JPH02274829A - Intermetallic compound ti3al-base lightweight heat-resistance alloy - Google Patents
Intermetallic compound ti3al-base lightweight heat-resistance alloyInfo
- Publication number
- JPH02274829A JPH02274829A JP9614689A JP9614689A JPH02274829A JP H02274829 A JPH02274829 A JP H02274829A JP 9614689 A JP9614689 A JP 9614689A JP 9614689 A JP9614689 A JP 9614689A JP H02274829 A JPH02274829 A JP H02274829A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- weight
- ti3al
- intermetallic compound
- phase
- 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.)
- Pending
Links
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 34
- 239000000956 alloy Substances 0.000 title claims abstract description 34
- 229910000765 intermetallic Inorganic materials 0.000 title claims abstract description 11
- 230000000087 stabilizing effect Effects 0.000 claims abstract description 10
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 6
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 5
- 229910052796 boron Inorganic materials 0.000 claims abstract description 4
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 3
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 3
- 239000010703 silicon Substances 0.000 claims description 3
- 229910021330 Ti3Al Inorganic materials 0.000 abstract description 5
- 229910052782 aluminium Inorganic materials 0.000 abstract description 3
- 238000002844 melting Methods 0.000 abstract description 3
- 230000008018 melting Effects 0.000 abstract description 3
- 229910052719 titanium Inorganic materials 0.000 abstract description 3
- 239000002994 raw material Substances 0.000 abstract description 2
- 230000002542 deteriorative effect Effects 0.000 abstract 2
- QYEXBYZXHDUPRC-UHFFFAOYSA-N B#[Ti]#B Chemical compound B#[Ti]#B QYEXBYZXHDUPRC-UHFFFAOYSA-N 0.000 abstract 1
- 229910033181 TiB2 Inorganic materials 0.000 abstract 1
- 230000007547 defect Effects 0.000 abstract 1
- 239000003381 stabilizer Substances 0.000 abstract 1
- 239000010955 niobium Substances 0.000 description 9
- 239000000463 material Substances 0.000 description 7
- 238000000034 method Methods 0.000 description 7
- 230000007423 decrease Effects 0.000 description 5
- 230000000694 effects Effects 0.000 description 4
- 239000010936 titanium Substances 0.000 description 4
- 229910052721 tungsten Inorganic materials 0.000 description 4
- 229910052758 niobium Inorganic materials 0.000 description 3
- 229910052715 tantalum Inorganic materials 0.000 description 3
- 238000009864 tensile test Methods 0.000 description 3
- 229910000831 Steel Inorganic materials 0.000 description 2
- 229910001069 Ti alloy Inorganic materials 0.000 description 2
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 229910052750 molybdenum Inorganic materials 0.000 description 2
- 239000010959 steel Substances 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 229910002056 binary alloy Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 238000010248 power generation Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
Landscapes
- Manufacture And Refinement Of Metals (AREA)
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明は、軽くて高温強度が高く、航空機用エンジン部
材や発電用ガスタービン部材等への利用が期待されてい
る金属間化合物Ｔｉ３Ａｌ基合金であって、特にその軽
量および高強度という特徴が損なわれずに常温延性が改
善されたＴｉＪＱ基合金に関するものである。Detailed Description of the Invention (Field of Industrial Application) The present invention relates to an intermetallic compound Ti3Al-based alloy that is lightweight and has high high-temperature strength and is expected to be used in aircraft engine parts, power generation gas turbine parts, etc. In particular, the present invention relates to a TiJQ-based alloy with improved cold ductility without sacrificing its light weight and high strength characteristics.
（従来の技術）
Ｔｉ−Ａｌｌ！２元系において、ＴＩ、＾ｆ、ＴｉＡＮ
およびＴｌＡｊ！２の３種類の金属間化合物が存在する
ことが知られている。このうちＴ１側に近いＴｉＪｌは
α２相とも呼ばれ、ＤＯｌ、型の結晶構造を有している
。(Prior art) Ti-All! In a binary system, TI, ^f, TiAN
and TlAj! It is known that three types of intermetallic compounds exist. Among these, TiJl near the T1 side is also called α2 phase and has a DOl type crystal structure.
Ｔｉ５Ａｆは化学量論組成（Ｔｉ−１５，８重量％Ａｆ
ｆｉ）からＡｆｆｉ側に広い固溶範囲を形成し、高温で
はβ相に変態する。Ti5Af has a stoichiometric composition (Ti-15, 8% by weight Af
fi) forms a wide solid solution range from the Affi side, and transforms into the β phase at high temperatures.
Ｔｌ５Ａｊ！はチタンよりも軽く、強度が高く、その強
度は７５０℃程度まで大きく低下す′ることかない。Tl5Aj! It is lighter than titanium and has higher strength, and its strength does not decrease significantly up to about 750°C.
また、この温度付近まで耐酸化性が良好であることも大
きな長所である。現在の高温用チタン合金の使用可能な
上限温度は約６００°Ｃであるが、上記Ｔｉ３Ａｊ！を
主体とする合金（以下ｒＴｉ、Ａｌ基合金」という）を
利用することにより、この使用限界温度を向上させるこ
とが可能であり、宇宙航空機用エンジン部材やタービン
部材等への応用が広がることが期待される。Another great advantage is that it has good oxidation resistance up to around this temperature. The upper limit temperature at which current high-temperature titanium alloys can be used is about 600°C, but the Ti3Aj! By using alloys mainly composed of rTi (hereinafter referred to as rTi, Al-based alloys), it is possible to improve this service temperature limit, and its application to spacecraft engine parts, turbine parts, etc. can be expanded. Be expected.
しかしながら、ＴＩ、ｌは高温強度が優れている反面、
室温延性は皆無に近い、このためにＴＩＪ ｆの実用化
が制限されているのが実情である。However, while TI,l has excellent high temperature strength,
Room-temperature ductility is almost non-existent, which limits the practical application of TIJ f.
Ｔ１３Ａ ｌの常温延性を改善するためにβ相安定化元
素であるニオブ（Ｎｂ）を添加し、Ｔｉ３Ａｌ中に少量
のβ相を分散させる方法がある（米国特許４，２９２，
０７７号明細書）、このようなβ相を分散させる方法に
おいては、β相の増加に伴い、常温延性は向上するが、
反面、Ｔｉ１／／！の大きな特長である高温強度が低下
する。従って、分散させるβ相の量には制限があり、常
温延性と高温強度の兼ね合いによってβ相の量、すなわ
ちアルミニウム（Ａ ｆｆｉ ）とβ相安定化元素の比
率が決められることになる。高温強度を低下させないた
めには、β相が可能な限り少ない状態で常温延性を向上
させることが望ましい。In order to improve the cold ductility of T13Al, there is a method of adding niobium (Nb), a β phase stabilizing element, to disperse a small amount of β phase in Ti3Al (US Pat. No. 4,292,
077 specification), in such a method of dispersing the β phase, the room temperature ductility improves as the β phase increases, but
On the other hand, Ti1//! The high temperature strength, which is a major feature of steel, decreases. Therefore, there is a limit to the amount of β phase to be dispersed, and the amount of β phase, ie, the ratio of aluminum (A ffi ) to β phase stabilizing elements, is determined by the balance between room temperature ductility and high temperature strength. In order not to reduce high-temperature strength, it is desirable to improve cold ductility with as little β phase as possible.
本発明者らは、先にＡＮ ： ９〜２５重量％、Ｂ：０
．００１〜０．４００重量％、残部Ｔｉからなるチタン
合金を提案した（特開昭６２−２５０１３９号公報）、
その合金は、ＴｉＪｊ！主体の合金にＢを添加すること
により熱間加工性を大幅に向上させたものである。The present inventors previously determined that AN: 9 to 25% by weight, B: 0
．． proposed a titanium alloy consisting of 0.001 to 0.400% by weight and the balance being Ti (Japanese Patent Application Laid-open No. 62-250139).
The alloy is TiJj! Hot workability is greatly improved by adding B to the main alloy.
（発明が解決しようとする課題）
ＴｉＪｊ！は常温延性が乏しく、そのために用途が非常
に制限される。その常温延性を高める方法として、常温
延性の高いβ相を分散させる前掲の米国特許４，２９２
，０７７号明細書の方法は優れた方法である。しかし、
そこに開示されている合金は、Ｎｂを１９．５〜３０重
量％と多量に含むものである。 Ｎｂは原子１９３の重
い元素で、しかも高価であるから、このような元素を多
量に添加することはＴｉ３Ａ １２の軽量性を損ない、
かつ材料コストを上げることになる。Ｎｂに限らず、他
のβ相安定化元素を添加してＴｉ５Ａ ｌとβ相からな
る組織とする場合も同様の問題が生じる。(Problem to be solved by the invention) TiJj! has poor room-temperature ductility, which severely limits its uses. As a method for increasing the room temperature ductility, the aforementioned U.S. Patent No. 4,292 discloses dispersing a β phase with high room temperature ductility.
, 077 is an excellent method. but,
The alloy disclosed therein contains a large amount of Nb, 19.5 to 30% by weight. Nb is a heavy element with 193 atoms and is expensive, so adding a large amount of such an element will impair the lightweight properties of Ti3A12.
This also increases material costs. Similar problems occur when not only Nb but also other β-phase stabilizing elements are added to create a structure consisting of Ti5Al and β-phase.
更に、通常は常温延性が向上すれば、常温強度および高
温強度が低下するのが一般的であり、これは耐熱合金の
長所を損なうことになる。Furthermore, as cold ductility improves, cold strength and high temperature strength generally decrease, which detracts from the advantages of heat-resistant alloys.
本発明の課題は、ｔｔｓ＾ｉ基合金の本来の特性である
軽量、高強度という長所をできるだけ損なわず、その常
温延性を改善することにある。具体的には、ＴｉＪｆｆ
ｉとβ相からなる組織においてβ相の量を極力抑えて、
Ｔｉ１Ａｌ基合金の高温強度の低下を引き起こさず、そ
の常温延性を改善することを目的とする。An object of the present invention is to improve the cold ductility of the tts^i-based alloy without impairing its original characteristics of light weight and high strength as much as possible. Specifically, TiJff
In a structure consisting of i and β phases, the amount of β phase is suppressed as much as possible,
The purpose is to improve the cold ductility of a Ti1Al-based alloy without causing a decrease in its high-temperature strength.
本発明において目標とするＴｌｌＡｌ基合金の特性は、
常温引張伸びが３％以上、７００”Ｃにおける０、２％
耐力が３０ｋｇｆ／■−２以上である。The properties of the TllAl-based alloy targeted in the present invention are as follows:
Tensile elongation at room temperature is 3% or more, 0.2% at 700"C
The yield strength is 30 kgf/■-2 or more.
（課題を解決するための手段）
本発明は、基本的にはβ安定化元素を添加してＴｉ、Ａ
ｌ中に少量のβ相を分散させてその常温延性を改善す
るものである。しかし、この方法において、β安定化元
素量を増加させ、β相を増加させることは前記のような
問題が生じるため、分散させるβ相の量を極力抑えなが
ら延性を改善することが望まれる。(Means for Solving the Problems) The present invention basically consists of adding β stabilizing elements to Ti, A
A small amount of β phase is dispersed in the steel to improve its room temperature ductility. However, in this method, increasing the amount of β-stabilizing elements and increasing the β-phase causes the above-mentioned problems, so it is desirable to improve ductility while suppressing the amount of the β-phase to be dispersed as much as possible.
本発明者らは、Ｂ（ボロン）、Ｃ（炭素）、Ｓｌ（珪素
）を単独または２種以上併せて適正量含有させることに
よって、β相の量を最小限に抑えながら、ＴｉＪ Ｊ！
基合金の常温延性を大きく改善できることを確認した。The present inventors have discovered that by containing appropriate amounts of B (boron), C (carbon), and Sl (silicon) alone or in combination of two or more, TiJ J!
It was confirmed that the room temperature ductility of the base alloy could be greatly improved.
ＢＳＣ，およびＳｌは、いずれも原子量がＴ１よりも小
さい軽元素であるから、前記のＮｂだけを多量に含有さ
せた場合のように合金の軽量性をｔ員なうことはない、
しかも、これらの元素の添加量を適正範囲にすれば、合
金の強度を低下させることもない。BSC and Sl are both light elements with an atomic weight smaller than T1, so the lightness of the alloy will not be reduced as in the case where only a large amount of Nb is contained.
Furthermore, if the amounts of these elements added are within appropriate ranges, the strength of the alloy will not be reduced.
本発明は、「金属間化合物Ｔ１．＾２を主体とし、体積
百分率（ｖｏｌ、％）で１〜２０％のβ相が分散した組
織の合金であって、更にボロン（Ｂ）、炭素（Ｃ）、お
よび珪素（Ｓｔ）の１種以上を単独または合計で０．０
０１〜０．４重量％含有する金属面化合物ＴｒＡｌ基軽
量耐熱合金」を要旨とする。The present invention is an alloy with a structure consisting mainly of an intermetallic compound T1.^2 with a β phase of 1 to 20% by volume (vol, %) dispersed therein, and further comprising boron (B) and carbon (C). ), and one or more types of silicon (St), singly or in total, 0.0
01 to 0.4% by weight of a metal surface compound TrAl-based lightweight heat-resistant alloy.
（作用）
まず、［金属間化合物ＴＩ！＾２を主体とする合金」に
ついて説明する。(Function) First, [Intermetallic Compound TI! An alloy mainly composed of ^2 will be explained.
この合金は、Ｔ１をベースとして、Ａ？１２〜１６重量
％と、■、Ｍｏ、 Ｎｂ、 Ｔａ、 Ｗ、 Ｃｒ、 Ｍ
ｎ、 Ｆｅ、 Ｃｏ、Ｎ１、Ｃｕなどのβ相安定化元素
を１種以上含むものである。これらの成分の含有量は、
代表的なＶに換算して、次の■当量式で３〜１２重量％
になるように含有させればよい。This alloy is based on T1 and A? 12-16% by weight, ■, Mo, Nb, Ta, W, Cr, M
It contains one or more β phase stabilizing elements such as n, Fe, Co, N1, and Cu. The content of these ingredients is
Converting to a typical V, 3 to 12% by weight according to the following ■equivalent formula
It is sufficient if it is contained so that it becomes.
Ｖｓｑ（χ）−■（χ）＋１．４Ｍｏ（χ） ＋０．４
Ｎｂ（χ）＋０．３Ｔａ（χ）＋０．６Ｗ（χ）＋２．
４Ｃｒ（χ）＋２．３％Ｍｎ（Ｘ）＋１．７Ｎ＋（χ）
＋４．３Ｆｅ（χ）＋２．１Ｃｏ（χ）＋１．２Ｃｕ（
χ）式中元素の「χ」は「重量％」である。Vsq(χ)−■(χ)+1.4Mo(χ)+0.4
Nb(χ)+0.3Ta(χ)+0.6W(χ)+2.
4Cr(χ)+2.3%Mn(X)+1.7N+(χ)
+4.3Fe(χ)+2.1Co(χ)+1.2Cu(
χ) "χ" of the element in the formula is "% by weight".
前記β相安定化元素のうちＭｏ、 Ｎｂ、 Ｔａ、 Ｗ
は■より重い、特にＴａ、 Ｗは重い元素であるので、
軽量性を維持するためには少ない含有量の方が好ましい
。また、Ｗ、Ｃｒ、Ｍｎ、 ＭＬ、 Ｆｅ、 Ｃｏ、
ＣｕはＴｉと結びついて他の金属間化合物を形成しやす
い、従って、最も実用的なのは、■を３〜１２重量％含
有する合金である。Among the β phase stabilizing elements, Mo, Nb, Ta, W
is heavier than ■, especially since Ta and W are heavy elements,
In order to maintain lightness, a small content is preferable. Also, W, Cr, Mn, ML, Fe, Co,
Cu tends to combine with Ti to form other intermetallic compounds. Therefore, the most practical alloy is an alloy containing 3 to 12% by weight of ■.
β相の量は、上記β相安定化元素の添加量によって調整
できるが、前記の理由からその量は必要最小限にとどめ
る。望ましいβ相の量は１〜２０ｖｏｌ。The amount of β phase can be adjusted by adjusting the amount of the β phase stabilizing element added, but for the reasons mentioned above, the amount is kept to the minimum necessary. The desirable amount of β phase is 1 to 20 vol.
％である。%.
次に、Ｂ、Ｃ，およびＳｔの含有量について説明する。Next, the contents of B, C, and St will be explained.
これらの元素の添加によって常温延性が改善されるのは
、次のような理由によるものと考えられる。すなわち、
これらの元素は、β相のみならずＴｉＪｆｆｉ相の粒界
に偏析し、粒界を強化して粒界破壊を防止することによ
ってＴｌｓ＾ｌ基合金の常温延性を改善する。このよう
な作用により、β相の分散量が少ない場合でも高い常温
延性が得られるから、β相安定化元素の添加量は少なく
て済む。The reason why room temperature ductility is improved by the addition of these elements is considered to be as follows. That is,
These elements segregate not only in the β phase but also in the grain boundaries of the TiJffi phase, strengthen the grain boundaries and prevent grain boundary fracture, thereby improving the room temperature ductility of the Tls^l-based alloy. Due to this effect, high cold ductility can be obtained even when the amount of β phase dispersed is small, so the amount of β phase stabilizing element added can be small.
Ｂ、ＣおよびＳｌはいずれも同様の効果を有するから、
単独添加でもよく、２種または３種の複合添加でもよい
、ただし、いずれの場合でも含有量は０．００１〜０．
４重量％の範囲とする。 ０．００１重量％未満では添
加の効果は認められない、また、０．４重量％を超える
含有量になると、これらの元素の偏析が起こりやすく合
金の脆化をもたらし、常温延性は却って低下する。Since B, C and Sl all have similar effects,
It may be added alone or in combination of two or three types, but in either case, the content is 0.001 to 0.
The range is 4% by weight. If the content is less than 0.001% by weight, the effect of addition is not recognized, and if the content exceeds 0.4% by weight, segregation of these elements tends to occur, resulting in embrittlement of the alloy, and the room temperature ductility decreases on the contrary. .
（実施例）
原料として純度９９．７％のスポンジチタン、純度９９
．９％のＡｌ、８４重量％Ｖ−１６重量％Ａｆｆｉの母
合金、ＴｉＢｘ 、Ｔｉｃ、純度９９．９９％のＳｉを
用い、非消耗電極式真空アーク溶解炉を使用して第１表
に示す化学組成を有する１、２ｋｇのインゴットを溶製
した。(Example) Sponge titanium with a purity of 99.7% as a raw material, purity 99
．． Using a master alloy of 9% Al, 84 wt% V-16 wt% Affi, TiBx, Tic, and 99.99% pure Si, the chemistry shown in Table 1 was performed using a non-consumable electrode type vacuum arc melting furnace. A 1-2 kg ingot having the following composition was melted.
第１表中の比較材というのは、Ｂ、、Ｓｔ、Ｃのいずれ
をも含有しないもの、またはそれらの含有量が多すぎる
ものである。The comparative materials in Table 1 are those that do not contain any of B, St, and C, or those that contain too much of these.
次にこれをβ域において熱間鍛造し外径１５層層の丸棒
を得て、真空中で９００’Ｃで２時間の焼鈍を行った。Next, this was hot forged in the β range to obtain a round bar with an outer diameter of 15 layers, and annealed in vacuum at 900'C for 2 hours.
これより外径４Ｉ、標点間距離１６ｍｇ＋の丸棒引張試
験片を採取し、引張試験に供した。引張試験は室温およ
び７００”Ｃにおいて歪速度を破断まで０．５％／ｗｒ
ｉ ｎとして実施した。試験の結果を第１表に示す。From this, a round bar tensile test piece with an outer diameter of 4I and a gauge distance of 16 mg+ was taken and subjected to a tensile test. Tensile tests were performed at room temperature and 700"C with a strain rate of 0.5%/wr to failure.
It was carried out as i.n. The test results are shown in Table 1.
本発明材は全て常温伸びが３％以上、７００℃での０．
２％耐力が３０ｋｇｆ／ｍａ＋”以上という目標値を満
足している。これに対して、比較材は、常温伸びと７０
０”Ｃでの０．２％耐力の一方または両方が目標値に達
していない。All of the materials of the present invention have an elongation at room temperature of 3% or more and an elongation of 0.2% at 700°C.
The 2% proof stress satisfies the target value of 30 kgf/ma+" or more. In contrast, the comparison material has a room temperature elongation of 70
One or both of the 0.2% yield strength at 0''C has not reached the target value.
（以下、余白）
（発明の効果）
実施例の試験結果にも明らかなように、本発明の合金は
、従来のＴｉ３Ａｊ！基合金に較べて同等以上の強度を
保ちながら延性が改善されている。(Hereinafter, blank space) (Effects of the invention) As is clear from the test results of the examples, the alloy of the present invention is different from the conventional Ti3Aj! Compared to the base alloy, it has improved ductility while maintaining the same or higher strength.
本発明のＴｉ３Ａ １基合金は、実施例のように溶解法
で製造することも、或いは粉末冶金法で製造することも
可能であって、そして、この合金は板材、管材、その他
各種の鋳鍛造材として広（実用化できるものである。The Ti3A single-base alloy of the present invention can be manufactured by a melting method as in the embodiments, or by a powder metallurgy method, and this alloy can be used for plate materials, pipe materials, and various other types of casting and forging. Widely used as a material (can be put to practical use).
Claims (2)
率で１〜２０％のβ相が分散した組織の合金であって、
更にボロン、炭素、および珪素の１種以上を単独または
合計で０．００１〜０．４重量％含有する金属間化合物
Ｔｉ＿３Ａｌ基軽量耐熱合金。(1) An alloy mainly composed of an intermetallic compound Ti_3Al and having a structure in which a β phase of 1 to 20% by volume is dispersed,
Furthermore, the intermetallic compound Ti_3Al-based lightweight heat-resistant alloy contains 0.001 to 0.4% by weight of one or more of boron, carbon, and silicon, singly or in total.
る特許請求の範囲第１項記載の金属間化合物Ｔｉ＿３Ａ
ｌ基軽量耐熱合金。(2) Intermetallic compound Ti_3A according to claim 1, containing 3 to 12% by weight of V as a β-phase stabilizing element
L-based lightweight heat-resistant alloy.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP9614689A JPH02274829A (en) | 1989-04-14 | 1989-04-14 | Intermetallic compound ti3al-base lightweight heat-resistance alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP9614689A JPH02274829A (en) | 1989-04-14 | 1989-04-14 | Intermetallic compound ti3al-base lightweight heat-resistance alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH02274829A true JPH02274829A (en) | 1990-11-09 |
Family
ID=14157243
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP9614689A Pending JPH02274829A (en) | 1989-04-14 | 1989-04-14 | Intermetallic compound ti3al-base lightweight heat-resistance alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH02274829A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5281285A (en) * | 1992-06-29 | 1994-01-25 | General Electric Company | Tri-titanium aluminide alloys having improved combination of strength and ductility and processing method therefor |
| JP2003064434A (en) * | 2001-08-21 | 2003-03-05 | Daido Steel Co Ltd | Ti BASED HEAT RESISTANT MATERIAL |
| CN104789808A (en) * | 2015-04-29 | 2015-07-22 | 陕西理工学院 | Titanium-aluminum-carbon-ceramic-reinforced Ti3Al-base composite material and preparation method thereof |
-
1989
- 1989-04-14 JP JP9614689A patent/JPH02274829A/en active Pending
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5281285A (en) * | 1992-06-29 | 1994-01-25 | General Electric Company | Tri-titanium aluminide alloys having improved combination of strength and ductility and processing method therefor |
| JP2003064434A (en) * | 2001-08-21 | 2003-03-05 | Daido Steel Co Ltd | Ti BASED HEAT RESISTANT MATERIAL |
| CN104789808A (en) * | 2015-04-29 | 2015-07-22 | 陕西理工学院 | Titanium-aluminum-carbon-ceramic-reinforced Ti3Al-base composite material and preparation method thereof |
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