WO2009113335A1 - Alliage à base de tial et son procédé de fabrication, et lame de rotor le comprenant - Google Patents

Alliage à base de tial et son procédé de fabrication, et lame de rotor le comprenant Download PDF

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Publication number
WO2009113335A1
WO2009113335A1 PCT/JP2009/051539 JP2009051539W WO2009113335A1 WO 2009113335 A1 WO2009113335 A1 WO 2009113335A1 JP 2009051539 W JP2009051539 W JP 2009051539W WO 2009113335 A1 WO2009113335 A1 WO 2009113335A1
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WIPO (PCT)
Prior art keywords
tial
based alloy
atomic
temperature
phase
Prior art date
Application number
PCT/JP2009/051539
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English (en)
Japanese (ja)
Inventor
健太郎 新藤
利光 鉄井
雅夫 竹山
Original Assignee
三菱重工業株式会社
国立大学法人東京工業大学
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by 三菱重工業株式会社, 国立大学法人東京工業大学 filed Critical 三菱重工業株式会社
Priority to EP09720943A priority Critical patent/EP2251445A4/fr
Priority to US12/863,529 priority patent/US20100316525A1/en
Publication of WO2009113335A1 publication Critical patent/WO2009113335A1/fr

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Classifications

    • BPERFORMING OPERATIONS; TRANSPORTING
    • B21MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21KMAKING FORGED OR PRESSED METAL PRODUCTS, e.g. HORSE-SHOES, RIVETS, BOLTS OR WHEELS
    • B21K3/00Making engine or like machine parts not covered by sub-groups of B21K1/00; Making propellers or the like
    • B21K3/04Making engine or like machine parts not covered by sub-groups of B21K1/00; Making propellers or the like blades, e.g. for turbines; Upsetting of blade roots
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B21MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21JFORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
    • B21J5/00Methods for forging, hammering, or pressing; Special equipment or accessories therefor
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C14/00Alloys based on titanium
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22FCHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/16Changing 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
    • C22F1/18High-melting or refractory metals or alloys based thereon
    • C22F1/183High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
    • FMECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F05INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
    • F05BINDEXING SCHEME RELATING TO WIND, SPRING, WEIGHT, INERTIA OR LIKE MOTORS, TO MACHINES OR ENGINES FOR LIQUIDS COVERED BY SUBCLASSES F03B, F03D AND F03G
    • F05B2220/00Application
    • F05B2220/40Application in turbochargers
    • FMECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F05INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
    • F05BINDEXING SCHEME RELATING TO WIND, SPRING, WEIGHT, INERTIA OR LIKE MOTORS, TO MACHINES OR ENGINES FOR LIQUIDS COVERED BY SUBCLASSES F03B, F03D AND F03G
    • F05B2230/00Manufacture
    • F05B2230/20Manufacture essentially without removing material
    • F05B2230/25Manufacture essentially without removing material by forging
    • FMECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F05INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
    • F05CINDEXING SCHEME RELATING TO MATERIALS, MATERIAL PROPERTIES OR MATERIAL CHARACTERISTICS FOR MACHINES, ENGINES OR PUMPS OTHER THAN NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES
    • F05C2201/00Metals
    • F05C2201/04Heavy metals
    • F05C2201/0403Refractory metals, e.g. V, W
    • F05C2201/0412Titanium

Definitions

  • the present invention relates to a TiAl-based alloy, a manufacturing method thereof, and a moving blade using the same.
  • a TiAl-based alloy that is lightweight (specific gravity approximately 4) and excellent in heat resistance has attracted attention.
  • the lighter the component of the moving blade the smaller the centrifugal stress. Therefore, the maximum rotation speed can be increased, the moving blade can be increased in area, and the load stress on the disk can be reduced. Reduction can be achieved.
  • the TiAl-based alloy is an alloy mainly composed of TiAl or Ti 3 Al, which is an intermetallic compound excellent in high-temperature strength, and has excellent heat resistance.
  • Forging methods include isothermal forging using superplastic working and hot forging.
  • Constant temperature forging is a method of processing a cast alloy ingot at a low speed while heating it at a high temperature.
  • Hot forging is a method in which a cast alloy ingot is heated at a high temperature and then processed at high speed while being allowed to cool.
  • a component composition in which a ⁇ phase excellent in deformability at high temperatures is precipitated and a ⁇ phase stabilizing element such as Cr, V, Mn as the third element is used. Is added.
  • Patent Document 1 discloses superplastic working (constant temperature forging) of a TiAl-based alloy containing 43 to 47 atomic% of Al and added with Cr as a third element.
  • a TiAl-based alloy having the above composition is deformed at a low strain rate at which dynamic recrystallization occurs in a plastic working device using a heating and holding device, and has a fine structure in which a ⁇ phase is precipitated at a grain boundary of a ⁇ phase.
  • a base alloy has been obtained.
  • Patent Document 2 discloses a TiAl-based alloy containing 40 to 48 atomic% of Al and adding one or more selected from Cr and V as a third element, and a third element containing 38 to 48 atomic% of Al.
  • a TiAl-based alloy to which Mn is added is disclosed.
  • the TiAl base alloy having the above composition is subjected to high-speed plastic working (hot forging) to form a lamellar structure grain in which ⁇ 2 phase and ⁇ layer are alternately laminated, thereby improving the high temperature strength of the TiAl base alloy. ing.
  • the hot forging described in Patent Document 2 is practical and high in productivity because it can be forged in the same manner as general steel by general-purpose equipment.
  • the TiAl-based alloy described in Patent Document 2 improves the high-temperature strength by precipitating lamellar structure grains by hot forging, but has a lower creep strength and oxidation resistance than cast TiAl-based alloy. It was insufficient. For this reason, the applicable temperature of the TiAl-based alloy was 650 ° C. or less.
  • An object of the present invention is to provide a hot forged TiAl-based alloy having excellent oxidation resistance and high high-temperature strength, and a method for producing the same.
  • the present invention provides a TiAl-based alloy containing Al: (40 + a) atomic% and Nb: b atomic%, with the balance being Ti and inevitable impurities, b is the following formula (1) and (2): 0 ⁇ a ⁇ 2 (1) 3 + a ⁇ b ⁇ 7 + a (2)
  • a TiAl-based alloy satisfying the above requirements is provided.
  • this invention contains Al: (40 + a) atomic% and Nb: b atomic%, and also 1 type selected from V: c atomic%, Cr: d atomic%, and Mo: e atomic%
  • a TiAl-based alloy satisfying the above requirements is provided.
  • the TiAl-based alloy of the present invention has a temperature region that becomes a two-phase region of ⁇ phase and ⁇ phase at a high temperature in a temperature range that can be realized by a general-purpose forging facility, and hot forging in this temperature region is possible. .
  • the TiAl-based alloy of the present invention contains Nb as a ⁇ -phase stabilizing element in the above range, and the Al content is 40 atomic% or more and 42 atomic% or less, which is lower than the conventional TiAl-based alloy, so High temperature strength while maintaining. Further, by adding Nb, it becomes possible to improve the oxidation resistance as compared with the conventional hot forged TiAl-based alloy.
  • V, Cr and Mo are elements that are easy to form a ⁇ phase like Nb and have a high effect of improving the forgeability of a TiAl-based alloy.
  • V contributes to improvement in tensile strength at high temperatures.
  • Cr reduces the deformation resistance of the TiAl-based alloy.
  • Mo contributes to the improvement of creep strength.
  • the TiAl-based alloy preferably has a metal structure in which lamellar grains in which ⁇ 2 phase and ⁇ phase are alternately laminated are arranged.
  • a TiAl-based alloy having high temperature strength is obtained.
  • the present invention is a TiAl-based alloy material containing Al: (40 + a) atomic% and Nb: b atomic%, the balance being Ti and inevitable impurities, wherein the a and b are represented by the following formula (1 ) And (2): 0 ⁇ a ⁇ 2 (1) 3 + a ⁇ b ⁇ 7 + a (2)
  • the TiAl base alloy material satisfying the above conditions is held at a holding temperature within the equilibrium temperature region of the ( ⁇ + ⁇ ) phase, and the high speed plastic working is performed while cooling the TiAl base alloy material held at the holding temperature to a predetermined final processing temperature.
  • the manufacturing method of a TiAl base alloy provided with the process to perform is provided.
  • the present invention contains Al: (40 + a) atomic% and Nb: b atomic%, and is further selected from V: c atomic%, Cr: d atomic%, and Mo: e atomic%
  • the TiAl base alloy material satisfying the above conditions is held at a holding temperature within the equilibrium temperature region of the ( ⁇ + ⁇ ) phase, and the high speed plastic working is performed while cooling the TiAl base alloy material held at the holding temperature to a predetermined final processing temperature.
  • the TiAl-based alloy having the above composition has an equilibrium region of ( ⁇ + ⁇ ) phase at high temperature and contains one or more elements selected from V, Cr, and Mo and Nb, so that the ⁇ phase is stably precipitated. . Since the TiAl-based alloy material is held in the equilibrium temperature region of the ( ⁇ + ⁇ ) phase and the ⁇ phase having a high high temperature deformability is stably present, the plastic working is performed at a high speed, so that the workability is good. In addition, many strains are introduced into the alloy by performing high-speed plastic working while cooling from the holding temperature in the equilibrium temperature region of the ( ⁇ + ⁇ ) phase to the final working temperature.
  • the TiAl-based alloy exhibits high high-temperature strength.
  • the ( ⁇ + ⁇ ) phase can be stably precipitated in the metal structure.
  • the final processing temperature is 1150 ° C. or higher, high deformability capable of high-speed plastic processing can be maintained. If it is lower than 1150 ° C., the deformability is lowered, and there is a risk of cracking in the TiAl-based alloy material.
  • a forging method can be used as the high-speed plastic working.
  • a moving blade using the above TiAl-based alloy is excellent in high-temperature strength and oxidation resistance, and is a moving blade that can withstand use at 650 ° C. or higher.
  • a TiAl-based alloy having high strength at high temperatures and high oxidation resistance and excellent forgeability can be obtained.
  • the moving blade using the TiAl-based alloy of the present invention is excellent in high-temperature strength and oxidation resistance, and therefore can be applied even in a use environment of 650 ° C. or higher. Moreover, since the forgeability is good, the molding can be performed in a short time.
  • the TiAl-based alloy according to the first embodiment of the present invention contains Al: (40 + a) atomic% and Nb: b atomic%, with the balance being Ti and inevitable impurities, where a and b are the following formulae (1) and (2): 0 ⁇ a ⁇ 2 (1) 3 + a ⁇ b ⁇ 7 + a (2) Meet.
  • the TiAl-based alloy having the above composition contains Al in a proportion of 40 atomic% to 42 atomic%.
  • Al content is less than 40 atomic%, the high temperature strength decreases.
  • Al content exceeds 42 atomic%, forgeability will fall.
  • the TiAl-based alloy according to the first embodiment is excellent in oxidation resistance by containing Nb.
  • Nb also has the effect of stably depositing the ⁇ phase in a high temperature region. Since the ⁇ phase has a large deformability at high temperatures, the forgeability is improved by stably precipitating the ⁇ phase. Further, the precipitation of the ⁇ phase makes it easy to form a lamellar structure (for example, a fine lamellar structure having an average particle diameter of 1 ⁇ m to 50 ⁇ m) during the cooling process. For this reason, the high temperature strength of the alloy after forging, especially the creep strength is improved. On the contrary, when the Nb content increases, the lamellar structure becomes difficult to precipitate, and the high-temperature strength decreases. By setting the Nb content to the above ratio, a TiAl-based alloy having excellent high temperature strength and good forgeability is obtained.
  • the TiAl-based alloy according to the second embodiment of the present invention contains Al: (40 + a) atomic% and Nb: b atomic%, and further includes V: c atomic%, Cr: d atomic%, and Mo: e. It contains one or more elements selected from atomic%, the balance is made of Ti and inevitable impurities, and a to e are the following formulas (3) to (9): 0 ⁇ a ⁇ 2 (3) 3 + a ⁇ b + 1.0c + 1.8d + 3.8e ⁇ 7 + a (4) b ⁇ 2 (5) c ⁇ 0 (6) d ⁇ 0 (7) e ⁇ 0 (8) c + d + e> 0 (9) Meet.
  • V, Cr, and Mo are elements that are easy to form a ⁇ phase like Nb.
  • the effect of ⁇ -phase precipitation of Cr and Mo is 1.8 times and 3.8 times that of Nb, respectively, and the ⁇ -phase can be stably precipitated with a small amount of addition compared to Nb.
  • V has the effect of further improving the tensile strength at high temperatures.
  • Cr has the effect of reducing the deformation resistance of the TiAl-based alloy, and forgeability is further improved.
  • Mo has the effect of further improving the creep strength.
  • Nb, V, Cr, and Mo are preferably within the above range in consideration of forgeability and high temperature strength.
  • a method for producing the TiAl-based alloy of the first embodiment and the second embodiment by the hot forging method will be described below.
  • a TiAl-based alloy material (for example, ingot shape) having a composition represented by the above composition is melted.
  • the TiAl-based alloy material is heated in a heavy oil furnace or the like and held for a long time at a holding temperature within the equilibrium temperature region of the ( ⁇ + ⁇ ) phase. By this step, an ⁇ phase and a ⁇ phase are precipitated in the metal structure.
  • the holding temperature is 1150 ° C. to 1350 ° C. in the case of the TiAl-based alloy having the above composition formula.
  • the retained TiAl-based alloy material is removed from the furnace, and high-speed plastic working is performed using a general-purpose hydraulic press machine or the like while the temperature of the alloy material is in the ( ⁇ + ⁇ ) phase equilibrium temperature region. Strain is introduced into the ⁇ phase by high-speed plastic working during the cooling process. Dynamic recrystallization takes place starting from strain, and as a result, fine lamellar grains in which ⁇ 2 and ⁇ phases are alternately laminated are formed. From the ⁇ phase, the ⁇ phase precipitates during the cooling process to form an equiaxed microstructure. In the case of the TiAl-based alloy having the above composition, if the final processing temperature is 1150 ° C.
  • plastic processing can be performed in a state where a ⁇ phase having a large deformability is precipitated. If the final processing temperature is less than 1150 ° C., the deformability is lowered and material cracking occurs. On the other hand, if the cooling rate is too fast, massive transformation occurs and a lamellar structure is not formed. If the cooling rate is too slow, the lamellar spacing increases and the material strength decreases.
  • the cooling rate is preferably about 50 to 700 ° C./min, for example.
  • a moving blade manufactured using the TiAl-based alloy of this embodiment is excellent in high-temperature strength and oxidation resistance at high temperatures.
  • the moving blade is manufactured by the following procedure.
  • a TiAl-based alloy material (such as an ingot shape) having the composition of the first embodiment or the second embodiment is melted.
  • hot free forging is performed on the TiAl-based alloy material to improve the forgeability in the die forging in the subsequent process.
  • the alloy material is cut into a rod shape and used as a rough ground for die forging of a moving blade.
  • a rod-like TiAl-based alloy material may be melted when cost is important.
  • the shape of the bar is processed into a dogbone shape so that the final wing shape can be easily given.
  • the rod-shaped TiAl-based alloy material is heated in a heavy oil furnace or the like and held at a holding temperature in the ( ⁇ + ⁇ ) phase equilibrium temperature region.
  • the alloy material is molded by forging with a general-purpose hammer press using forged wasteland.
  • die forging in order to prevent thermal deformation during the cooling process, it is cooled in a heat insulating material or in a low temperature furnace of about 600 ° C.
  • the forged product is formed into a moving blade shape by cutting or the like.
  • the TiAl-based alloy of this embodiment is excellent in forgeability, it is possible to form a moving blade, which is a large member, in a simple process in a short time.
  • Example 1 TiAl-based alloy ingots having the components shown in Examples 1-1 to 1-4 in Table 1 were produced by casting. Each ingot was cut to a predetermined size and surface-treated to obtain a columnar TiAl-based alloy material having a diameter of 80 mm and a height of 60 mm.
  • Each TiAl base alloy material was heated and held at 1300 ° C. in a heavy oil furnace. After holding, the TiAl-based alloy material was taken out from the heavy oil furnace, and upset forging with a forging ratio of 3 s was performed using a general-purpose 300-ton hydraulic press. The TiAl-based alloy material was taken out and finished forging within 10 seconds. Cooling after forging was air cooling on an iron mount. As heat treatment after forging, stress relief annealing was performed at 800 ° C. for 24 hours using a muffle furnace.
  • Comparative example TiAl-based alloy ingots having the components shown in Comparative Examples 1-1 to 1-9 in Table 1 were produced by casting. Each ingot was cut and subjected to surface processing to obtain a columnar TiAl-based alloy material having a diameter of 80 mm and a height of 60 mm. In the same manner as in Example 1, forging of each TiAl-based alloy material and stress removal annealing after forging were performed.
  • Examples 2 to 5 TiAl-based alloy ingots comprising the components shown in Examples 2 to 5 in Table 1 were produced by casting. The ingot was cut and surface-treated to obtain a columnar TiAl-based alloy material having a diameter of 80 mm and a height of 60 mm. In the same manner as in Example 1, forging of the TiAl-based alloy material of Example 2 and stress removal annealing after forging were performed.
  • Each TiAl-based alloy was subjected to forgeability evaluation, creep strength test and oxidation resistance test. Forgeability evaluation visually confirmed whether or not the ingot after forging was cracked. When cracks did not occur, forgeability was good ( ⁇ ), and when cracks occurred, forgeability was poor (x).
  • forgeability was good
  • x forgeability was poor
  • the creep rupture time was 25 hours or longer and the high-temperature strength was good ( ⁇ ), and the low temperature strength was insufficient (x) in less than 25 hours.
  • oxidation resistance test a cubic test piece having a side of 2.8 mm was cut out from the ingot after annealing, heated at 870 ° C. for 50 hours, and compared in terms of increase in oxidation per unit area.
  • increase in oxidation was 0.01 g / mm 2 or less, the oxidation resistance was good ( ⁇ ), and when it exceeded 0.01 g / mm 2 , the oxidation resistance was insufficient (x).
  • the TiAl-based alloys of Examples 1-1 to 1-4 all had a metal structure in which lamellar grains were precipitated, and high high-temperature strength was obtained.
  • the oxidation resistance was significantly improved as compared with the TiAl-based alloy of Comparative Example 1-9 containing no Nb.
  • Table 2 shows the evaluation results of the deformation resistance measurement, the tensile test, the creep strength test, and the oxidation resistance test for the TiAl-based alloys of Example 1-1 and Examples 2 to 5.
  • the deformation resistance was measured by cutting a cylindrical test piece having a diameter of 7 mm and a length of 12 mm from the ingot after annealing, holding at 1250 ° C. using high-frequency heating, and a deformation rate of 100 mm / second.
  • the tensile test was performed in a 700 ° C. atmosphere on a test piece having a total length of 60 mm, a rating part diameter of 4 mm, and a rating part length of 20 mm cut out from the ingot after annealing.
  • Example 2 and 3 containing V the tensile strength at break was improved as compared with Example 1-1.
  • Example 4 containing Cr the deformation resistance was small. That is, the deformability at high temperature increased.
  • Example 5 containing Mo the creep strength was greatly improved.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Forging (AREA)
  • Turbine Rotor Nozzle Sealing (AREA)

Abstract

L'invention porte sur un alliage à base de TiAl forgé à chaud, présentant une excellente résistance à l'oxydation et une résistance élevée à des températures supérieures. L'invention porte également sur un procédé pour fabriquer l'alliage. L'invention porte spécifiquement sur un alliage à base de TiAl comprenant (40 + a) % atomique de Al et b % atomique de Nb, le reste étant Ti et des impuretés inévitables, où a et b satisfont aux exigences représentées par les formules suivantes (1) et (2). 0 ≤ a ≤ 2 (1) 3 + a ≤ b ≤ 7 + a (2). Specifiquement, l'invention porte également sur un alliage à base de TiAl comprenant (40 + a) % atomique de Al, b % atomique de Nb et au moins un élément choisi parmi c % atomique de V, d % atomique de Cr et e % atomique de Mo, le reste étant Ti et des impuretés inévitables, où a à e satisfont aux exigences représentées par les formules suivantes (3) à (9). 0 ≤a ≤ 2 (3) 3 + a ≤ b + 1,0c + 1,8d + 3,8e ≤ 7 + a (4) b ≥ 2 (5) c ≥ 0 (6) d ≥ 0 (7) e ≥ 0 (8) c + d + e > 0 (9).
PCT/JP2009/051539 2008-03-12 2009-01-30 Alliage à base de tial et son procédé de fabrication, et lame de rotor le comprenant WO2009113335A1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
EP09720943A EP2251445A4 (fr) 2008-03-12 2009-01-30 Alliage à base de tial et son procédé de fabrication, et lame de rotor le comprenant
US12/863,529 US20100316525A1 (en) 2008-03-12 2009-01-30 TiAl-BASED ALLOY, PROCESS FOR PRODUCING SAME, AND ROTOR BLADE USING SAME

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2008-062690 2008-03-12
JP2008062690A JP2009215631A (ja) 2008-03-12 2008-03-12 TiAl基合金及びその製造方法並びにそれを用いた動翼

Publications (1)

Publication Number Publication Date
WO2009113335A1 true WO2009113335A1 (fr) 2009-09-17

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US (1) US20100316525A1 (fr)
EP (1) EP2251445A4 (fr)
JP (1) JP2009215631A (fr)
WO (1) WO2009113335A1 (fr)

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JP2015151612A (ja) * 2014-02-19 2015-08-24 国立研究開発法人物質・材料研究機構 熱間鍛造型TiAl基合金およびその製造方法
JP6202556B2 (ja) * 2013-06-19 2017-09-27 国立研究開発法人物質・材料研究機構 熱間鍛造型TiAl基合金
US10208360B2 (en) 2013-06-19 2019-02-19 National Institute For Materials Science Hot-forged TiAl-based alloy and method for producing the same
CN103757578B (zh) * 2014-01-24 2016-03-30 中国科学院金属研究所 一种γ-TiAl合金细小全片层组织制备方法
EP2905350A1 (fr) * 2014-02-06 2015-08-12 MTU Aero Engines GmbH Alliage TiAl haute température
CN103820672B (zh) * 2014-03-12 2017-05-03 北京工业大学 一种Cr、Mn合金化β相凝固高Nb‑TiAl合金及其制备方法
DE102015103422B3 (de) 2015-03-09 2016-07-14 LEISTRITZ Turbinentechnik GmbH Verfahren zur Herstellung eines hochbelastbaren Bauteils aus einer Alpha+Gamma-Titanaluminid-Legierung für Kolbenmaschinen und Gasturbinen, insbesondere Flugtriebwerke
CN105397000A (zh) * 2015-12-02 2016-03-16 贵州安大航空锻造有限责任公司 钛合金板形锻件的轧制方法
JP6687118B2 (ja) * 2016-09-02 2020-04-22 株式会社Ihi TiAl合金及びその製造方法
WO2022219991A1 (fr) 2021-04-16 2022-10-20 株式会社神戸製鋼所 Alliage tial pour forgeage, matériau à base d'alliage tial et procédé de production d'un matériau d'alliage tial
CN114603141B (zh) * 2022-03-09 2022-12-27 西北工业大学 一种TiAl合金叶片模锻成形的方法

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US20100316525A1 (en) 2010-12-16

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