JPH04235263A - Manufacture of ti-al intermetallic compound-series ti alloy excellent in strength and ductility - Google Patents
Manufacture of ti-al intermetallic compound-series ti alloy excellent in strength and ductilityInfo
- Publication number
- JPH04235263A JPH04235263A JP6080091A JP6080091A JPH04235263A JP H04235263 A JPH04235263 A JP H04235263A JP 6080091 A JP6080091 A JP 6080091A JP 6080091 A JP6080091 A JP 6080091A JP H04235263 A JPH04235263 A JP H04235263A
- Authority
- JP
- Japan
- Prior art keywords
- phase
- temperature
- intermetallic compound
- alloy
- ductility
- Prior art date
- Legal status (The legal status 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 status listed.)
- Granted
Links
- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 42
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 10
- 238000010438 heat treatment Methods 0.000 claims abstract description 23
- 238000001816 cooling Methods 0.000 claims abstract description 20
- 230000032683 aging Effects 0.000 claims abstract description 6
- 229910010038 TiAl Inorganic materials 0.000 claims description 27
- 229910000765 intermetallic Inorganic materials 0.000 claims description 26
- 125000004122 cyclic group Chemical group 0.000 claims description 5
- 238000000034 method Methods 0.000 abstract description 12
- 239000012535 impurity Substances 0.000 abstract description 7
- 229910004349 Ti-Al Inorganic materials 0.000 abstract 3
- 229910004692 Ti—Al Inorganic materials 0.000 abstract 3
- 229910021362 Ti-Al intermetallic compound Inorganic materials 0.000 abstract 1
- 239000012071 phase Substances 0.000 description 59
- 239000000243 solution Substances 0.000 description 13
- 239000000956 alloy Substances 0.000 description 11
- 239000013078 crystal Substances 0.000 description 6
- 238000007796 conventional method Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 229910021330 Ti3Al Inorganic materials 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 239000012300 argon atmosphere Substances 0.000 description 1
- 239000000919 ceramic Substances 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Abstract
Description
【0001】0001
【産業上の利用分野】この発明は、TiAl金属間化合
物系Ti合金の強度および延性を向上させる方法に関す
るものである。BACKGROUND OF THE INVENTION 1. Field of the Invention This invention relates to a method for improving the strength and ductility of a TiAl intermetallic compound-based Ti alloy.
【0002】0002
【従来の技術】一般に、軽量にして耐熱性が要求される
タービンブレードや自動車のターボチャージャローター
などの部材の製造にTiAl金属間化合物系Ti合金の
適用が提案されており、その中でもAl:48原子%を
含有し、残りがTiおよび不可避不純物からなるTi合
金を真空中、温度:1300℃に三日間保持後放冷の条
件で焼鈍処理した状態での適用が考えられている。[Prior Art] In general, it has been proposed to use TiAl intermetallic compound-based Ti alloys in the production of parts such as turbine blades and automobile turbocharger rotors that require light weight and heat resistance. Among them, Al: 48 It is considered that a Ti alloy containing atomic percent Ti and the remainder consisting of Ti and unavoidable impurities is annealed in a vacuum at a temperature of 1300° C. for three days and then allowed to cool.
【0003】さらに、「日本金属学会講演概要、236
〜237ページ、平成元年9月13日発行」には、Al
:40原子%を含有し、残りがTiおよび不可避不純物
からなるTi合金並びにAl:40原子%を含有し、残
りがTiおよび不可避不純物からなるTi合金の試料を
均質化処理後水冷して得られた溶体化処理材を時効処理
することによりα相(Ti固溶体相およびTi3 Al
固溶体相の総称)およびγ相(TiAl金属間化合物相
)からなるラメラー組織が得られることが記載されてい
る。[0003] Furthermore, “Japan Institute of Metals Lecture Summary, 236
~237 pages, published September 13, 1989,” includes Al
: 40 atomic % with the remainder consisting of Ti and unavoidable impurities, and a Ti alloy sample containing 40 atomic % Al with the remainder consisting of Ti and unavoidable impurities after homogenization treatment and water cooling. By aging the solution-treated material, α phase (Ti solid solution phase and Ti3Al
It is described that a lamellar structure consisting of a solid solution phase) and a γ phase (TiAl intermetallic compound phase) can be obtained.
【0004】0004
【発明が解決しようとする課題】しかし、上記公知の熱
処理を施してもTiAl金属間化合物系Ti合金の強度
および延性を十分に向上させることができなかった。そ
の原因として、上記熱処理を施したTiAl金属間化合
物系Ti合金の平均結晶粒径は260μm以上と大きく
かつα相およびγ相からなるラメラー組織の縞状γ相の
厚さが厚いことによるためであることが分かったのであ
る。[Problems to be Solved by the Invention] However, even if the above-mentioned known heat treatment was performed, the strength and ductility of Ti alloys based on TiAl intermetallic compounds could not be sufficiently improved. This is because the average grain size of the TiAl intermetallic compound Ti alloy subjected to the above heat treatment is as large as 260 μm or more, and the thickness of the striped γ phase in the lamellar structure consisting of α phase and γ phase is thick. It turns out that there is something.
【0005】[0005]
【課題を解決するための手段】そこで、本発明者らは、
かかる観点から、TiAl金属間化合物系Ti合金の平
均結晶粒径を小さくし、かつ上記ラメラー組織の縞状γ
相の厚さを薄くすべく研究を行った結果、Al:38〜
45原子%を含有し、残りがTiおよび不可避不純物か
らなるTiAl金属間化合物系Ti合金を、所定の温度
に加熱保持して溶体化処理を施し、続いて、α相単相温
度領域内の所定の温度に保持する熱処理(以下、α単相
化処理という)を施したのち、β相単相温度領域内の所
定の温度に昇温保持する熱処理(以下、β単相化処理と
いう)を繰り返し行うサイクル熱処理を施すと、組織の
結晶粒径が微細化してTiAl金属間化合物系Ti合金
の強度および延性が向上し、さらに、この微細化した組
織を有するTiAl金属間化合物系Ti合金に1150
〜1300℃内の所定の温度:Tに所定時間保持後冷却
のα溶体化処理を施し、ついで650℃〜(T−100
)℃の範囲内の所定の温度に所定時間保持後急冷の時効
処理を施すと、ラメラー組織の縞状γ相の厚さが薄くな
り、TiAl金属間化合物系Ti合金の強度および延性
を一層向上させることができるという知見を得たのであ
る。[Means for solving the problem] Therefore, the present inventors
From this point of view, the average grain size of the TiAl intermetallic compound Ti alloy is reduced, and the striped γ of the lamellar structure is reduced.
As a result of research to reduce the thickness of the phase, Al: 38 ~
A TiAl intermetallic compound-based Ti alloy containing 45 at. After performing heat treatment to maintain the temperature at a temperature of When the cyclic heat treatment is performed, the grain size of the structure becomes finer and the strength and ductility of the TiAl intermetallic compound Ti alloy is improved.
Predetermined temperature within ~1300℃: T is subjected to α solution treatment by cooling after being held for a predetermined time, and then heated to 650℃ ~ (T-100
) After holding at a predetermined temperature for a predetermined period of time within the range of 100 to 1000 °C, the material is rapidly cooled to reduce the thickness of the striped γ phase in the lamellar structure, further improving the strength and ductility of the TiAl intermetallic compound-based Ti alloy. We obtained the knowledge that it is possible to do so.
【0006】この発明は、かかる知見に基づいて成され
たものであって、(1)Al:38〜45原子%を含有
し、残りがTiおよび不可避不純物からなるTiAl金
属間化合物系Ti合金を、所定の温度に加熱保持して溶
体化処理を施し、続いてα単相化処理およびβ単相化処
理の繰り返し行うサイクル熱処理を施す強度および延性
に優れたTiAl金属間化合物系Ti合金の製造法、並
びに(2)Al:38〜45原子%を含有し、残りがT
iおよび不可避不純物からなるTiAl金属間化合物系
Ti合金を、所定の温度に加熱保持して溶体化処理を施
し、続いてα単相化処理およびβ単相化処理の繰り返し
行うサイクル熱処理を施し、さらに1150〜1300
℃内の所定の温度:Tに所定時間保持後冷却のα溶体化
処理を施し、ついで650℃〜(T−100)℃の範囲
内の所定の温度に所定時間保持後急冷の時効処理を施す
強度および延性に優れたTiAl金属間化合物系Ti合
金の製造法、に特徴を有するものである。[0006] The present invention was made based on this knowledge, and includes (1) a TiAl intermetallic compound-based Ti alloy containing 38 to 45 atomic % Al, with the remainder consisting of Ti and unavoidable impurities; Production of a TiAl intermetallic compound-based Ti alloy with excellent strength and ductility, by heating and holding at a predetermined temperature to perform solution treatment, followed by cycle heat treatment in which α single-phase treatment and β single-phase treatment are repeated. and (2) Al: 38 to 45 at%, the remainder being T.
A TiAl intermetallic compound-based Ti alloy consisting of i and unavoidable impurities is subjected to solution treatment by heating and holding at a predetermined temperature, followed by cyclic heat treatment in which α single-phase treatment and β single-phase treatment are repeated, Further 1150-1300
A predetermined temperature within °C: α solution treatment is performed by holding at T for a predetermined time and then cooling, and then an aging treatment is performed by holding at a predetermined temperature within the range of 650 °C to (T-100) °C for a predetermined time and rapid cooling. This method is characterized by a method for producing a TiAl intermetallic compound-based Ti alloy that has excellent strength and ductility.
【0007】この発明では、TiAl金属間化合物系T
i合金を、まず所定の温度に加熱保持して溶体化処理を
十分に行うが、この溶体化処理は、α相単相温度領域内
の所定の温度に保持してα溶体化処理を施してもよいが
、β相単相温度領域内の所定の温度に保持してβ溶体化
処理を施す方が好ましく、上記β相単相温度領域内の内
でも1300℃超〜1500℃内の所定の温度であるこ
とが一層好ましい。1300℃以下で溶体化処理しても
α相が残り、β溶体化処理したことにはならず、一方、
1500℃を越えた高温では、液相が現れて不均一な組
織となるので好ましくないことによるものである。In this invention, TiAl intermetallic compound system T
The i-alloy is first heated and held at a predetermined temperature to undergo sufficient solution treatment. However, it is preferable to perform the β solution treatment while maintaining the temperature at a predetermined temperature within the β-phase single-phase temperature range. More preferably, it is temperature. Even if solution treatment is performed at 1300°C or lower, the α phase remains and β solution treatment is not performed.On the other hand,
This is because a high temperature exceeding 1500° C. is undesirable because a liquid phase appears and a non-uniform structure is formed.
【0008】かかる溶体化処理を施したのち、この温度
からα相単相温度領域に降温し、α単相化処理して最密
六方晶であるα相とし、再びβ相単相温度領域に昇温し
、β単相化処理して体心立方晶であるβ相とし、α相単
相温度領域→β相単相温度領域→α相単相温度領域→β
相単相温度領域となるように加熱保持および冷却保持の
サイクル熱処理を施すことにより、TiAl金属間化合
物系Ti合金の結晶構造をα相(最密六方晶)とβ相(
体心立方晶)との間を往復せしめ、それにより結晶粒を
微細化させるのである。After the solution treatment, the temperature is lowered from this temperature to the α-phase single-phase temperature region, α-single-phase treatment is performed to form the α-phase, which is a close-packed hexagonal crystal, and then the temperature is reduced to the β-phase single-phase temperature region again. The temperature is raised, β-single phase processing is performed to obtain the β-phase which is a body-centered cubic crystal, and the α-phase single-phase temperature range → β-phase single-phase temperature range → α-phase single-phase temperature range → β
By carrying out cyclic heat treatment of heating and cooling to maintain a single-phase temperature range, the crystal structure of the TiAl intermetallic compound-based Ti alloy is divided into α phase (close-packed hexagonal crystal) and β phase (
body-centered cubic crystal), thereby making the crystal grains finer.
【0009】このようにして微細化した結晶粒を有する
組織を持ったTiAl金属間化合物系Ti合金を、さら
に1150〜1300℃内の所定の温度:Tに所定時間
保持後50℃/min 以上の冷却速度で冷却のα溶体
化処理を施し、ついで650℃〜(T−100)℃の範
囲内の所定の温度に所定時間保持後50℃/min 以
上の冷却速度で急冷の時効処理を施すと、ラメラー組織
の縞状γ相の厚さが一層薄くなり、TiAl金属間化合
物系Ti合金の強度および延性を一層向上させることが
できる。[0009] The TiAl intermetallic compound-based Ti alloy having a structure having grains refined in this manner is further held at a predetermined temperature: T within the range of 1150 to 1300°C for a predetermined time, and then heated at a rate of 50°C/min or more. If α solution treatment is performed by cooling at a cooling rate, then after holding at a predetermined temperature within the range of 650°C to (T-100)°C for a predetermined time, rapid cooling aging treatment is performed at a cooling rate of 50°C/min or more. , the thickness of the striped γ phase of the lamellar structure becomes even thinner, and the strength and ductility of the TiAl intermetallic compound-based Ti alloy can be further improved.
【0010】TiAl金属間化合物系Ti合金のAl含
有量は、38原子%未満ではラメラー組織を確保するこ
とができず、一方、45原子%を越えるとβ相単相領域
が存在しなくなるのでこの発明の方法を実施することが
できない。したがって、この発明の方法で用いるTiA
l金属間化合物系Ti合金のAl含有量は、38〜45
原子%に定めた。このTiAl金属間化合物系Ti合金
のサイクル熱処理は、α相単相温度領域とβ相単相温度
領域の間を往復するように加熱冷却を繰り返すことによ
り行われるが、α相単相温度領域→β相単相温度領域へ
の加熱速度およびβ相単相温度領域→α相単相温度領域
への冷却速度は、大きい方が好ましく、いずれも10℃
/sec 以上であることが一層好ましい。[0010] If the Al content of the Ti alloy based on TiAl intermetallic compound is less than 38 atomic %, it is not possible to secure a lamellar structure, whereas if it exceeds 45 atomic %, the β phase single phase region will not exist. Unable to carry out the method of the invention. Therefore, the TiA used in the method of this invention
The Al content of the intermetallic Ti alloy is 38 to 45
Defined as atomic percent. This cyclic heat treatment of the TiAl intermetallic compound-based Ti alloy is performed by repeating heating and cooling so as to go back and forth between the α-phase single-phase temperature region and the β-phase single-phase temperature region. The heating rate to the β-phase single-phase temperature region and the cooling rate from the β-phase single-phase temperature region to the α-phase single-phase temperature region are preferably larger, and both are 10°C.
It is more preferable that it is equal to or more than /sec.
【0011】さらに上記結晶粒を微細化したTiAl金
属間化合物系Ti合金のラメラー組織におけるγ相の薄
状化は、α相単相温度領域内の1150〜1300℃内
の所定の温度:Tに保持してα溶体化処理を施したのち
、50℃/min 以上の冷却速度で650℃〜(T−
100)℃の時効処理温度まで冷却し、この時効処理温
度に冷却した後、50℃/min 以上の冷却速度で冷
却するとラメラー組織におけるγ相の厚さを1.2μm
以下に薄くすることができ、強度および伸びが大幅に向
上する。Furthermore, the thinning of the γ phase in the lamellar structure of the TiAl intermetallic compound Ti alloy with finer grains occurs at a predetermined temperature: T within the α phase single phase temperature range of 1150 to 1300°C. After being held and subjected to α solution treatment, it was cooled at a cooling rate of 50°C/min or more to 650°C (T-
After cooling to the aging treatment temperature of 100)℃, cooling at a cooling rate of 50℃/min or more reduces the thickness of the γ phase in the lamellar structure to 1.2μm.
It can be thinned to less than
【0012】0012
【実施例】この発明を実施例に基づいて具体的に説明す
る。EXAMPLES The present invention will be specifically explained based on examples.
【0013】通常のアーク炉を用い、アルゴン雰囲気中
でそれぞれ表1に示されるような成分組成を有する溶湯
を調製し、セラミック鋳型を用いて遠心鋳造し、たて:
12mm、横:12mm、長さ:70mmの寸法を有す
るTiAl金属間化合物系Ti合金材(以下、Ti合金
材という)を作製した。[0013] Molten metals having the compositions shown in Table 1 were prepared in an argon atmosphere using an ordinary arc furnace, and centrifugally cast using a ceramic mold.
A TiAl intermetallic compound-based Ti alloy material (hereinafter referred to as Ti alloy material) having dimensions of 12 mm, width: 12 mm, and length: 70 mm was produced.
【0014】[0014]
【表1】[Table 1]
【0015】このTi合金材を表1に示される条件で溶
体化処理を施したのち、表1に示されるα相単相温度領
域内の温度に表1に示される時間保持してα単相化処理
し、ついで表1に示されるβ相単相温度領域内の温度に
表1に示される時間保持してβ単相化処理し、このα単
相化処理→β単相化処理を1サイクルとして表1に示さ
れるサイクル数だけ繰り返し、本発明法1〜4を実施し
、得られたTi合金材の組織および機械的特性を測定し
てその結果を表2に示した。After subjecting this Ti alloy material to solution treatment under the conditions shown in Table 1, it was maintained at a temperature within the α-phase single-phase temperature range shown in Table 1 for the time shown in Table 1 to form an α-single phase. Then, the temperature is held within the β-phase single-phase temperature range shown in Table 1 for the time shown in Table 1 to perform β-single-phase processing, and this α-single-phase processing → β-single-phase processing is Methods 1 to 4 of the present invention were repeated for the number of cycles shown in Table 1, and the structure and mechanical properties of the obtained Ti alloy material were measured, and the results are shown in Table 2.
【0016】[0016]
【表2】[Table 2]
【0017】さらに、上記本発明法1〜4で得られたT
i合金材をさらに表3に示される条件でラメラー層微細
化処理を施して本発明法5〜8を実施し、得られたTi
合金材の組織および機械的特性を測定してその結果を表
4に示した。Furthermore, T obtained by the above-mentioned methods 1 to 4 of the present invention
The Ti alloy material was further subjected to lamellar layer refinement treatment under the conditions shown in Table 3, and the methods 5 to 8 of the present invention were carried out.
The structure and mechanical properties of the alloy material were measured and the results are shown in Table 4.
【0018】一方、比較のために、Al:48原子%、
残りTiおよび不可避不純物からなるTi合金を、真空
中、温度:1300℃、3日間保持後空冷の焼鈍処理を
施して従来法を実施し、得られたTi合金材の組織およ
び機械的特性を測定してその結果を表4に示した。On the other hand, for comparison, Al: 48 atomic %,
A Ti alloy consisting of remaining Ti and unavoidable impurities was held in a vacuum at a temperature of 1300°C for 3 days, and then subjected to air-cooling annealing treatment using the conventional method, and the structure and mechanical properties of the obtained Ti alloy material were measured. The results are shown in Table 4.
【0019】[0019]
【表3】[Table 3]
【0020】[0020]
【表4】[Table 4]
【0021】[0021]
【発明の効果】表1および表2の結果から、本発明法1
〜4で得られたTi合金材は、いずれも従来法で得られ
た表4のTi合金材よりも平均粒径が小さく、引張り強
さおよび伸びが優れており、また、表3および表4の結
果から、本発明法5〜8に見られるように、本発明法1
〜4で得られたTi合金材にさらにラメラー層微細化処
理を施すことにより引張り強さおよび伸びが一層向上す
ることがわかる。[Effect of the invention] From the results in Tables 1 and 2, it is clear that the method 1 of the present invention
All of the Ti alloy materials obtained in Tables 3 and 4 have smaller average particle diameters and superior tensile strength and elongation than the Ti alloy materials in Table 4 obtained by conventional methods. From the results, as seen in methods 5 to 8 of the invention, method 1 of the invention
It can be seen that the tensile strength and elongation are further improved by further subjecting the Ti alloy material obtained in 4 to 4 to a lamellar layer refinement treatment.
【0022】したがって、この発明の製造法を用いるこ
とにより、強度および延性の優れたTiAl金属間化合
物系Ti合金を提供することができ、産業上優れた効果
を奏するものである。[0022] Therefore, by using the manufacturing method of the present invention, a TiAl intermetallic compound-based Ti alloy having excellent strength and ductility can be provided, resulting in excellent industrial effects.
Claims (3)
りがTiおよび不可避不純物からなるTiAl金属間化
合物系Ti合金を所定の温度に加熱保持して溶体化処理
し、続いて、α相単相温度領域内の所定の温度に保持す
る熱処理およびβ相単相温度領域内の所定の温度に昇温
保持する熱処理を繰り返し行うサイクル熱処理を施すこ
とを特徴とする強度および延性に優れたTiAl金属間
化合物系Ti合金の製造法。[Claim 1] A TiAl intermetallic compound-based Ti alloy containing 38 to 45 at. TiAl with excellent strength and ductility, which is characterized by subjecting it to cyclic heat treatment in which heat treatment is repeated to maintain the temperature at a predetermined temperature within the single-phase temperature range, and heat treatment to raise and maintain the temperature at a predetermined temperature within the β-phase single-phase temperature range. A method for producing an intermetallic Ti alloy.
りがTiおよび不可避不純物からなるTiAl金属間化
合物系Ti合金を所定の温度に加熱保持して溶体化処理
を施し、続いて、α相単相温度領域内の所定の温度に保
持する熱処理およびβ相単相温度領域内の所定の温度に
昇温保持する熱処理を繰り返し行うサイクル熱処理を施
し、さらに1150〜1300℃内の所定の温度:Tに
所定時間保持後冷却のα溶体化処理を施し、ついで65
0℃〜(T−100)℃の範囲内の所定の温度に所定時
間保持後急冷の時効処理を施すことを特徴とする強度お
よび延性に優れたTiAl金属間化合物系Ti合金の製
造法。2. A TiAl intermetallic compound-based Ti alloy containing 38 to 45 at. A cycle heat treatment is performed in which heat treatment is repeated to maintain the temperature at a predetermined temperature within the single-phase temperature range, and heat treatment to raise and maintain the temperature at a predetermined temperature within the β-phase single-phase temperature range, and further to a predetermined temperature within the range of 1150 to 1300°C. : T is subjected to α solution treatment by cooling after holding for a predetermined time, and then 65
A method for producing a TiAl intermetallic compound-based Ti alloy with excellent strength and ductility, which comprises holding at a predetermined temperature in the range of 0° C. to (T-100)° C. for a predetermined time and then subjecting it to an aging treatment of rapid cooling.
1300℃超〜1500℃内の所定の温度であることを
特徴とする請求項1または2記載の強度および延性に優
れたTiAl金属間化合物系Ti合金の製造法。3. The solution treatment temperature preferably includes:
3. The method for producing a TiAl intermetallic compound-based Ti alloy with excellent strength and ductility according to claim 1 or 2, characterized in that the temperature is a predetermined temperature of over 1300°C to 1500°C.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP6080091A JP2817428B2 (en) | 1991-01-08 | 1991-01-08 | Method for producing TiAl intermetallic compound Ti alloy excellent in strength and ductility |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP6080091A JP2817428B2 (en) | 1991-01-08 | 1991-01-08 | Method for producing TiAl intermetallic compound Ti alloy excellent in strength and ductility |
Publications (2)
Publication Number | Publication Date |
---|---|
JPH04235263A true JPH04235263A (en) | 1992-08-24 |
JP2817428B2 JP2817428B2 (en) | 1998-10-30 |
Family
ID=13152763
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP6080091A Expired - Lifetime JP2817428B2 (en) | 1991-01-08 | 1991-01-08 | Method for producing TiAl intermetallic compound Ti alloy excellent in strength and ductility |
Country Status (1)
Country | Link |
---|---|
JP (1) | JP2817428B2 (en) |
-
1991
- 1991-01-08 JP JP6080091A patent/JP2817428B2/en not_active Expired - Lifetime
Also Published As
Publication number | Publication date |
---|---|
JP2817428B2 (en) | 1998-10-30 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
US5458705A (en) | Thermal cycling titanium matrix composites | |
JP3959766B2 (en) | Treatment method of Ti alloy with excellent heat resistance | |
JPH0686638B2 (en) | High-strength Ti alloy material with excellent workability and method for producing the same | |
WO2018043187A1 (en) | Tial alloy and method for producing same | |
CN108977693B (en) | A kind of recrystallization high-strength titanium alloy and preparation method thereof | |
RU2525003C1 (en) | Titanium aluminide alloy and method for processing blanks thereof | |
CN113564717A (en) | Ni3Al-based single crystal high-temperature alloy and preparation method thereof | |
JPH04235262A (en) | Manufacture of ti-al intermetallic compound-series ti alloy excellent in strength and ductility | |
JPH06116691A (en) | Method for heat-treating ti-al intermetallic compound series ti alloy | |
CN112359246B (en) | Cu-Ti-P-Ni-Er copper alloy material and preparation method thereof | |
JPH04235263A (en) | Manufacture of ti-al intermetallic compound-series ti alloy excellent in strength and ductility | |
CN109385561B (en) | Production process of Al-Mg-Si-Zr aluminum alloy tubular bus | |
JP2687641B2 (en) | High toughness TiA (1) Method for producing intermetallic compound-based Ti alloy material | |
CN111850359A (en) | Aluminum alloy applied to electric vehicle charging and preparation method thereof | |
JPH05132745A (en) | Production of aluminum alloy excellent in formability | |
JPH03193851A (en) | Production of tial-base alloy having extremely superfine structure | |
JP7233658B2 (en) | Titanium aluminide alloy material for hot forging and method for forging titanium aluminide alloy material | |
JP2729011B2 (en) | TiAl-based intermetallic compound alloy having high strength and method for producing the same | |
JP3334246B2 (en) | Method for producing TiAl-based thermostat forged alloy | |
CN112322936B (en) | Anti-oxidation high-temperature titanium alloy and preparation method thereof | |
JPH03130351A (en) | Production of titanium and titanium alloy having fine and equiaxial structure | |
JP3065782B2 (en) | Hydrogen treatment method for titanium alloy | |
JPH03249147A (en) | Intermetallic compound ti-al base alloy excellent in oxidation resistance and its manufacture | |
CN115927935A (en) | Al-Cu-Mg-Ag-Si-Sc high-heat-resistance aluminum alloy and preparation method thereof | |
JP3039106B2 (en) | Manufacturing method of heat-resistant titanium alloy cast member with excellent room temperature ductility |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 Effective date: 19980721 |