JP2009215631A - Titanium-aluminum-based alloy and production method therefor, and moving blade using the same - Google Patents
Titanium-aluminum-based alloy and production method therefor, and moving blade using the same Download PDFInfo
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21K—MAKING FORGED OR PRESSED METAL PRODUCTS, e.g. HORSE-SHOES, RIVETS, BOLTS OR WHEELS
- B21K3/00—Making engine or like machine parts not covered by sub-groups of B21K1/00; Making propellers or the like
- B21K3/04—Making 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
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- 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
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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
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- 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
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
- F05B—INDEXING SCHEME RELATING TO WIND, SPRING, WEIGHT, INERTIA OR LIKE MOTORS, TO MACHINES OR ENGINES FOR LIQUIDS COVERED BY SUBCLASSES F03B, F03D AND F03G
- F05B2220/00—Application
- F05B2220/40—Application in turbochargers
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
- F05B—INDEXING SCHEME RELATING TO WIND, SPRING, WEIGHT, INERTIA OR LIKE MOTORS, TO MACHINES OR ENGINES FOR LIQUIDS COVERED BY SUBCLASSES F03B, F03D AND F03G
- F05B2230/00—Manufacture
- F05B2230/20—Manufacture essentially without removing material
- F05B2230/25—Manufacture essentially without removing material by forging
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
- F05C—INDEXING SCHEME RELATING TO MATERIALS, MATERIAL PROPERTIES OR MATERIAL CHARACTERISTICS FOR MACHINES, ENGINES OR PUMPS OTHER THAN NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES
- F05C2201/00—Metals
- F05C2201/04—Heavy metals
- F05C2201/0403—Refractory metals, e.g. V, W
- F05C2201/0412—Titanium
Abstract
Description
本発明は、ＴｉＡｌ基合金及びその製造方法、並びにそれを用いた動翼に関するものである。 The present invention relates to a TiAl-based alloy, a manufacturing method thereof, and a moving blade using the same.
ガスタービンや過給機の動翼などに用いる材料として、軽量（比重約４）で耐熱性に優れるＴｉＡｌ基合金が注目されている。特に、大型の回転動翼の場合、動翼の構成部材が軽量であるほど遠心応力が少なくなるので、最高到達回転数の向上や動翼の大面積化、さらにはディスク部分への負荷応力の低減を図ることができる。 As a material used for a gas turbine, a rotor blade of a supercharger, and the like, a TiAl-based alloy that is lightweight (specific gravity about 4) and excellent in heat resistance has attracted attention. In particular, in the case of a large rotating blade, 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.
ＴｉＡｌ基合金は、高温強度に優れた金属間化合物であるＴｉＡｌやＴｉ３Ａｌを主体とする合金であり、耐熱性に優れている。しかし、ＴｉＡｌ基合金は鋳造性が悪く、鋳造での大型部品の製造が困難であるため、鍛造による成形が研究されている。鍛造方法には、超塑性加工を利用した恒温鍛造と熱間鍛造とがある。恒温鍛造は、鋳造合金のインゴットを高温で加熱しながら低速で加工する方法である。熱間鍛造は、鋳造合金インゴットを高温で加熱した後、放冷しながら高速で加工する方法である。この熱間鍛造では、ＴｉＡｌ基合金の鍛造性を向上させるために、高温での変形能に優れるβ相が析出する成分組成とし、第３元素としてＣｒ，Ｖ，Ｍｎなどのβ相安定化元素が添加される。 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. However, since TiAl-based alloys have poor castability and it is difficult to produce large parts by casting, forming by forging has been studied. 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. In this hot forging, in order to improve the forgeability of the TiAl-based alloy, a component composition in which a β phase excellent in deformability at high temperatures is precipitated and a β phase stabilizing element such as Cr, V, Mn as the third element is used. Is added.
特許文献１には、Ａｌを４３〜４７原子％含有し、第３元素としてＣｒを添加したＴｉＡｌ基合金を、超塑性加工（恒温鍛造）することが開示されている。上記組成のＴｉＡｌ基合金を、加熱保持装置を用いた塑性加工装置で、動的再結晶が起こる低歪速度で変形し、γ相の結晶粒界にβ相を析出させた微細構造を有するＴｉＡｌ基合金を得ている。 Patent Document 1 discloses superplastic working (constant temperature forging) of a TiAl-based alloy containing 43 to 47 atomic percent 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 β phase is precipitated at a grain boundary of a γ phase. A base alloy has been obtained.
特許文献２には、Ａｌを４０〜４８原子％含有し第３元素としてＣｒ及びＶから選択される１種以上を添加したＴｉＡｌ基合金、及び、Ａｌを３８〜４８原子％含有し第３元素としてＭｎを添加したＴｉＡｌ基合金が開示されている。上記組成のＴｉＡｌ基合金に対して高速塑性加工（熱間鍛造）を施し、α２相とγ層とが交互に積層されたラメラ組織粒を形成させて、ＴｉＡｌ基合金の高温強度を向上させている。
特許文献１に記載の超塑性加工は、高温に保持しながらの低歪速度での塑性加工であるので、生産性が低く工業的な実用性は低い。 The superplastic working described in Patent Document 1 is a plastic working at a low strain rate while being kept at a high temperature, so that productivity is low and industrial practicality is low.
一方、特許文献２に記載される熱間鍛造は、汎用設備にて一般鋼材とほぼ同様の鍛造加工が可能であるため、生産性が高く実用的である。
しかし、特許文献２に記載されるＴｉＡｌ基合金は、熱間鍛造によりラメラ組織粒を析出させて高温強度を向上させているが、鋳造ＴｉＡｌ基合金に比べてクリープ強度が低く、耐酸化性も不十分であった。このため、ＴｉＡｌ基合金の適用可能温度は６５０℃以下となっていた。
On the other hand, 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.
However, 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.
本発明は、耐酸化性に優れ、且つ、高温強度の高い熱間鍛造ＴｉＡｌ基合金及びその製造方法を提供することを目的とする。 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.
上記課題を解決するために、本発明は、Ａｌ：（４０＋ａ）原子％と、Ｎｂ：ｂ原子％とを含有し、残部がＴｉ及び不可避的不純物からなるＴｉＡｌ基合金であって、前記ａ及びｂが以下の式（１）及び（２）：
０≦ａ≦２ （１）
３＋ａ≦ｂ≦７＋ａ （２）
を満たすＴｉＡｌ基合金を提供する。
In order to solve the above-mentioned problems, 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.
また、本発明は、Ａｌ：（４０＋ａ）原子％と、Ｎｂ：ｂ原子％とを含有し、更にＶ：ｃ原子％、Ｃｒ：ｄ原子％、及びＭｏ：ｅ原子％から選択される１種以上の元素を含有し、残部がＴｉ及び不可避的不純物からなるＴｉＡｌ基合金であって、前記ａ乃至ｅが以下の式（３）乃至（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）
を満たすＴｉＡｌ基合金を提供する。
Further, 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% A TiAl-based alloy containing the above elements, the balance being Ti and inevitable impurities, wherein 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)
A TiAl-based alloy satisfying the above requirements is provided.
Ａｌ含有量が高くなると高温強度は向上する。しかし、Ａｌ含有量が高いと、高温での変形能に優れるβ相が析出しない、あるいは、析出温度域が高いために、鍛造性が悪くなる。本発明のＴｉＡｌ基合金は、汎用の鍛造設備で実現可能な温度範囲の高温でα相とβ相の２相領域となる温度領域を有し、この温度領域での熱間鍛造が可能である。本発明のＴｉＡｌ基合金は、β相安定化元素としてＮｂを上記範囲で含有し、Ａｌ含有量が４０原子％以上４２原子％以下と従来のＴｉＡｌ基合金よりも低くすることにより、鍛造性を維持しつつ高い高温強度を有する。また、Ｎｂを添加することにより、従来の熱間鍛造ＴｉＡｌ基合金よりも耐酸化性を向上させることが可能となる。 The high temperature strength improves as the Al content increases. However, if the Al content is high, the β phase, which is excellent in deformability at high temperatures, does not precipitate, or because the precipitation temperature range is high, the forgeability deteriorates. The TiAl-based alloy of the present invention has a temperature region that becomes a two-phase region of α phase and β 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 β-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, thereby improving the forgeability. 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及びＭｏは、Ｎｂと同様にβ相を形成させやすく、ＴｉＡｌ基合金の鍛造性を向上させる効果が高い元素である。Ｎｂの他にＶ，Ｃｒ及びＭｏから選択される１種以上の元素を上記の割合で含有することで、鍛造性に優れたＴｉＡｌ基合金となる。更に、Ｖは高温での引張強度向上に寄与する。Ｃｒは、ＴｉＡｌ基合金の変形抵抗を低下させる。Ｍｏはクリープ強度向上に寄与する。Ｖ，Ｃｒ及びＭｏから選択される１種以上の元素を含有することにより、合金性能を更に向上させることが可能となる。 V, Cr and Mo are elements that are easy to form a β phase like Nb and have a high effect of improving the forgeability of the TiAl-based alloy. By containing at least one element selected from V, Cr, and Mo in addition to Nb in the above ratio, a TiAl-based alloy having excellent forgeability can be obtained. Furthermore, 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. By including one or more elements selected from V, Cr and Mo, the alloy performance can be further improved.
上記発明において、ＴｉＡｌ基合金が、α２相とγ相とが交互に積層されたラメラ粒が配列してなる金属組織を有することが好ましい。ラメラ粒が配列した金属組織を有することで、高温強度の高いＴｉＡｌ基合金となる。 In the above invention, the TiAl-based alloy preferably has a metal structure in which lamellar grains in which α 2 phase and γ phase are alternately laminated are arranged. By having a metal structure in which lamella grains are arranged, a TiAl-based alloy having high temperature strength is obtained.
本発明は、Ａｌ：（４０＋ａ）原子％と、Ｎｂ：ｂ原子％とを含有し、残部がＴｉ及び不可避的不純物からなるＴｉＡｌ基合金素材であって、前記ａ及びｂが以下の式（１）及び（２）：
０≦ａ≦２ （１）
３＋ａ≦ｂ≦７＋ａ （２）
を満たすＴｉＡｌ基合金素材を、（α＋β）相の平衡温度領域内の保持温度に保持する工程と、該保持温度に保持したＴｉＡｌ基合金素材を、所定の最終加工温度まで冷却しながら高速塑性加工する工程とを備えるＴｉＡｌ基合金の製造方法を提供する。
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 (α + β) 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.
また、本発明は、Ａｌ：（４０＋ａ）原子％と、Ｎｂ：ｂ原子％とを含有し、更にＶ：ｃ原子％、Ｃｒ：ｄ原子％、及びＭｏ：ｅ原子％から選択される１種以上の元素を含有し、残部がＴｉ及び不可避的不純物からなるＴｉＡｌ基合金素材であって、前記ａ乃至ｅが以下の式（３）乃至（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）
を満たすＴｉＡｌ基合金素材を、（α＋β）相の平衡温度領域内の保持温度に保持する工程と、該保持温度に保持したＴｉＡｌ基合金素材を、所定の最終加工温度まで冷却しながら高速塑性加工する工程とを備えるＴｉＡｌ基合金の製造方法を提供する。
Further, 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% A TiAl-based alloy material containing the above elements, the balance being Ti and inevitable impurities, wherein 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)
The TiAl base alloy material satisfying the above conditions is held at a holding temperature within the equilibrium temperature region of the (α + β) 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.
上記組成のＴｉＡｌ基合金は、高温において（α＋β）相の平衡領域を有するとともに、Ｖ，Ｃｒ及びＭｏから選択される１種以上の元素及びＮｂを含有するので、β相が安定して析出する。ＴｉＡｌ基合金素材を（α＋β）相の平衡温度領域保持して、高温変形能の高いβ相が安定して存在する状態で、高速にて塑性加工を施すので、加工性が良好である。また、（α＋β）相の平衡温度領域の保持温度から最終加工温度まで冷却する間に高速塑性加工を施すことにより、合金中に歪みが多数導入される。この歪みを起点として動的再結晶が誘起され、最終的に微細なラメラ粒が配列する金属組織が形成される。このラメラ粒が存在する金属組織とすることで、ＴｉＡｌ基合金は高い高温強度を示す。 The TiAl-based alloy having the above composition has an equilibrium region of (α + β) phase at high temperature and contains one or more elements selected from V, Cr, and Mo and Nb, so that the β phase is stably precipitated. . Since the TiAl-based alloy material is held in the equilibrium temperature region of the (α + β) phase and the β 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 (α + β) phase to the final working temperature. Starting from this strain, dynamic recrystallization is induced, and finally a metal structure in which fine lamellar grains are arranged is formed. By using a metal structure in which these lamella grains are present, the TiAl-based alloy exhibits high high-temperature strength.
上記発明において、前記保持温度が、１１５０℃以上１３５０℃以下であれば、金属組織内に（α＋β）相が安定して析出させることができる。 In the said invention, if the said holding temperature is 1150 degreeC or more and 1350 degrees C or less, an ((alpha) + (beta)) phase can be stably deposited in a metal structure.
上記発明において、前記最終加工温度が、１１５０℃以上であれば、高速塑性加工が可能な高い変形能を維持できる。１１５０℃未満であると、変形能が低下してＴｉＡｌ基合金素材に割れが発生する恐れがある。 In the said invention, if the said final processing temperature is 1150 degreeC or more, the high deformability in which a high-speed plastic processing is possible 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.
上記発明において、前記高速塑性加工として鍛造法を用いることができる。 In the above invention, a forging method can be used as the high-speed plastic working.
上記のＴｉＡｌ基合金を用いた動翼は、高温強度と耐酸化性に優れ、６５０℃以上での使用に耐え得る動翼となる。 A moving blade using the 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.
本発明によれば、高温強度と耐酸化性が高く、鍛造性に優れたＴｉＡｌ基合金とすることができる。本発明のＴｉＡｌ基合金を用いた動翼は、高温強度と耐酸化性に優れるため、６５０℃以上の使用環境においても適用可能である。また、鍛造性が良好であるため、短時間での成形が可能である。 According to the present invention, a TiAl-based alloy having high high-temperature strength 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.
本発明の第一実施形態に係るＴｉＡｌ基合金は、Ａｌ：（４０＋ａ）原子％と、Ｎｂ：ｂ原子％とを含有し、残部がＴｉ及び不可避的不純物からなり、ａ及びｂが以下の式（１）及び（２）：
０≦ａ≦２ （１）
３＋ａ≦ｂ≦７＋ａ （２）
を満たす。
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.
上記組成のＴｉＡｌ基合金は、Ａｌを４０原子％以上４２原子％の割合で含有する。Ａｌ含有量が４０原子％未満であると、高温強度が低下する。Ａｌ含有量が４２原子％を超えると、鍛造性が低下する。 The TiAl-based alloy having the above composition contains Al in a proportion of 40 atomic% to 42 atomic%. When the Al content is less than 40 atomic%, the high temperature strength decreases. When Al content exceeds 42 atomic%, forgeability will fall.
第一実施形態のＴｉＡｌ基合金は、Ｎｂを含有することにより耐酸化性に優れる。Ｎｂはβ相を高温領域で安定して析出させる効果もある。β相は高温での変形能が大きいため、β相を安定して析出させることで鍛造性が向上する。また、β相が析出することによって、冷却過程でラメラ組織（例えば、平均粒径が１μｍから５０μｍの微細ラメラ組織）が形成されやすくなる。このため、鍛造後の合金の高温強度、特にクリープ強度が向上する。Ｎｂ含有量が多くなると逆にラメラ組織が析出しにくくなり、高温強度が低下する。Ｎｂ含有量を上記割合とすることで、高温強度に優れ鍛造性が良好なＴｉＡｌ基合金となる。 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 β phase in a high temperature region. Since the β phase has a large deformability at high temperatures, the forgeability is improved by stably precipitating the β phase. Further, the precipitation of the β phase makes it easy to form a lamellar structure (for example, a fine lamellar structure having an average particle diameter of 1 μm to 50 μm) 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.
本発明の第二実施形態に係るＴｉＡｌ基合金は、Ａｌ：（４０＋ａ）原子％と、Ｎｂ：ｂ原子％とを含有し、更にＶ：ｃ原子％、Ｃｒ：ｄ原子％、及びＭｏ：ｅ原子％から選択される１種以上の元素を含有し、残部がＴｉ及び不可避的不純物からなり、ａ乃至ｅが以下の式（３）乃至（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）
を満たす。
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及びＭｏは、Ｎｂと同様にβ相を形成させやすい元素である。Ｎｂのβ相析出効果をＮｂ量：ｂ（原子％）に換算した値をＮｂ当量とすると、各元素のＮｂ当量は以下のようになる。
Ｖ：ｂ＝１．０ｃ
Ｃｒ：ｂ＝１．８ｄ
Ｍｏ：ｂ＝３．８ｅ
すなわち、Ｖのβ相析出効果はＮｂの場合と同等である。Ｃｒ及びＭｏのβ相析出効果は、それぞれＮｂの１．８倍、３．８倍であり、Ｎｂに比べて少量の添加でβ相を安定して析出させることができる。
V, Cr, and Mo are elements that are easy to form a β phase like Nb. When the value obtained by converting the β-phase precipitation effect of Nb into Nb amount: b (atomic%) is Nb equivalent, the Nb equivalent of each element is as follows.
V: b = 1.0c
Cr: b = 1.8d
Mo: b = 3.8e
That is, the β phase precipitation effect of V is equivalent to that of Nb. The effect of β-phase precipitation of Cr and Mo is 1.8 times and 3.8 times that of Nb, respectively, and the β-phase can be stably precipitated with a small amount of addition compared to Nb.
β相を安定して析出させる効果の他に、Ｖは高温での引張強度を更に向上させる効果がある。ＣｒはＴｉＡｌ基合金の変形抵抗を低下させる効果があり、鍛造性が更に向上する。Ｍｏはクリープ強度を更に向上させる効果がある。 In addition to the effect of stably precipitating the β phase, 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及びＭｏの含有量は、鍛造性及び高温強度を考慮すると、上記割合の範囲内とすると良い。 The contents of Nb, V, Cr, and Mo are preferably set within the above-mentioned ratio range in consideration of forgeability and high-temperature strength.
第一実施形態および第二実施形態のＴｉＡｌ基合金を熱間鍛造法で製造する方法を、以下に説明する。
上記組成で表される組成となるＴｉＡｌ基合金素材（例えばインゴット形状）を溶製する。
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.
ＴｉＡｌ基合金素材を重油炉などで加熱して、（α＋β）相の平衡温度領域内の保持温度で長時間保持する。この工程により、金属組織内にα相及びβ相を析出させる。保持温度は、上記組成式のＴｉＡｌ基合金の場合は、１１５０℃から１３５０℃となる。 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 (α + β) phase. By this step, an α phase and a β 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.
保持後のＴｉＡｌ基合金素材を炉から取り出し、合金素材の温度が（α＋β）相平衡温度領域である間に、汎用の油圧プレス機などを用いて、高速塑性加工を施す。冷却過程での高速塑性加工により、α相に歪みが導入される。歪みを起点として動的再結晶がおこり、その結果、α２相とγ相とが交互に積層された微細なラメラ粒が形成する。β相からは冷却過程でγ相が析出して等軸的な微細組織が形成される。上記組成のＴｉＡｌ基合金の場合、最終加工温度は１１５０℃以上とすれば、変形能が大きいβ相が析出した状態で塑性加工を施すことができる。最終加工温度が１１５０℃未満であると、変形能が低下して材料割れが発生する。また、冷却速度が速すぎると、マッシブ変態を生じてラメラ組織が形成されず、冷却速度が遅すぎるとラメラ間隔が広がり材料強度が低下する。冷却速度は、例えば５０〜７００℃／分程度とすることが好ましい。 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 (α + β) phase equilibrium temperature region. Strain is introduced into the α phase by high-speed plastic working during the cooling process. Dynamic recrystallization occurs starting from strain, and as a result, fine lamellar grains in which α 2 and γ phases are alternately stacked are formed. From the β phase, the γ 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. or more, plastic processing can be performed in a state where a β 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.
本実施形態のＴｉＡｌ基合金を用いて製造された動翼は、高温強度及び高温での耐酸化性に優れる。動翼は以下の手順にて製造される。
第一実施形態または第二実施形態の組成のＴｉＡｌ基合金素材（インゴット形状など）を溶製する。次に、ＴｉＡｌ基合金素材に熱間自由鍛造を施し、後工程の型鍛造における鍛造性を向上させる。その後、合金素材を棒状に切断し、動翼の型鍛造の荒地とする。荒地の製造は、コストを重視する場合には、棒状のＴｉＡｌ基合金素材を溶製しても良い。棒材の形状は、最終的な翼形状を付与しやすいように、ドッグボーン形状などに加工する。
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. Next, hot free forging is performed on the TiAl-based alloy material to improve the forgeability in the die forging in the subsequent process. After that, the alloy material is cut into a rod shape and used as a rough ground for die forging of a moving blade. In the case of manufacturing wasteland, 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.
型鍛造工程では、棒状のＴｉＡｌ基合金素材を重油炉などで加熱し、（α＋β）相平衡温度領域内の保持温度に保持する。合金素材を炉から取り出した直後に、鍛造荒地を使用して、汎用のハンマープレスで型鍛造を施して成形する。型鍛造後は、冷却過程での熱変形を防ぐために断熱材中あるいは６００℃程度の低温炉中で除冷する。最後に、鍛造品を切削加工などで動翼形状に成形する。 In the die forging step, the rod-like TiAl-based alloy material is heated in a heavy oil furnace or the like and held at a holding temperature within the (α + β) phase equilibrium temperature region. Immediately after taking out the alloy material from the furnace, it is molded by forging with a general-purpose hammer press using forged wasteland. After 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. Finally, the forged product is formed into a moving blade shape by cutting or the like.
本実施形態のＴｉＡｌ基合金は鍛造性に優れるため、大型部材である動翼を簡略な工程にて短時間で形成することが可能である。 Since 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.
（実施例１）
表１の実施例１−１乃至実施例１−４に示す成分からなるＴｉＡｌ基合金インゴットを鋳造により製造した。各インゴットを所定の寸法となるように切断して表面加工を施し、直径８０ｍｍ、高さ６０ｍｍの柱状のＴｉＡｌ基合金素材を得た。
Example 1
TiAl-based alloy ingots comprising 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.
各ＴｉＡｌ基合金素材を重油炉内で１３００℃に加熱保持した。保持後、重油炉からＴｉＡｌ基合金素材を取り出し、汎用の３００トン油圧プレスを用いて、鍛造比３ｓの据え込み鍛造を行った。なお、ＴｉＡｌ基合金素材取出しから鍛造終了まで１０秒以内で実施した。鍛造後の冷却は、鉄製架台上にて大気放冷とした。鍛造後熱処理として、マッフル炉を使用して８００℃、２４時間の応力除去焼鈍を実施した。 Each TiAl-based 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.
（比較例）
表１の比較例１−１乃至比較例１−９に示す成分からなるＴｉＡｌ基合金インゴットを鋳造により製造した。各インゴットを切断して表面加工を施し、直径８０ｍｍ、高さ６０ｍｍの柱状のＴｉＡｌ基合金素材を得た。実施例１と同様の方法で、各ＴｉＡｌ基合金素材の鍛造及び鍛造後の応力除去焼鈍を実施した。
(Comparative example)
TiAl-based alloy ingots made of 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.
（実施例２〜５）
表１の実施例２乃至実施例５に示す成分からなるＴｉＡｌ基合金インゴットを鋳造により製造した。インゴットを切断して表面加工を施し、直径８０ｍｍ、高さ６０ｍｍの柱状ＴｉＡｌ基合金素材を得た。実施例１と同様の方法で、実施例２のＴｉＡｌ基合金素材の鍛造及び鍛造後の応力除去焼鈍を実施した。
(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.
各ＴｉＡｌ基合金の鍛造性評価、クリープ強度試験及び耐酸化性試験を実施した。
鍛造性評価は、鍛造後のインゴットの割れの発生有無を目視で確認した。割れが発生しない場合は鍛造性良好（○）とし、割れが発生する場合は鍛造性不良（×）とした。
クリープ強度試験は、焼鈍後のインゴットから試験片を切り出し、試験温度７６０度、負荷応力３１１ＭＰａで実施した。クリープ破断時間が２５時間以上で高温強度良好（○）とし、２５時間未満で高温強度不足（×）とした。
耐酸化性試験は、焼鈍後のインゴットから一辺が２．８ｍｍの立方体試験片を切り出し、８７０℃にて５０時間加熱し、単位面積当たりの酸化増量で比較した。酸化増量が０．０１ｇ／ｍｍ２以下で耐酸化性良好（○）とし、０．０１ｇ／ｍｍ２を超えた場合に耐酸化性不足（×）とした。
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).
In the creep strength test, a test piece was cut out from the ingot after annealing, and the test temperature was 760 degrees and the load stress was 311 MPa. 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.
In the 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. When the 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).
実施例１−１乃至実施例１−４のＴｉＡｌ基合金は、いずれもラメラ粒が析出した金属組織となり、高い高温強度が得られた。また、Ｎｂを含有しない比較例１−９のＴｉＡｌ基合金と比較して、耐酸化性が大幅に改善された。 The TiAl-based alloys of Examples 1-1 to 1-4 all had a metal structure in which lamellar particles were precipitated, and high high-temperature strength was obtained. Moreover, compared with the TiAl base alloy of Comparative Example 1-9 not containing Nb, the oxidation resistance was greatly improved.
Ａｌが４０原子％（ａｔ％）未満の場合、クリープ破断時間が低下した（比較例１−１、比較例１−３）。Ａｌが４２原子％を超えると、クリープ破断時間が長く高温強度は良好だったが、鍛造割れが発生した（比較例１−５、比較例１−７）。
Ｎｂの含有量ｂが不等式ｂ＜３＋ａを満たす場合、鍛造割れが発生した（比較例１−２、比較例１−６）。Ｎｂ含有量ｂが不等式ｂ＞７＋ａとなる場合は、クリープ破断時間が低下した（比較例１−４、比較例１−８）。
When Al was less than 40 atomic% (at%), the creep rupture time decreased (Comparative Example 1-1, Comparative Example 1-3). When Al exceeded 42 atomic%, the creep rupture time was long and the high-temperature strength was good, but forging cracks occurred (Comparative Example 1-5, Comparative Example 1-7).
When the content b of Nb satisfies the inequality b <3 + a, forging cracks occurred (Comparative Example 1-2, Comparative Example 1-6). When the Nb content b was inequality b> 7 + a, the creep rupture time was reduced (Comparative Example 1-4, Comparative Example 1-8).
実施例２乃至実施例５のＴｉＡｌ基合金はいずれも、鍛造性、高温強度及び耐酸化性は良好だった。 All of the TiAl-based alloys of Examples 2 to 5 had good forgeability, high temperature strength, and oxidation resistance.
実施例１−１、及び、実施例２乃至実施例５のＴｉＡｌ基合金について、変形抵抗測定、引張試験、クリープ強度試験、及び耐酸化性試験の評価結果を表２に示す。変形抵抗測定は、焼鈍後のインゴットから直径７ｍｍ、長さ１２ｍｍの円柱試験片を切り出し、高周波加熱を用いて１２５０℃に保持し、変形速度１００ｍｍ／秒で実施した。引張試験は、焼鈍後のインゴットから切り出した全長６０ｍｍ、評定部直径４ｍｍ、評定部長さ２０ｍｍの試験片に対し、７００℃大気中にて実施した。 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.
Ｖを含有する実施例２及び実施例３は、実施例１−１と比較し引張破断強度が向上した。Ｃｒを含有する実施例４は、変形抵抗が小さくなった。すなわち、高温での変形能が増大した。Ｍｏを含有する実施例５は、クリープ強度が大幅に向上した。 In Examples 2 and 3 containing V, the tensile strength at break was improved as compared with Example 1-1. In Example 4 containing Cr, the deformation resistance was small. That is, the deformability at high temperature increased. In Example 5 containing Mo, the creep strength was greatly improved.
Claims (9)
Ｎｂ：ｂ原子％とを含有し、
残部がＴｉ及び不可避的不純物からなるＴｉＡｌ基合金であって、
前記ａ及びｂが以下の式（１）及び（２）：
０≦ａ≦２ （１）
３＋ａ≦ｂ≦７＋ａ （２）
を満たすＴｉＡｌ基合金。 Al: (40 + a) atomic%,
Nb: b atomic%,
The balance is TiAl based alloy composed of Ti and inevitable impurities,
Said a and b are the following formulas (1) and (2):
0 ≦ a ≦ 2 (1)
3 + a ≦ b ≦ 7 + a (2)
TiAl base alloy satisfying
Ｎｂ：ｂ原子％とを含有し、更に
Ｖ：ｃ原子％、
Ｃｒ：ｄ原子％、及び
Ｍｏ：ｅ原子％
から選択される１種以上の元素を含有し、
残部がＴｉ及び不可避的不純物からなるＴｉＡｌ基合金であって、
前記ａ乃至ｅが以下の式（３）乃至（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）
を満たすＴｉＡｌ基合金。 Al: (40 + a) atomic%,
Nb: b atom%, and V: c atom%,
Cr: d atomic%, and Mo: e atomic%
Containing one or more elements selected from
The balance is TiAl based alloy composed of Ti and inevitable impurities,
The 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)
TiAl base alloy satisfying
Ｎｂ：ｂ原子％とを含有し、
残部がＴｉ及び不可避的不純物からなるＴｉＡｌ基合金素材であって、
前記ａ及びｂが以下の式（１）及び（２）：
０≦ａ≦２ （１）
３＋ａ≦ｂ≦７＋ａ （２）
を満たすＴｉＡｌ基合金素材を、（α＋β）相の平衡温度領域内の保持温度に保持する工程と、
該保持温度に保持したＴｉＡｌ基合金素材を、所定の最終加工温度まで冷却しながら高速塑性加工する工程とを備えるＴｉＡｌ基合金の製造方法。 Al: (40 + a) atomic%,
Nb: b atomic%,
The balance is TiAl based alloy material consisting of Ti and inevitable impurities,
Said a and b are the following formulas (1) and (2):
0 ≦ a ≦ 2 (1)
3 + a ≦ b ≦ 7 + a (2)
Holding the TiAl-based alloy material satisfying the condition at a holding temperature within the equilibrium temperature region of the (α + β) phase;
And a high-speed plastic working process for cooling the TiAl-based alloy material held at the holding temperature to a predetermined final processing temperature.
Ｎｂ：ｂ原子％とを含有し、更に
Ｖ：ｃ原子％、
Ｃｒ：ｄ原子％、及び
Ｍｏ：ｅ原子％
から選択される１種以上の元素を含有し、
残部がＴｉ及び不可避的不純物からなるＴｉＡｌ基合金素材であって、
前記ａ乃至ｅが以下の式（３）乃至（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）
を満たすＴｉＡｌ基合金素材を、（α＋β）相の平衡温度領域内の保持温度に保持する工程と、
該保持温度に保持したＴｉＡｌ基合金素材を、所定の最終加工温度まで冷却しながら高速塑性加工する工程とを備えるＴｉＡｌ基合金の製造方法。 Al: (40 + a) atomic%,
Nb: b atom%, and V: c atom%,
Cr: d atomic%, and Mo: e atomic%
Containing one or more elements selected from
The balance is TiAl based alloy material consisting of Ti and inevitable impurities,
The 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)
Holding the TiAl-based alloy material satisfying the condition at a holding temperature within the equilibrium temperature region of the (α + β) phase;
And a high-speed plastic working process for cooling the TiAl-based alloy material held at the holding temperature to a predetermined final processing temperature.
Priority Applications (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2008062690A JP2009215631A (en) | 2008-03-12 | 2008-03-12 | Titanium-aluminum-based alloy and production method therefor, and moving blade using the same |
| US12/863,529 US20100316525A1 (en) | 2008-03-12 | 2009-01-30 | TiAl-BASED ALLOY, PROCESS FOR PRODUCING SAME, AND ROTOR BLADE USING SAME |
| EP09720943A EP2251445A4 (en) | 2008-03-12 | 2009-01-30 | Tial-based alloy, process for production of the same, and rotor blade comprising the same |
| PCT/JP2009/051539 WO2009113335A1 (en) | 2008-03-12 | 2009-01-30 | Tial-based alloy, process for production of the same, and rotor blade comprising the same |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2008062690A JP2009215631A (en) | 2008-03-12 | 2008-03-12 | Titanium-aluminum-based alloy and production method therefor, and moving blade using the same |
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| Publication Number | Publication Date |
|---|---|
| JP2009215631A true JP2009215631A (en) | 2009-09-24 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2008062690A Withdrawn JP2009215631A (en) | 2008-03-12 | 2008-03-12 | Titanium-aluminum-based alloy and production method therefor, and moving blade using the same |
Country Status (4)
| Country | Link |
|---|---|
| US (1) | US20100316525A1 (en) |
| EP (1) | EP2251445A4 (en) |
| JP (1) | JP2009215631A (en) |
| WO (1) | WO2009113335A1 (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2014203714A1 (en) * | 2013-06-19 | 2014-12-24 | 独立行政法人物質・材料研究機構 | Hot-forged ti-al-based alloy and method for producing same |
| JP2015004092A (en) * | 2013-06-19 | 2015-01-08 | 独立行政法人物質・材料研究機構 | HOT FORGING TYPE TiAl BASED ALLOY |
| JP2015151612A (en) * | 2014-02-19 | 2015-08-24 | 国立研究開発法人物質・材料研究機構 | HOT FORGING TYPE TiAl-BASED ALLOY AND PRODUCTION METHOD THEREOF |
| JP2016166418A (en) * | 2015-03-09 | 2016-09-15 | ライストリッツ タービンテクニック ゲーエムベーハー | METHOD FOR PRODUCTION OF HIGHLY STRESSABLE COMPONENT FROM α+γ- TITANIUM ALUMINIDE ALLOY FOR RECIPROCATING-PISTON ENGINE AND GAS TURBINE, ESPECIALLY AIRCRAFT ENGINE |
| JPWO2018043187A1 (en) * | 2016-09-02 | 2019-04-18 | 株式会社Ihi | TiAl alloy and method of manufacturing the same |
| WO2022219991A1 (en) | 2021-04-16 | 2022-10-20 | 株式会社神戸製鋼所 | Tial alloy for forging, tial alloy material, and method for producing tial alloy material |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103757578B (en) * | 2014-01-24 | 2016-03-30 | 中国科学院金属研究所 | The tiny complete lamellar structure preparation method of a kind of gamma-TiAl alloy |
| EP2905350A1 (en) | 2014-02-06 | 2015-08-12 | MTU Aero Engines GmbH | High temperature TiAl alloy |
| CN103820672B (en) * | 2014-03-12 | 2017-05-03 | 北京工业大学 | Cr and Mn alloying beta phase solidifying high Nb-TiAl alloy and preparation method thereof |
| CN105397000A (en) * | 2015-12-02 | 2016-03-16 | 贵州安大航空锻造有限责任公司 | Rolling method of titanium alloy plate-shaped forgings |
| CN114603141B (en) * | 2022-03-09 | 2022-12-27 | 西北工业大学 | TiAl alloy blade die forging forming method |
Family Cites Families (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5370839A (en) * | 1991-07-05 | 1994-12-06 | Nippon Steel Corporation | Tial-based intermetallic compound alloys having superplasticity |
| JPH05320791A (en) * | 1992-05-15 | 1993-12-03 | Mitsubishi Heavy Ind Ltd | Ti-al intermetallic compound alloy |
| JPH0633172A (en) * | 1992-07-17 | 1994-02-08 | Sumitomo Light Metal Ind Ltd | Ti-al intermetallic compound |
| US5451366A (en) * | 1992-07-17 | 1995-09-19 | Sumitomo Light Metal Industries, Ltd. | Product of a halogen containing Ti-Al system intermetallic compound having a superior oxidation and wear resistance |
| JPH06116691A (en) * | 1992-10-05 | 1994-04-26 | Mitsubishi Materials Corp | Method for heat-treating ti-al intermetallic compound series ti alloy |
| DE19581384C2 (en) * | 1994-10-25 | 1999-03-11 | Mitsubishi Heavy Ind Ltd | Titanium-aluminum alloy based on an intermetallic compound |
| JP4287991B2 (en) * | 2000-02-23 | 2009-07-01 | 三菱重工業株式会社 | TiAl-based alloy, method for producing the same, and moving blade using the same |
| DE102007060587B4 (en) * | 2007-12-13 | 2013-01-31 | Helmholtz-Zentrum Geesthacht Zentrum für Material- und Küstenforschung GmbH | titanium aluminide |
-
2008
- 2008-03-12 JP JP2008062690A patent/JP2009215631A/en not_active Withdrawn
-
2009
- 2009-01-30 WO PCT/JP2009/051539 patent/WO2009113335A1/en active Application Filing
- 2009-01-30 US US12/863,529 patent/US20100316525A1/en not_active Abandoned
- 2009-01-30 EP EP09720943A patent/EP2251445A4/en not_active Withdrawn
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2014203714A1 (en) * | 2013-06-19 | 2014-12-24 | 独立行政法人物質・材料研究機構 | Hot-forged ti-al-based alloy and method for producing same |
| JP2015004092A (en) * | 2013-06-19 | 2015-01-08 | 独立行政法人物質・材料研究機構 | HOT FORGING TYPE TiAl BASED ALLOY |
| US10208360B2 (en) | 2013-06-19 | 2019-02-19 | National Institute For Materials Science | Hot-forged TiAl-based alloy and method for producing the same |
| JP2015151612A (en) * | 2014-02-19 | 2015-08-24 | 国立研究開発法人物質・材料研究機構 | HOT FORGING TYPE TiAl-BASED ALLOY AND PRODUCTION METHOD THEREOF |
| JP2016166418A (en) * | 2015-03-09 | 2016-09-15 | ライストリッツ タービンテクニック ゲーエムベーハー | METHOD FOR PRODUCTION OF HIGHLY STRESSABLE COMPONENT FROM α+γ- TITANIUM ALUMINIDE ALLOY FOR RECIPROCATING-PISTON ENGINE AND GAS TURBINE, ESPECIALLY AIRCRAFT ENGINE |
| JPWO2018043187A1 (en) * | 2016-09-02 | 2019-04-18 | 株式会社Ihi | TiAl alloy and method of manufacturing the same |
| US11078563B2 (en) | 2016-09-02 | 2021-08-03 | Ihi Corporation | TiAl alloy and method of manufacturing the same |
| WO2022219991A1 (en) | 2021-04-16 | 2022-10-20 | 株式会社神戸製鋼所 | Tial alloy for forging, tial alloy material, and method for producing tial alloy material |
Also Published As
| Publication number | Publication date |
|---|---|
| US20100316525A1 (en) | 2010-12-16 |
| EP2251445A4 (en) | 2011-12-14 |
| EP2251445A1 (en) | 2010-11-17 |
| WO2009113335A1 (en) | 2009-09-17 |
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