intentionally added.
  • Cr chromium
  • V vanadium
  • reduction of mechanical strength and reduction of oxidation resistance can be suppressed.
  • Mo molecular weight
  • reduction of specific strength can be suppressed.
  • the form of solidification of the TiAl alloy relates to the content percentages of Al, Zr and Nb.
  • the form of solidification of the TiAl alloy changes among ⁇ solidification, ⁇ solidification, ⁇ solidification, and ⁇ solidification + ⁇ solidification.
  • the ⁇ solidification is a form of solidification in which a solidification process of the TiAl alloy passes through an ⁇ single phase region.
  • the ⁇ solidification is a form of solidification in which a solidification process of the TiAl alloy passes through a ⁇ single phase region.
  • the ⁇ solidification is a form of solidification in which a solidification process of the TiAl alloy passes through a ⁇ single phase region.
  • the ⁇ solidification + ⁇ solidification is a form of solidification in which a solidification process of the TiAl alloy passes through an ⁇ + ⁇ dual phase region.
  • anisotropy of the metallographic structure becomes stronger because coarse columnar crystal grains grow.
  • isotropy of the metallographic structure becomes stronger and anisotropy of the metallographic structure becomes weaker because isometric crystal grains grow.
  • the form of solidification of the TiAl alloy tends to be the ⁇ solidification.
  • the form of solidification of the TiAl alloy tends to be the ⁇ solidification + ⁇ solidification, the ⁇ solidification or the ⁇ solidification.
  • the form of solidification of the TiAl alloy tends to be the ⁇ solidification.
  • the form of solidification of the TiAl alloy tends to be the ⁇ solidification + ⁇ solidification, the ⁇ solidification or the ⁇ solidification.
  • the form of solidification of the TiAl alloy tends to be the ⁇ solidification + ⁇ solidification, the ⁇ solidification or the ⁇ solidification.
  • the form of solidification of the TiAl alloy tends to be the ⁇ solidification.
  • FIG. 1 is a drawing showing a relation between content percentages of Al and Zr when a content percentage of Nb is 1 at%.
  • the TiAl alloy may be constituted of a composition range of the content percentages of Al and Zr, which is enclosed by four points of an R1 point (Al: 47 at%, Zr: 2 at%), an R2 point (Al: 48 at%, Zr: 2 at%), an R3 point (Al: 48 at%, Zr: 4 at%), and an R4 point (Al: 47 at%, Zr: 5 at%) shown in FIG. 1 .
  • the TiAl alloy may contain Al and Zr of the composition range enclosed by the four points of the R1 point, the R2 point, the R3 point and the R4 point shown in FIG. 1 and the balance may be constituted of Ti and inevitable impurities.
  • the form of solidification can be only the ⁇ solidification or the ⁇ solidification + ⁇ solidification.
  • anisotropy of the metallographic structure is suppressed as compared with the case where the form of solidification is of only the ⁇ solidification.
  • the mechanical property or such of the TiAl alloy becomes more isotropic.
  • such a TiAl alloy may contain 1 at% of Nb, 0.05 at% or more and 0.3 at% or less of B, 47 at% or more and 48 at% or less of Al and 2 at% or more and 4 at% or less of Zr and the balance may be constituted of Ti and inevitable impurities.
  • FIG. 2 is a drawing showing a relation between content percentages of Al and Zr when a content percentage of Nb is 1 at%.
  • the TiAl alloy may be constituted of a composition range of the content percentages of Al and Zr, which is enclosed by four points of an S1 point (Al: 47 at%, Zr: 2 at%), an S2 point (Al: 48 at%, Zr: 2 at%), an S3 point (Al: 48 at%, Zr: 3 at%), and an S4 point (Al: 47 at%, Zr: 5 at%) shown in FIG. 2 .
  • the TiAl alloy may contain 1 at% of Nb, 0.05 at% or more and 0.3 at% or less of B, Al and Zr of the composition range enclosed by the four points of the S1 point, the S2 point, the S3 point and the S4 point shown in FIG. 2 and the balance may be constituted of Ti and inevitable impurities.
  • the form of solidification can be only the ⁇ solidification.
  • anisotropy of the metallographic structure is further suppressed.
  • the mechanical property or such of the TiAl alloy becomes further more isotropic.
  • such a TiAl alloy may contain 1 at% of Nb, 0.05 at% or more and 0.3 at% or less of B, 47 at% or more and 48 at% or less of Al and 2 at% or more and 3 at% or less of Zr and the balance may be constituted of Ti and inevitable impurities.
  • FIG. 3 is a drawing showing a relation between content percentages of Al and Zr when a content percentage of Nb is 2 at%.
  • the TiAl alloy may be constituted of a composition range of the content percentages of Al and Zr, which is enclosed by five points of a T1 point (Al: 47 at%, Zr: 2 at%), a T2 point (Al: 49 at%, Zr: 2 at%), a T3 point (Al: 49 at%, Zr: 3 at%), a T4 point (Al: 48 at%, Zr: 4 at%), and a T5 point (Al: 47 at%, Zr: 4 at%) shown in FIG. 3 .
  • the TiAl alloy may contain Al and Zr of the composition range enclosed by the five points of the T1 point, the T2 point, the T3 point, the T4 point, and the T5 point shown in FIG. 3 and the balance may be constituted of Ti and inevitable impurities.
  • the form of solidification can be only the ⁇ solidification or the ⁇ solidification + ⁇ solidification.
  • anisotropy of the metallographic structure is suppressed.
  • the mechanical property or such of the TiAl alloy becomes more isotropic.
  • such a TiAl alloy may contain 2 at% of Nb, 0.05 at% or more and 0.3 at% or less of B, 47 at% or more and 49 at% or less of Al and 2 at% or more and 3 at% or less of Zr and the balance may be constituted of Ti and inevitable impurities.
  • such a TiAl alloy may contain 2 at% of Nb, 0.05 at% or more and 0.3 at% or less of B, 47 at% or more and 48 at% or less of Al and 2 at% or more and 4 at% or less of Zr and the balance may be constituted of Ti and inevitable impurities.
  • FIG. 4 is a drawing showing a relation between content percentages of Al and Zr when a content percentage of Nb is 2 at%.
  • the TiAl alloy may be constituted of a composition range of the content percentages of Al and Zr, which is enclosed by four points of a W1 point (Al: 47 at%, Zr: 2 at%), a W2 point (Al: 49 at%, Zr: 2 at%), a W3 point (Al: 48 at%, Zr: 4 at%), and a W4 point (Al: 47 at%, Zr: 4 at%) shown in FIG. 4 .
  • the TiAl alloy may contain 2 at% of Nb, 0.05 at% or more and 0.3 at% or less of B, Al and Zr of the composition range enclosed by the four points of the W1 point, the W2 point, the W3 point and the W4 point shown in FIG. 4 and the balance may be constituted of Ti and inevitable impurities.
  • the form of solidification can be only the ⁇ solidification.
  • anisotropy of the metallographic structure is further suppressed.
  • the mechanical property or such of the TiAl alloy becomes further more isotropic.
  • such a TiAl alloy may contain 2 at% of Nb, 0.05 at% or more and 0.3 at% or less of B, 47 at% or more and 48 at% or less of Al and 2 at% or more and 4 at% or less of Zr and the balance may be constituted of Ti and inevitable impurities.
  • FIG. 5 is a drawing showing a relation between content percentages of Al and Zr when a content percentage of Nb is 1 at% or more and 2 at% or less.
  • the TiAl alloy may be constituted of a composition range of the content percentages of Al and Zr, which is enclosed by four points of an X1 point (Al: 47 at%, Zr: 2 at%), an X2 point (Al: 48 at%, Zr: 2 at%), an X3 point (Al: 48 at%, Zr: 4 at%), and an X4 point (Al: 47 at%, Zr: 4 at%) shown in FIG. 4 .
  • the TiAl alloy may contain2 at% of Nb, 0.05 at% or more and 0.3 at% or less of B, Al and Zr of the composition range enclosed by the four points of the X1 point, the X2 point, the X3 point and the X4 point shown in FIG. 5 and the balance may be constituted of Ti and inevitable impurities.
  • the composition range enclosed by the four points of the X1 point, the X2 point, the X3 point, and the X4 point shown in FIG. 5 shows a composition range in which the composition range enclosed by the four points of the R1 point, the R2 point, the R3 point and the R4 point shown in FIG. 1 overlaps with the composition range enclosed by the five points of the T1 point, the T2 point, the T3 point, the T4 point and the T5 point shown in FIG. 3 .
  • the form of solidification can be only the ⁇ solidification or the ⁇ solidification + ⁇ solidification.
  • such a TiAl alloy may contain 1 at% or more and 2 at% or less of Nb, 0.05 at% or more and 0.3 at% or less of B, 47 at% or more and 48 at% or less of Al and 2 at% or more and 4 at% or less of Zr and the balance may be constituted of Ti and inevitable impurities.
  • FIG. 6 is a drawing showing a relation between content percentages of Al and Zr when a content percentage of Nb is 1 at% or more and 2 at% or less.
  • the TiAl alloy may be constituted of a composition range of the content percentages of Al and Zr, which is enclosed by four points of a Y1 point (Al: 47 at%, Zr: 2 at%), a Y2 point (Al: 48 at%, Zr: 2 at%), a Y3 point (Al: 48 at%, Zr: 3 at%), and a Y4 point (Al: 47.5 at%, Zr: 4 at%) shown in FIG. 6 .
  • the TiAl alloy may contain 1 at% or more and 2 at% or less of Nb, 0.05 at% or more and 0.3 at% or less of B, and Al and Zr of the composition range enclosed by the five points of the Y1 point, the Y2 point, the Y3 point, the Y4 point and the Y5 point shown in FIG. 6 and the balance may be constituted of Ti and inevitable impurities.
  • the composition range enclosed by the five points of the Y1 point, the Y2 point, the Y3 point, the Y4 point and the Y5 point shown in FIG. 6 shows a composition range in which the composition range enclosed by the four points of the S1 point, the S2 point, the S3 point and the S4 point shown in FIG. 2 overlaps with the composition range enclosed by the four points of the W1 point, the W2 point, the W3 point and the W4 point shown in FIG. 4 .
  • the form of solidification can be only the ⁇ solidification. Thereby, as the ⁇ solidification is not contained in the form of solidification, anisotropy of the metallographic structure is further suppressed.
  • such a TiAl alloy may contain 1 at% or more and 2 at% or less of Nb, 0.05 at% or more and 0.3 at% or less of B, 47 at% or more and 48 at% or less of Al and 2 at% or more and 3 at% or less of Zr and the balance may be constituted of Ti and inevitable impurities.
  • the metallographic structure of the TiAl alloy will be described next.
  • the metallographic structure of the TiAl alloy is constituted of fine crystal grains with a grain diameter of 100 micrometers or less. Thereby ductility of the TiAl alloy is improved.
  • the metallographic structure of the TiAl alloy is constituted of lamellar grains and ⁇ grains and is free from segregation. Each lamella is formed in which ⁇ 2 phases formed of Ti 3 Al and ⁇ phases formed of TiAl are regularly arranged in a layered form.
  • the ⁇ grains are formed of TiAl.
  • the ⁇ grains are for example isometric ⁇ grains.
  • borides with a grain diameter of 0.1 micrometers or less are contained.
  • the borides are constituted of TiB, TiB 2 or such in an acicular shape or such.
  • the lamellar grains can improve the mechanical strength such as the tensile strength, the fatigue strength, the creep strength or such.
  • the ⁇ grains can improve the ductility and the high-temperature strength.
  • the borides with a grain diameter of 0.1 micrometers or less can improve the mechanical strength.
  • the metallographic structure of the TiAl alloy exhibits that the volume fraction of the ⁇ grains is 80 vol% or more given that the total volume fraction of the lamellar grains and the ⁇ grains is 100 vol%, and the remainder is preferably the lamellar grains.
  • the metallographic structure of the TiAl alloy is constituted mainly of the ⁇ grains, the mechanical strength and the ductility can be improved with balance.
  • the metallographic structure of the TiAl alloy is free from segregation of Zr, reduction of the mechanical strength and the ductility can be suppressed.
  • the mechanical properties of the TiAl alloy in accordance with the present disclosure will be next described.
  • the mechanical properties of the TiAl alloy at room temperature is, if tensile tests are carried out in conformity with JIS, ASTM or such, that a room temperature ultimate tensile strength can be 600 MPa or more, and a room temperature tensile fracture strain can be 1.2 % or more.
  • the mechanical strength and the ductility can be improved with balance.
  • FIG. 7 is a drawing showing a constitution of a TiAl alloy component 10 formed of a turbine blade.
  • the TiAl alloy as described above is superior in the mechanical strength such as the high temperature strength, it can improve heat resistance of the TiAl alloy component 10. Further, as the TiAl alloy as described above shows excellent ductility such as room temperature ductility, damage of the TiAl alloy component 10 would be suppressed even in a case when the TiAl alloy component 10 is under assembly or installation.
  • the TiAl alloy component is not limited to an aeroplane engine component but may be a supercharger component such as a turbine wheel for a supercharger or a vehicle component such as an engine valve for a vehicle.
  • the TiAl alloy component can be produced by melting and casting the TiAl alloy as described above.
  • the TiAl alloy component can be produced by melting the TiAl alloy as described above in a vacuum induction heater furnace or such and then casting the same.
  • any casting machine used for casting a general metal material can be used.
  • the TiAl alloy component may be powder molded by using the TiAl alloy powder formed of the TiAl alloy as described above as an ingredient powder and by means of a metal powder injection molding (MIM) method or a hot isostatic pressing (HIP) method.
  • the TiAl alloy powder is formed of the TiAl alloy as described above and may be produced through a sinter synthesis method, a mechanical alloying method, a plasma rotary electrode method, an atomizing method (water atomizing or gas atomizing) or such.
  • the TiAl alloy powder is preferably made as a rapid solidified powder. Because the rapid solidified powder is produced by rapidly solidifying alloy liquid droplets, segregation of Zr contained in the TiAl alloy can be further suppressed.
  • FIG. 8 is a flowchart showing a constitution of the production method of the TiAl alloy component.
  • the production method of the TiAl alloy component is provided with a sealing step (S10) and a hot isostatic pressing step (S12) .
  • the sealing step (S10) is a step for filling a metal sheath with the TiAl alloy powder formed of the TiAl alloy as described above and sealing it.
  • the TiAl alloy powder formed of the TiAl alloy is used.
  • a rapid solidified powder produced by gas atomizing or such is applied.
  • the TiAl alloy powder is filled and sealed in the metal sheath.
  • a titanium sheath formed of pure titanium is applied.
  • the thickness of the titanium sheath is preferably 1 mm for example.
  • the TiAl alloy powder filled in the metal sheath is subject to sealing by electron beam welding or such after vacuum evacuation.
  • the hot isostatic pressing step (S12) is a step for treating the TiAl alloy powder filled in the metal sheath with hot isostatic pressing at 1200 degrees C or higher and 1300 degrees C or lower and under a pressure of 150 MPa or higher.
  • the hot isostatic pressing treatment can be carried out at 1200 degrees or higher and 1300 degrees C or lower and under a pressure of 150 MPa or higher.
  • the pressure is preferably 150 MPa or higher and 200 MPa or lower for example.
  • Duration of time for keeping the heating temperature may be 3 hours or longer.
  • the duration of time for keeping the heating temperature is preferably 3 hours or longer and 5 hours or shorter for example.
  • furnace cooling down to 900 degrees C is carried out, and further rapid cooling below 900 degrees C is carried out.
  • a cooling rate faster than air cooling is used and the cooling is possibly performed by gas fan cooling or such.
  • the production method of the TiAl alloy component may include, after the hot isostatic pressing step (S12), a stress relieving step for relieving stress by holding the component at a temperature range from 800 degrees C or higher to 950 degrees C or lower, for 1 hour or more and 5 hours or less. As residual stress or such in the TiAl alloy component is thereby relieved, the ductility of the TiAl alloy component can be improved.
  • the hot isostatic pressing treatment and the stress relieving are preferably carried out in a vacuum atmosphere or an inert gas atmosphere such as argon gas for the purpose of oxidation prevention.
  • a HIP machine or such used for general hot isostatic pressing onto metal materials is applicable.
  • a general atmosphere furnace used for stress relief annealing on metal materials is applicable.
  • the TiAl alloy constituted as in the way described above contains 47 at% or more and 50 at% or less of Al, 1 at% or more and 2 at% or less of Nb, 2 at% or more and 5 at% or less of Zr and 0.05 at% or more and 0.3 at% or less of B, and the balance is constituted of Ti and inevitable impurities. Thereby the mechanical strength and the ductility of the TiAl alloy can be improved with balance.
  • TiAl alloys of examples 1 through 18 A form of solidification of the TiAl alloy was examined. TiAl alloys of examples 1 through 18 will be described. Each TiAl alloy of the examples 1 through 18 contains Al, Nb, Zr and B and the balance is constituted of Ti and inevitable impurities. Alloy compositions of the TiAl alloys are summarized in TABLE 1. TABLE.
  • the content percentage of Nb was set 1 at% and the content percentage of B was set 0.2 at%, and the content percentages of Al were varied from 47 at% to 50 at% and the content percentages of Zr were varied from 3 at% to 5 at%.
  • the content percentage of Nb was set 2 at% and the content percentage of B was set 0.2 at%, and the content percentages of Al were varied from 48 at% to 50 at% and the content percentages of Zr were varied from 2 at% to 4 at%.
  • FIG. 9 is photographs showing results of the metallographic observation on the TiAl alloys of the examples 1 through 9.
  • FIG. 10 is photographs showing results of the metallographic observation on the TiAl alloys of the examples 10 through 18.
  • the forms of solidification were only the ⁇ solidification.
  • the forms of solidification are only the ⁇ solidification.
  • the forms of solidification are only the ⁇ solidification.
  • the forms of solidification are only the ⁇ solidification.
  • the form of solidification is the ⁇ solidification + ⁇ solidification.
  • the forms of solidification are only the ⁇ solidification.
  • FIG. 11 is a graph showing forms of solidification of the TiAl alloys of the examples 1 through 9.
  • FIG. 12 is a graph showing forms of solidification of the TiAl alloys of the examples 10 through 18.
  • the Zr contents (at%) are put on the horizontal axes
  • the Al contents (at%) are put on the vertical axes
  • circles represent that the form of solidification is only the ⁇ solidification
  • triangles represents that the form of solidification is the ⁇ solidification + ⁇ solidification
  • squares represent that the form of solidification is only the ⁇ solidification.
  • the form of solidification became only the ⁇ solidification when the content percentage of Zr is 2 at%
  • the form of solidification became the ⁇ solidification + ⁇ solidification when the content percentage of Zr is 3 at%
  • the form of solidification became only the ⁇ solidification when the content percentage of Zr is 4 at%.
  • the form of solidification becomes either only the ⁇ solidification or the ⁇ solidification + ⁇ solidification in a case where the content percentage of Nb is 1 at% and the content percentages of Al and Zr are constituted of the composition range enclosed by the four points of the R1 point (Al: 47 at%, Zr: 2 at%), the R2 point (Al: 48 at%, Zr: 2 at%), the R3 point (Al: 48 at%, Zr: 4 at%) and the R4 point (Al: 47 at%, Zr: 5 at%) shown in FIG. 1 as described above.
  • the form of solidification becomes only the ⁇ solidification or the ⁇ solidification + ⁇ solidification.
  • the form of solidification becomes either only the ⁇ solidification or the ⁇ solidification + ⁇ solidification in a case where the content percentage of Nb is 2 at% and the content percentages of Al and Zr are constituted of the composition range enclosed by the five points of the T1 point (Al: 47 at%, Zr: 2 at%), the T2 point (Al: 49 at%, Zr: 2 at%), the T3 point (Al: 49 at%, Zr: 3 at%), the T4 point (Al: 48 at%, Zr: 4 at%) and the T5 point (Al: 47 at%, Zr: 4 at%) shown in FIG. 3 as described above.
  • the content percentage of Zr at the T5 point (Al: 47 at%, Zr: 4 at%) is smaller than that at the T4 point (Al: 48 at%, Zr: 4 at%), it becomes only the ⁇ solidification. Therefore, in a case where the content percentages of Al and Zr are constituted of the composition range enclosed by the five points of the T1 point, the T2 point, the T3 point, the T4 point and the T5 point shown in FIG. 3 as described above, the form of solidification becomes either only the ⁇ solidification or the ⁇ solidification + ⁇ solidification.
  • the form of solidification becomes only the ⁇ solidification in a case where the content percentage of Nb is 2 at% and the content percentages of Al and Zr are constituted of the composition range enclosed by the four points of the W1 point (Al: 47 at%, Zr: 2 at%), the W2 point (Al: 49 at%, Zr: 2 at%), the W3 point (Al: 48 at%, Zr: 4 at%) and the W4 point (Al: 47 at%, Zr: 4 at%) shown in FIG. 4 as described above.
  • the W2 point (Al: 49 at%, Zr: 2 at%) and the W3 point (Al: 48 at%, Zr: 4 at%) causes only the ⁇ solidification.
  • the content percentage of Zr at the W1 point (Al: 47 at%, Zr: 2 at%) is smaller than that at the W2 point (Al: 49 at%, Zr: 2 at%), it becomes only the ⁇ solidification.
  • the content percentage of Zr at the W4 point (Al: 47 at%, Zr: 4 at%) is smaller than that at the W3 point (Al: 48 at%, Zr: 4 at%), it becomes only the ⁇ solidification.
  • the form of solidification becomes the ⁇ solidification + ⁇ solidification in a case where the content percentage of Nb is 1 at% or more and 2 at% or less and the content percentages of Al and Zr are constituted of the composition range enclosed by the four points of the X1 point (Al: 47 at%, Zr: 2 at%), the X2 point (Al: 48 at%, Zr: 2 at%), the X3 point (Al: 48 at%, Zr: 4 at%) and the X4 point (Al: 47 at%, Zr: 4 at%) shown in FIG. 5 as described above.
  • the form of solidification becomes only the ⁇ solidification in a case where the content percentage of Nb is 1 at% or more and 2 at% or less and the content percentages of Al and Zr are constituted of the composition range enclosed by the five points of the Y1 point (Al: 47 at%, Zr: 2 at%), the Y2 point (Al: 48 at%, Zr: 2 at%), the Y3 point (Al: 48 at%, Zr: 3 at%), the Y4 point (Al: 47.5 at%, Zr: 4 at%) and the Y5 point (Al: 47 at%, Zr: 4 at%) shown in FIG. 6 as described above.
  • test pieces of the examples A, B were prepared by using the TiAl alloy powder formed of the TiAl alloy of the examples 1, 11 and then its mechanical properties were examined. First, the preparation method of the test pieces of the examples A, B will be described. The test pieces of the examples A, B were prepared through powder molding by the hot isostatic pressing method.
  • the TiAl alloy powder was filled and sealed in pure titanium sheaths.
  • the TiAl alloy powder formed of the TiAl alloy of the example 1 was used.
  • the TiAl alloy powder formed of the TiAl alloy of the example 11 was used.
  • rapid solidified powders produced by the gas atomizing method were used.
  • the TiAl alloy powders filled in the pure titanium sheaths were subject to sealing by electron beam welding.
  • the TiAl alloy powders filled in the pure titanium sheaths were subject to a hot isostatic pressing treatment at 1250 degrees C, under 172 MPa and for three hours. After the hot isostatic pressing, the pressure was relieved and furnace cooling down to 900 degrees C was carried out, and further rapid cooling below 900 degrees C was carried out. The rapid cooling from 900 degrees C was carried out by gas fan cooling. Thus the test pieces of the examples A, B were prepared.
  • FIGs. 13 are photographs showing results of the metallographic observation on the examples A, B obtained by the optical microscope and FIG. 13A is a photograph of the test piece of the example A and FIG. 13B is a photograph of the test piece of the example B.
  • the metallographic structures of the test pieces of the examples A, B were constituted of fine crystal grains with a grain diameter of 100 micrometers or less.
  • the metallographic structures of the test pieces of the examples A, B were constituted of lamellar grains and isometric ⁇ grains, and contain borides with a grain diameter of 0.1 micrometers or less in the isometric ⁇ grains.
  • the metallographic structures of the examples 1, 11 exhibited that the volume fractions of the isometric ⁇ grains were 80 vol% or more given that the total volume fraction of the lamellar grains and the isometric ⁇ grains is 100 vol%, and the remainders were constituted of the lamellar grains.
  • volume fractions in the respective grains areal shares of the respective grains were calculated by image processing from information about contrasts of the respective grains in metallographic structural photos by the electronic microscope, and were adopted as these volume fractions. Further, any segregation of Zr were not found in the metallographic structures of the test pieces of the examples A, B.
  • the room temperature mechanical properties of the test pieces of the examples A, B were next examined.
  • the test pieces of the examples A, B were subject to room temperature tensile testing.
  • a test piece of a comparative example A was subject to room temperature tensile testing.
  • the test piece of the comparative example A was formed of a TiAl alloy containing 48 at% of Al, 2 at% of Nb and 2 at% of Cr, and the balance is formed of Ti and inevitable impurities.
  • FIG. 14 is a graph showing tensile test results.
  • strain is put on the horizontal axis and stress is put on the vertical axis, and it shows stress-strain curves of the respective test pieces.
  • the room temperature ultimate tensile strengths and the room temperature tensile fracture strains were larger.
  • the room temperature ultimate tensile strengths of the test pieces of the examples A, B were 600 MPa or more and the room temperature tensile fracture strains were 1.2 % or more.
  • the room temperature ultimate tensile strength of the test piece of the example A was 700 MPa or more and the room temperature tensile fracture strain of the test piece of the example B was 1.4 % or more. It became apparent from these results that the test pieces of the examples A, B show excellent mechanical properties and ductility, and the mechanical properties and the ductility are improved with balance.
  • FIG. 15 is a graph showing creep test results.
  • Larson-Miller parameter P is put on the horizontal axis, specific strength is put on the vertical axis, squares represent the test piece of the example A and Xs represent the test piece of the comparative example A.
  • the test piece of the example A showed excellent creep properties as compared with the test piece of the comparative example A. It was found from these results that the test piece of the example A is superior in the high temperature strength properties to the test piece of the comparative example A.
  • the present disclosure is useful in aeroplane engine components or turbine vanes or blades for generator gas turbines.
EP22820205.7A 2021-06-09 2022-06-07 Tial-legierung, tial-legierungspulver, tial-legierungsbauteil und verfahren zu dessen herstellung Pending EP4353855A1 (de)

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JPH03173017A (ja) * 1989-11-30 1991-07-26 Sumitomo Electric Ind Ltd 酸化物超電導線材の製造方法およびコイルの製造方法
ATE127860T1 (de) * 1990-05-04 1995-09-15 Asea Brown Boveri Hochtemperaturlegierung für maschinenbauteile auf der basis von dotiertem titanaluminid.
JPH05255827A (ja) * 1992-03-13 1993-10-05 Sumitomo Metal Ind Ltd ＴｉＡｌ金属間化合物基合金の製造方法
GB9714391D0 (en) * 1997-07-05 1997-09-10 Univ Birmingham Titanium aluminide alloys
DE102007060587B4 (de) * 2007-12-13 2013-01-31 Helmholtz-Zentrum Geesthacht Zentrum für Material- und Küstenforschung GmbH Titanaluminidlegierungen
US10597756B2 (en) 2012-03-24 2020-03-24 General Electric Company Titanium aluminide intermetallic compositions
JP7334896B2 (ja) * 2019-03-19 2023-08-29 国立大学法人島根大学 耐熱軽量高強度焼結体製造方法
EP3974551B1 (de) * 2019-05-23 2023-12-13 IHI Corporation Tial-legierung und verfahren zu ihrer herstellung

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