EP3974551A1 - Alliage tial et son procédé de production - Google Patents

Alliage tial et son procédé de production Download PDF

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Publication number
EP3974551A1
EP3974551A1 EP20808685.0A EP20808685A EP3974551A1 EP 3974551 A1 EP3974551 A1 EP 3974551A1 EP 20808685 A EP20808685 A EP 20808685A EP 3974551 A1 EP3974551 A1 EP 3974551A1
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Prior art keywords
tial alloy
less
tial
isostatic pressing
hot isostatic
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EP20808685.0A
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German (de)
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EP3974551B1 (fr
EP3974551A4 (fr
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Keiji Kubushiro
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IHI Corp
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IHI Corp
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    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
    • B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
    • 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
    • C22C1/02—Making non-ferrous alloys by melting
    • 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
    • C22C1/10—Alloys containing non-metals
    • C22C1/1036—Alloys containing non-metals starting from a melt
    • 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
    • C22C1/10—Alloys containing non-metals
    • C22C1/1094—Alloys containing non-metals comprising an after-treatment
    • 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
    • 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
    • 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
    • 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

Definitions

  • the present disclosure relates to a TiAl alloy and a method of manufacturing the same.
  • a TiAl (titanium aluminide) alloy is an alloy formed of an intermetallic compound of Ti and Al.
  • the TiAl alloy is excellent in the heat resistance, and has a lighter weight and larger specific strength than an Ni-base alloy, and thus, the TiAl alloy is applied to aircraft engine components such as turbine blades.
  • a TiAl alloy containing Cr and Nb is used (see Patent Literature 1).
  • an object of the present disclosure is to provide a TiAl alloy capable of improving the mechanical strength and the ductility of the TiAl alloy in a good balance, and a method of manufacturing the same.
  • a TiAl alloy according to the present disclosure contains 48 at% or more and 50 at% or less of Al, 1 at% or more and 3 at% or less of Nb, 0.3 at% or more and 1 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.
  • the content of Al may be 49 at% or more and 50 at% or less.
  • a metal structure may be formed of a lamellar grain and a ⁇ grain, and may be free of a segregation of Zr.
  • a volume fraction of the lamellar grain may be 50 volume % or more, relative to a total of the volume fraction of the lamellar grain and the volume fraction of the ⁇ grain being 100 volume %.
  • a room temperature ultimate tensile strength may be 400 MPa or more, and a room temperature tensile fracture strain may be 1.0 % or more.
  • creep strain after the elapse of 200 hours may be 2% or less when a temperature is 800 °C and applied stress is 150 MPa.
  • a method of manufacturing a TiAl alloy according to the present disclosure includes a casting step of casting a TiAl alloy raw material which contains 48 at% or more and 50 at% or less of Al, 1 at% or more and 3 at% or less of Nb, 0.3 at% or more and 1 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.
  • the method of manufacturing the TiAl alloy according to the present disclosure may include a hot isostatic pressing process step for performing a hot isostatic pressing process of applying hot isostatic pressing to the cast TiAl alloy at a temperature range from 1250 °C or higher to 1350 °C or lower, for a hour range from 1 hour or more to 5 hours or less, at an applied stress range from 158 MPa or higher to 186 MPa or lower, and then furnace cooling the cast TiAl alloy subjected to the hot isostatic pressing to 900 °C, followed by rapid cooling of the cast TiAl alloy subjected to the hot isostatic pressing from 900 °C.
  • the method of manufacturing the TiAl alloy according to the present disclosure may include a stress relieving step of relieving stress by holding the TiAl alloy subjected to the hot isostatic pressing process at a temperature range from 800 °C or higher to 950 °C or lower for a hour range from 1 hour or more to 5 hours or less.
  • the mechanical strength and the ductility of the TiAl alloy can be improved in a good balance.
  • a TiAl (titanium aluminide) alloy according to an embodiment of the present disclosure contains 48 at% or more and 50 at% or less of Al, 1 at% or more and 3 at% or less of Nb, 0.3 at% more and 1 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 composition range of each alloy component contained in the TiAl alloy is limited will be explained.
  • Al (aluminium) has a function of improving the mechanical strength and the ductility such as the room temperature ductility.
  • the content of Al is in a range from 48 at% or more to 50 at% or less.
  • the ductility degrades if the content of Al is less than 48 at%.
  • the ductility degrades if the content of Al is more than 50 at%. Therefore, the content of Al may be in a range from 49 at% or more to 50 at% or less, and the content of Al may be 49 at%. This can further improve the mechanical strength and the ductility.
  • Nb (niobium) has a function of improving the oxidation resistance and the mechanical strength.
  • the content of Nb is in a range from 1 at% or more to 3 at% or less. If the content of Nb is less than 1 at%, the oxidation resistance and the high-temperature strength degrade. If the content of Nb is more than 3 at%, the ductility such as the room temperature ductility degrades.
  • Zr zirconium has a function of improving the oxidation resistance and the mechanical strength.
  • the content of Zr is in a range from 0.3 at% or more to 1 at% or less. If the content of Zr is less than 0.3 at%, the oxidation resistance, the ductility such as the room temperature ductility, and the mechanical strength such as the high-temperature strength are degraded. Further, if the content of Zr is less than 0.3 at%, the castability degrades. If the content of Zr is more than 1 at%, the segregation may occur. The occurrence of the segregation of Zr may degrade the mechanical strength and the ductility.
  • the content of Zr may be in a range from 0.3 at% or more to 0.5 at% or less.
  • B (boron) has a function of enhancing the ductility such as the room temperature ductility by refining crystal grains.
  • the content of B is in a range from 0.05 at% or more to 0.3 at% or less. If the content of B is less than 0.05 at%, the crystal grains become coarse and the ductility degrades. If the content of B is more than 0.3 at%, the impact characteristic may be degraded.
  • the content of B is set to be in a range from 0.05 at% or more to 0.3 at% or less, the TiAl alloy is formed of fine crystal grains with a crystal grain size of 200 ⁇ m or less, and accordingly, the ductility can be improved.
  • the B has a function of improving the mechanical strength by precipitating fine borides in the crystal grains through a hot isostatic pressing process which will be described later.
  • the fine borides are formed by including borides with a grain size of 0.1 ⁇ m or less.
  • the fine borides contain TiB, TiB 2 and the like. The precipitation of the fine borides in the crystal grains can improve the mechanical strength such as the tensile strength, the fatigue strength, and the creep strength.
  • the balance of the TiAl alloy is Ti and inevitable impurities.
  • the inevitable impurities are impurities that have possibility to be mixed even if a user has no intention to add.
  • the TiAl alloy does not contain Cr (chromium), and thus, the degradation in the mechanical strength can be suppressed.
  • the TiAl alloy does not contain V (vanadium) either, and thus, the degradation in the mechanical strength and the oxidation resistance can be suppressed.
  • the TiAl alloy does not contain Mo (molybdenum), and thus, the degradation in the specific strength can be suppressed.
  • a method of manufacturing a TiAl alloy includes a casting step of melting and casting a TiAl alloy raw material which contains 48 at% or more and 50 at% or less of Al, 1 at% or more and 3 at% or less of Nb, 0.3 at% or more and 1 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.
  • the TiAl alloy raw material is melted in a vacuum induction furnace or the like and cast to form an ingot or the like. Casting of the TiAl alloy raw material may use a casting system which is used to cast a general metallic material.
  • the TiAl alloy has a lower solidification temperature than a conventional TiAl alloy, and thus, running properties during casting of the TiAl alloy can be improved.
  • a solid-liquid coexistent temperature region of the TiAl alloy may be set in a range from 1440 °C to 1510 °C. This enables the formation of a TiAl alloy component such as a turbine blade in a net-shape or a near-net-shape, and accordingly, the manufacturing cost can be reduced. Further, according to the TiAl alloy, to take a superheat is not needed, and therefore, the castability is improved.
  • the method of manufacturing the TiAl alloy may include a hot isostatic pressing process step for performing a hot isostatic pressing process of applying hot isostatic pressing (HIP) to the cast TiAl alloy at a temperature range from 1250 °C or higher to 1350 °C or lower, for an hour range from 1 hour or more to 5 hours or less, and at an applied stress range from 158 MPa or higher to 186 MPa or lower, and then furnace cooling, the cast TiAl alloy subjected to the hot isostatic pressing, to 900 °C, followed by rapid cooling of the cast TiAl alloy subjected to the hot isostatic pressing from 900 °C.
  • the application of the hot isostatic pressing process to the cast TiAl alloy can suppress casting defects such as voids and can control a metal structure.
  • the hot isostatic pressing to the cast TiAl alloy at a temperature range from 1250 °C or higher to 1350 °C or lower, for an hour range from 1 hour or more to 5 hours or less, and at an applied stress range from 158 MPa or higher to 186 MPa or lower, it is possible to suppress mainly casting defects including internal defects such as voids caused to the cast TiAl alloy. Further, it is possible to mainly control the metal structure by, after performing the hot isostatic pressing to the cast TiAl alloy, relieving the pressure and furnace cooling the cast TiAl alloy subjected to the hot isostatic pressing to 900 °C, and then, rapidly cooling the cast TiAl alloy subjected to the hot isostatic pressing from 900 °C.
  • the rapid cooling from 900 °C may be performed at a cooling rate that is equal to or higher than that of air cooling, and can be performed by gas fan cooling or the like.
  • the method of manufacturing the TiAl alloy may include a stress relieving step of relieving stress by holding the TiAl alloy subjected to the hot isostatic pressing process at a temperature range from 800 °C or higher to 950 °C or lower for an hour range from 1 hour or more to 5 hours or less. Residual stress and the like can be relieved by heat-treating the TiAl alloy subjected to the hot isostatic pressing process and relieving stress. This can further improve the ductility of the TiAl alloy.
  • the hot isostatic pressing process and the stress relief may be performed to the TiAl alloy in a vacuum atmosphere or an inert gas atmosphere with gas such as argon gas.
  • gas such as argon gas.
  • HIP equipment or the like which is used for the hot isostatic pressing of general metallic materials can be used.
  • stress relief an atmosphere furnace or the like which is used for stress relief annealing of general metallic materials can be used.
  • the metal structure of the TiAl alloy is formed of fine crystal grains with a crystal grain size of 200 ⁇ m or less. This can improve the ductility of the TiAl alloy. Further, the metal structure of the TiAl alloy is formed of lamellar grains and ⁇ grains, and no segregation of Zr is caused.
  • the lamellar grains are formed from ⁇ 2 phases formed of Ti 3 Al, and ⁇ phases formed of TiAl, which are regularly arranged one another in a layered structure.
  • the ⁇ grains are formed of TiAl. Boride having a grain size of 0.1 ⁇ m or less is contained in the ⁇ grains.
  • the boride is formed of TiB, TiB 2 and the like in a needle shape or the like.
  • the lamellar grains can improve the mechanical strength such as the tensile strength, the fatigue strength, and the creep strength.
  • the ⁇ grains can improve the ductility and the high-temperature strength. Fine borides with a grain size of 0.1 ⁇ m or less can improve the mechanical strength.
  • a volume fraction of the lamellar grains may be 50 volume % or more, and the balance may be ⁇ grains, relative to a total of the volume fraction of the lamellar grain and the volume fraction of the ⁇ grain being 100 volume %.
  • the metal structure of the TiAl alloy is mainly formed of the lamellar grains, and thus, the mechanical strength can be improved. Further, the metal structure of the TiAl alloy is free from the segregation of Zr, and thus, the degradation in the mechanical strength and the ductility can be suppressed.
  • mechanical characteristics of the TiAl alloy according to the embodiment of the present disclosure will be described.
  • mechanical characteristics of the TiAl alloy at a room temperature may be such that a room temperature ultimate tensile strength is 400 MPa or more and a room temperature tensile fracture strain is 1.0% or more.
  • high-temperature creep characteristics of the TiAl alloy may be such that creep strain after the elapse of 200 hours is 2% or less.
  • the high-temperature creep characteristics of the TiAl alloy may be such that creep strain after the elapse of 400 hours is 5% or less. Further, when the test is performed at a temperature of 800 °C and applied stress of 150 MPa, the high-temperature creep characteristics of the TiAl alloy may be such that creep strain after the elapse of 600 hours is 15% or less.
  • Fig. 1 is a diagram showing a structure of a turbine blade 10.
  • the TiAl alloy has high mechanical strength such as high-temperature strength, and thus, it is possible to improve the heat resistance of the turbine blade 10. Further, the TiAl alloy has excellent ductility such as room temperature ductility, and thus, even when the turbine blade 10 is assembled or fitted, it is possible to suppress damage to the turbine blade 10.
  • the TiAl alloy contains 48 at% or more and 50 at% or less of Al, 1 at% or more and 3 at% or less of Nb, 0.3 at% or more and 1 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. This can improve the mechanical strength and the ductility of the TiAl alloy in a good balance.
  • the method of manufacturing the TiAl alloy includes a casting step of casting a TiAl alloy raw material which contains 48 at% or more and 50 at% or less of Al, 1 at% or more and 3 at% or less of Nb, 0.3 at% or more and 1 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.
  • This enables manufacturing of the TiAl alloy with the mechanical strength and the ductility which are improved in a good balance, and also the improvement of the castability because the running properties are favorable.
  • the TiAl alloy of Example 1 contained 49.5 at% of Al, 2 at% of Nb, 0.5 at% of Zr, 0.2 at% of B, and the balance being Ti and inevitable impurities.
  • the TiAl alloy of Example 2 contained 49.5 at% of Al, 2 at% of Nb, 1 at% of Zr, 0.2 at% of B, and the balance being Ti and inevitable impurities.
  • the TiAl alloy of Reference Example 1 contained 48 at% of Al, 1 at% of Nb, 3 at% of Zr, 0.1 at% of B, and the balance being Ti and inevitable impurities.
  • the TiAl alloy of Reference Example 2 contained 49 at% of Al, 1 at% of Nb, 3 at% of Zr, 0.1 at% of B, and the balance being Ti and inevitable impurities.
  • the TiAl alloy of Reference Example 3 contained 48 at% of Al, 0.1 at% of B, and the balance being Ti and inevitable impurities.
  • the TiAl alloy of Reference Example 4 contained 49 at% of Al, 0.1 at% of B, and the balance being Ti and inevitable impurities.
  • the TiAl alloy of Reference Example 5 contained 50 at% of Al, 0.1 at% of B, and the balance being Ti and inevitable impurities.
  • the TiAl alloy of Reference Example 6 contained 49.5 at% of Al, 0.2 at% of B, and the balance being Ti and inevitable impurities.
  • the TiAl alloy of Reference Example 7 contained 49.5 at% of Al, 4 at% of Nb, 0.2 at% of Zr, 0.2 at% of B, and the balance being Ti and inevitable impurities.
  • the TiAl alloy of Reference Example 8 contained 49.5 at% of Al, 4 at% of Nb, 0.5 at% of Zr, 0.2 at% of B, and the balance being Ti and inevitable impurities.
  • the TiAl alloy of Comparative Example 1 contained 48 at% of Al, 2 at% of Nb, 2 at% of Cr, and the balance being Ti and inevitable impurities.
  • Each TiAl alloy raw material with each alloy composition shown in Table 1 was melted in a high-frequency vacuum melting furnace and cast to form an ingot of each TiAl alloy with each alloy composition.
  • Each TiAl alloy was casted, and then, subjected to a hot isostatic pressing process.
  • the hot isostatic pressing process the cast TiAl alloy was subjected to the hot isostatic pressing at a temperature of 1300 1 14 °C, for an hour of 3 ⁇ 0.1 hours, and at applied stress of 172 ⁇ 14 MPa, and then, furnace cooled to 900 °C after being subjected to the hot isostatic pressing, and thereafter, rapidly cooled from 900 °C by gas fan cooling.
  • Fig. 2 is a graph showing results of the tensile tests.
  • a horizontal axis represents the content of Al
  • a vertical axis represents strains
  • Reference Examples 3 to 5 are shown by white circles.
  • Strain indicates fracture strains.
  • the graph of Fig. 2 shows that the room temperature ductility degrades, if the content of Al is less than 48 at%, or if the content of Al is more than 50 at%. Further, the strain in Reference Examples 4 and 5 was larger than that in Reference Example 3.
  • Fig. 3 is a graph showing results of the tensile tests.
  • a horizontal axis represents the content of Zr
  • a vertical axis represents 0.2% proof stress
  • Reference Example 6 is indicated by a black circle
  • Examples 1 and 2 are indicated by black squares
  • Reference Examples 7 and 8 are indicated by white diamonds shapes.
  • Proof stress in Examples 1 and 2 was 0.2% greater than that in Reference Example 6.
  • the room temperature ductility in Reference Example 8 was lower than that in Example 1. This revealed that the ductility such as the room temperature ductility of the TiAl alloy degrades if the content of Nb is more than 3 at%.
  • Fig. 4 is photographs showing results of the observation of the metal structures that is Fig. 4(a) is a photograph of Example 1, Fig. 4(b) is a photograph of Example 2, Fig. 4(c) is a photograph of Reference Example 1, and Fig. 4(d) is a photograph of Reference Example 2.
  • the metal structures of Examples 1 and 2 were formed of fine crystal grains with a crystal grain size of 200 ⁇ m or less.
  • the metal structures of Examples 1 and 2 were formed of the lamellar grains and the ⁇ grains, and boride with a grain size of 0.1 ⁇ m or less was contained in the ⁇ grains.
  • a volume fraction of the lamellar grains was 50 volume % or more, and the balance was ⁇ grains, relative to a total of the volume fraction of the lamellar grain and the volume fraction of the ⁇ grain being 100 volume %.
  • An area ratio of each grain was calculated by applying image processing to information on the contrast of each grain in the photographs of the metal structures, and the thus obtained area ratio was regarded as the volume fraction of each grain.
  • Fig. 5 is a graph showing results of the tensile tests. Fig. 5 shows a stress-strain curve of each TiAl alloy, with a horizontal axis representing strain and a vertical axis representing stress.
  • Example 1 had greater room temperature strength than Comparative Example 1. Further, Example 1 had greater room temperature ductility than Comparative Example 1. More specifically, the room temperature ultimate tensile strength of Example 1 was 400 MPa or more, and the room temperature tensile fracture strain was 1.0% or more.
  • Fig. 6 is a graph showing results of the creep tests. Fig. 6 shows a creep curve of each TiAl alloy, with a horizontal axis representing a creep time and a vertical axis representing creep strain.
  • Example 1 had high temperature creep characteristics that are five times or more higher than those of Comparative Example 1.
  • Example 1 had more improved high temperature creep characteristics than Comparative Example 1.
  • the high temperature creep characteristics of Example 1 were such that creep strain after the elapse of 200 hours was 2% or less, when the test was performed under a condition where a test temperature was 800 °C and applied stress was 150 MPa. Further, the high temperature creep characteristics of Example 1 were such that the creep strain after the elapse of 400 hours was 5% or less, when the test was performed under a condition where a test temperature was 800 °C and applied stress was 150 MPa. Still further, the high temperature creep characteristics of Example 1 were such that the creep strain after the elapse of 600 hours was 15% or less, when the test was performed under a condition where a test temperature was 800 °C and applied stress was 150 MPa.
  • the TiAl alloy of Example 1 had excellent mechanical strength and ductility, and the mechanical strength and the ductility were improved in a good balance.
  • the TiAl alloy of Comparative Example 1 had more degraded room temperature mechanical characteristics and high temperature mechanical characteristics than the TiAl alloy of Example 1. The reason of the above degradation is considered to be caused by the influence or the like of Cr contained in the TiAl alloy of Comparative Example 1.
  • Fig. 7 is photographs showing results of the observation of the cross-sectional areas after the oxidation tests, that is, Fig. 7(a) is a photograph of Example 1, and Fig. 7(b) is a photograph of Comparative Example 1.
  • the thickness of the oxide layer of Example 1 was 2.1 ⁇ m.
  • the thickness of the oxide layer of Comparative Example 1 was 4.3 ⁇ m. From this result, it was found that Example 1 had more excellent oxidation resistance than Comparative Example 1.
  • Fig. 8 is a graph showing results of differential thermal analysis. Fig. 8 shows the solid-liquid coexistent temperature regions of the individual TiAl alloys with squares, with a horizontal axis representing each TiAl alloy and a vertical axis representing temperatures. From the graph shown in Fig. 8 , it was found that Example 1 had a lower solidification temperature than Comparative Example 1.
  • the solid-liquid coexistent temperature region of the TiAl alloy of Example 1 was in a range from 1440 °C to 1510 °C, when the solid-liquid coexistent temperature region was measured based on differential thermal analysis (DTA).
  • DTA differential thermal analysis
  • the present disclosure enables the improvement of the mechanical strength and the ductility of the TiAl alloy in a good balance, and thus, is applicable to turbine blades and the like of aircraft engine components.

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JP7317825B2 (ja) 2018-07-20 2023-07-31 ソニーセミコンダクタソリューションズ株式会社 面発光レーザおよびその製造方法
JP7226536B2 (ja) * 2019-05-23 2023-02-21 株式会社Ihi ＴｉＡｌ合金及びその製造方法
EP4353855A1 (fr) * 2021-06-09 2024-04-17 IHI Corporation Alliage tial, poudre d'alliage tial, composant d'alliage tial et leur procédé de production
CN114959361B (zh) * 2022-06-17 2023-11-28 芜湖天科航空科技有限公司 一种可析出大量有序ω相的TiAl合金及其制备方法
CN115584412B (zh) * 2022-10-08 2023-06-13 中南大学 一种双峰晶粒组织TiAl合金及其制备方法

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JPWO2020235200A1 (fr) 2020-11-26
JP7226535B2 (ja) 2023-02-21
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EP3974551B1 (fr) 2023-12-13
EP3974551A4 (fr) 2023-01-25

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