JPH05320791A - Ti-al intermetallic compound alloy - Google Patents
Ti-al intermetallic compound alloyInfo
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- JPH05320791A JPH05320791A JP12351692A JP12351692A JPH05320791A JP H05320791 A JPH05320791 A JP H05320791A JP 12351692 A JP12351692 A JP 12351692A JP 12351692 A JP12351692 A JP 12351692A JP H05320791 A JPH05320791 A JP H05320791A
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Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は高比強度耐熱構造部材
（航空機用エンジン，発電用ガスタービン，自動車用エ
ンジン，高速回転体等）に用いるに適した、Ｔｉ−Ａｌ
系金属間化合物合金に関し、更に詳しくはγ相及びβ相
を主構成相とするＴｉ−Ａｌ系金属間化合物合金に関す
る。The present invention relates to a Ti-Al suitable for use in high specific strength heat resistant structural members (aircraft engines, power generation gas turbines, automobile engines, high speed rotating bodies, etc.).
More particularly, it relates to a Ti—Al based intermetallic compound alloy having γ phase and β phase as main constituent phases.
【０００２】[0002]
【従来の技術】周知の如く、Ｔｉ−Ａｌ２元合金系にお
いては、Ｔｉ3 Ａｌ，ＴｉＡｌ及びＴｉＡｌ3 の３つの
金属間化合物相が存在することが知られているが、この
うちＴｉＡｌ相はγ相と呼ばれ、正方晶のＬ１0 型の結
晶構造を有している。このγ相は従来のＴｉ合金に比べ
ると軽量，高比強度であり、約７００℃程度までは耐酸
化性も良好であるとの好ましい特性を有しているため、
航空機用エンジンなどの高温環境下で高強度が要求され
る部位に適用できるのではないかと期待されてきた。As is well known, it is known that there are three intermetallic compound phases of Ti 3 Al, TiAl and TiAl 3 in a Ti-Al binary alloy system. Of these, the TiAl phase is γ. It is called a phase and has a tetragonal L1 0 type crystal structure. This γ phase is lighter in weight and has a higher specific strength than conventional Ti alloys, and since it has favorable characteristics that it has good oxidation resistance up to about 700 ° C.,
It has been expected that it can be applied to parts that require high strength in high temperature environments such as aircraft engines.
【０００３】[0003]
【発明が解決しようとする課題】しかしながら、以下の
問題があり、これまで工業製品としての実用化はなされ
ていなかった。 (1) 延性が乏しく、室温では引張変形量１％以下で破壊
する。However, there are the following problems, and they have not been put into practical use as industrial products until now. (1) It has poor ductility and breaks at room temperature with a tensile deformation of 1% or less.
【０００４】(2) 耐酸化性が７００℃以上になると、急
激に劣化し、航空機用エンジン等の現用材であるＮｉ基
耐熱合金（例えば、インコネル713C）と較べると、酸化
増量値で約１０倍と劣る。(2) When the oxidation resistance is 700 ° C. or higher, it rapidly deteriorates, and when compared with a Ni-base heat-resistant alloy (for example, Inconel 713C) which is the current material for aircraft engines, it has an oxidation weight increase value of about 10%. Inferior
【０００５】(3) 常温〜高温域における強度が現用材よ
り劣る。技術文献での一例を示すと、リップシット（Ｌ
ipsitt）ら著の冶金学会誌（Ｍetallurgical Ｔransac
tions ）第６Ａ号（1975年）1991頁によると、γ単相合
金の引張強度は室温で４５ｋｇｆ／ｍｍ2 ，８００℃で
３６Ｋｇｆ／ｍｍ2 である。一方、インコネル713Cの引
張強度は米国International Nickel社のデータブックに
よると、室温で８６Ｋｇｆ／ｍｍ2 ，７６０℃で９６Ｋ
ｇｆ／ｍｍ2 ，８７０℃で７４Ｋｇｆ／ｍｍ2 であるこ
とにより、比強度（強度を材料の密度で除した値）換算
してもγ単相合金の強度は、特に高温域においてインコ
ネル713Cより劣るといえる。なお、各材料の密度は、γ
単相合金３．８ｇ／ｃｍ3 ，インコネル713C７．９ｇ／
ｃｍ3 である。(3) The strength in the normal temperature to high temperature range is that of the current material.
Inferior. An example in the technical literature is the lip sit (L
ipsitt) et al. Journal of Metallurgical Society (Metallurgical Transac)
tions) No. 6A (1975), page 1991, γ single phase
The tensile strength of gold is 45 kgf / mm at room temperature2 At 800 ° C
36 Kgf / mm2 Is. Meanwhile, the Inconel 713C pull
Tensile strength in a data book from International Nickel, USA
According to the room temperature, 86 Kgf / mm2 96K at 760 ℃
gf / mm2 , Kgf / mm at 870 ℃2 It is
Converted to specific strength (value obtained by dividing strength by material density)
Even so, the strength of the γ single phase alloy is
It can be said that it is inferior to the Nell 713C. The density of each material is γ
Single phase alloy 3.8g / cm3 , Inconel 713C 7.9g /
cm3 Is.
【０００６】しかしながら、近年、第３元素を添加する
とともに、Ｔｉ及びＡｌの濃度を制御することにより、
組織を制御し、上記問題の改善を計る試みがいくつか提
案されている。However, in recent years, by adding the third element and controlling the concentrations of Ti and Al,
Several attempts have been proposed to control the organization and try to improve the above problems.
【０００７】例えば、特開平１−２９８１２７号公報の
明細書には、Ｔｉ６４．８重量％，Ａｌ３３．７重量
％，Ｃｒ１．５重量％（原子％に換算すると、Ｔｉ５
１．４原子％，Ａｌ４７．５原子％，Ｃｒ１．１原子
％）合金が開示されている。この合金は、ＴｉＡｌ相
（γ相）及びＴｉ3 Ａｌ相（γ相）及びＴｉ3 Ａｌ相
（α2 相）の２相組織合金であり、同明細書の実施例に
おいては、室温引張強度４０．４Ｋｇｆ／ｍｍ2 ，同伸
び１．９％であることが、また８００℃の引張強度４
１．６Ｋｇｆ／ｍｍ2 ，同伸び３．２％であることが開
示されている。即ち、第３元素としてＣｒ１．１原子％
を添加し、Ａｌ濃度４７．５原子％，Ｔｉ濃度５１．４
原子％として、組成をγ＋α2 の２相組織とすることに
より、常温延性が改善したとされている。しかしなが
ら、強度はほとんど改善されておらず、γ単相合金とほ
ぼ同等である。For example, in the specification of Japanese Patent Laid-Open No. 1-298127, 64.8% by weight of Ti, 33.7% by weight of Al, and 1.5% by weight of Cr (converted into atomic%, Ti5
1.4 at%, Al 47.5 at%, Cr 1.1 at%) alloys are disclosed. This alloy is a two-phase structure alloy of TiAl phase (γ phase), Ti 3 Al phase (γ phase) and Ti 3 Al phase (α 2 phase), and in the example of the specification, room temperature tensile strength is 40%. 0.4 Kgf / mm 2 The same elongation is 1.9%, and the tensile strength at 800 ° C is 4
1.6 Kgf / mm 2 , The same growth is disclosed to be 3.2%. That is, as the third element, Cr 1.1 atomic%
Is added, the Al concentration is 47.5 atomic% and the Ti concentration is 51.4.
It is said that the room temperature ductility is improved by making the composition a two-phase structure of γ + α 2 in terms of atomic%. However, the strength is hardly improved, and is almost the same as that of the γ single phase alloy.
【０００８】また、同じ特開平１−２９８１２７号公報
の明細書には、Ｔｉ５２．５重量％，Ａｌ３２．５重量
％，Ｎｂ１４．７重量％（原子％に換算すると、Ｔｉ４
４．７原子％，Ａｌ４８．９原子％，Ｎｂ６．４原子
％）合金が開示されている。この合金も同様にγ相とα
2 相の２相組織であり、同明細書の実施例においては室
温引張強度３９．８Ｋｇｆ／ｍｍ2 ，同伸び２．５％で
あることが、また８００℃の引張強度４０．０Ｋｇｆ／
ｍｍ2 ，同伸び４．１％であることが開示されている。
即ち、Ｎｂを６．４原子％添加し、Ａｌ濃度４８．９原
子％，Ｔｉ濃度４４．７原子％として組織をγ＋α2 の
２相組織とすることにより常温延性が改善したとされて
いる。しかしながら、Ｃｒ添加合金と同様に強度はほと
んど改善されておらず、γ相手合金とほぼ同等である。Further, in the specification of the same Japanese Unexamined Patent Publication No. 1-298127, 52.5% by weight of Ti, 32.5% by weight of Al, and 14.7% by weight of Nb (converted to atomic%, Ti4 is
(4.7 atomic%, Al 48.9 atomic%, Nb 6.4 atomic%) alloys are disclosed. This alloy also has γ phase and α
It has a two- phase two-phase structure, and in the examples of the specification, the room temperature tensile strength is 39.8 Kgf / mm 2. The same elongation is 2.5%, and the tensile strength at 800 ° C is 40.0 Kgf /
mm 2 , The same growth is disclosed to be 4.1%.
That is, it is said that the normal temperature ductility is improved by adding 6.4 atomic% of Nb and setting the Al concentration of 48.9 atomic% and the Ti concentration of 44.7 atomic% to form a two-phase structure of γ + α 2 . However, similarly to the Cr-added alloy, the strength has not been improved so much and is almost equal to that of the γ mating alloy.
【０００９】他の試みとして、特公昭５９−５８１号公
報の明細書には、Ｔｉ５６．３重量％，Ａｌ３３．７重
量％，Ａｇ１０重量％（原子％に換算すると、Ｔｉ４
６．７原子％，Ａｌ４９．６原子％，Ａｇ３．７原子
％）合金が開示されている。また、特公昭６２−２１５
号公報の明細書には、Ｔｉ６４．６重量％，Ａｌ３３．
３重量％，Ｍｎ２．１重量％（原子％に換算すると、Ｔ
ｉ５１．５原子％，Ａｌ４７．１原子％，Ｍｎ１．４原
子％）合金が開示されている。更に、米国特許第４，２
９４，６１５号には、Ｔｉ６１．８重量％，Ａｌ３４．
８重量％，Ｖ３．４重量％（原子％に換算すると、Ｔｉ
４８．８原子％，Ａｌ４８．７原子％，Ｖ２．５原子
％）合金が開示されている。これらの合金は、いずれも
常温延性はある程度改善されているものの、強度は逆に
低下し、γ単相合金よりもさらに低くなる。以上示した
５つの第３元素を添加したＴｉ−Ａｌ系合金の耐酸化性
は、次の通りである。 (1) Ａｇ，Ｍｎ，Ｖを各々添加した合金…γ単相合金よ
り劣る。 (2) Ｃｒを添加した合金…γ単相合金とほぼ同等であ
る。 (3) Ｎｂを添加した合金…γ単相合金よりも優れている
が、インコネル713Cよりは劣る。As another attempt, the specification of Japanese Patent Publication No. 59-581 discloses that Ti 56.3% by weight, Al 33.7% by weight, Ag 10% by weight (converted to atomic%, Ti 4
6.7 at%, Al 49.6 at%, Ag 3.7 at%) alloys are disclosed. In addition, Japanese Patent Publication Sho-62-215
In the specification of the publication, Ti 64.6% by weight, Al 33.
3 wt%, Mn 2.1 wt% (converted to atomic%, T
i51.5 at%, Al 47.1 at%, Mn 1.4 at%) alloys are disclosed. Furthermore, US Pat.
No. 94,615, Ti 61.8 wt%, Al34.
8% by weight, V3.4% by weight (converted to atomic%, Ti
48.8 atomic%, Al48.7 atomic%, V2.5 atomic%) alloys are disclosed. Although the room temperature ductility of each of these alloys has been improved to some extent, the strength of the alloys, on the contrary, decreases, which is even lower than that of the γ single phase alloy. The oxidation resistance of the Ti-Al alloy containing the above-mentioned five third elements is as follows. (1) Alloys with Ag, Mn, and V added ... inferior to γ single-phase alloys. (2) Cr-added alloy ... Almost the same as the γ single-phase alloy. (3) Nb-added alloy: Superior to γ single-phase alloy but inferior to Inconel 713C.
【００１０】要約すると、先に示したγ相の問題点を改
善すべく、第３元素を添加し、Ｔｉ及びＡｌの濃度を制
御して組織を制御する（γ＋α2 の２相組織にする）試
みが、これまで種々なされてきたが、いずれも不十分で
あると言える。即ち、常温延性はある程度改善されたも
のの、強度はほとんど改善していいない。また、耐酸化
性もＮｂ添加合金を除き、改善されていない。In summary, in order to improve the above-mentioned problems of the γ phase, a third element is added and the concentration of Ti and Al is controlled to control the texture (giving a two-phase texture of γ + α 2 ). Although various attempts have been made so far, it can be said that all are insufficient. That is, although the room temperature ductility was improved to some extent, the strength was hardly improved. Also, the oxidation resistance has not been improved except for the Nb-added alloy.
【００１１】本発明は上記事情に鑑みてなされたもの
で、γ相の特性改善を行い、従来技術の合金と同様の常
温延性を持ち、強度，耐酸化性で従来技術を陵駕するＴ
ｉ−Ａｌ系金属間化合物合金を提供することを目的とす
る。The present invention has been made in view of the above circumstances and has improved the characteristics of the γ phase, has room temperature ductility similar to that of the alloy of the prior art, and has strength and oxidation resistance, which are superior to those of the prior art.
It is an object to provide an i-Al-based intermetallic compound alloy.
【００１２】[0012]
【課題を解決するためのの手段】本発明者らは、上述の
ような観点から、種々の添加元素を含有するＴｉ−Ａｌ
系合金において、組成，組織と機械的特性及び耐酸化性
等の関係を研究した結果、以下の（ａ）〜（ｅ）に示す
知見を得るに至った。SUMMARY OF THE INVENTION From the above-mentioned viewpoints, the present inventors have made Ti-Al containing various additive elements.
As a result of studying the relationship between the composition, structure and mechanical properties, oxidation resistance, etc. of the system alloys, the following findings (a) to (e) have been obtained.
【００１３】（ａ）．Ｔｉ−Ａｌ２元系においてＡｌ濃
度４０〜６０原子％の範囲の合金の機械的特性を調査し
たところ、Ａｌ濃度５０原子％未満の合金の特性が優れ
ていることが分かった。また、この理由として、組成の
変化に伴う次の２つの材料固子の変化が関与しているこ
とが分かった。(A). When the mechanical properties of the alloy having an Al concentration of 40 to 60 atomic% in the Ti-Al binary system were investigated, it was found that the alloy having an Al concentration of less than 50 atomic% had excellent properties. Also, it was found that the reason for this is that the following two changes in the material solids due to the change in composition are involved.
【００１４】イ）．Ａｌ濃度が減少するほど正方晶であ
るγ相の結晶軸比（ｃ／ａ）は１に近づく。なお、一般
的に、結晶軸比が１に近づけば、結晶の異方性が減少
し、すべり変形等が容易になり、延性改善に結びつくと
言われている。 ロ）．Ａｌ濃度が減少するにつれ、組織はγ単相からγ
＋α2 ２層組織に変化する。また、Ａｌ濃度の減少に伴
い、α2 相の割合は増加する。A). The crystal axis ratio (c / a) of the tetragonal γ phase approaches 1 as the Al concentration decreases. It is generally said that when the crystal axis ratio is close to 1, crystal anisotropy is reduced, slip deformation and the like are facilitated, and ductility is improved. B). As the Al concentration decreases, the structure changes from γ single phase to γ
Change to + α 2 two-layer structure. Further, the proportion of the α 2 phase increases with the decrease of the Al concentration.
【００１５】即ち、Ｔｉ−Ａｌ２元系では、材料因子的
には結晶軸比が１に近づき、組織がγ＋α2 の２相組織
になることによって機械的特性は改善することが分かっ
た。Ａｌ濃度５０原子％未満において更に詳細に調査し
たところ、Ａｌ濃度と機械的性質には次の関係があるこ
とがわかった。 強度：Ａｌ濃度が減少するほど向上する。 延性：４８原子％付近が最も優れており、更にＡｌ濃度
が減少すると逆に低下する。That is, it was found that in the Ti-Al binary system, the crystal axis ratio approaches 1 in terms of a material factor and the structure becomes a two-phase structure of γ + α 2 so that the mechanical properties are improved. Further detailed investigation at an Al concentration of less than 50 atomic% revealed that the following relationship exists between the Al concentration and mechanical properties. Strength: Improves as the Al concentration decreases. Ductility: The highest value is around 48 atomic%, and conversely decreases as the Al concentration decreases.
【００１６】この理由としては、先に述べたようにＡｌ
濃度が減少すると、結晶軸比は１に近付くものの、その
一方で第２層であるα2 相の割合が増加することが考え
られる。即ち、α2 相は延性改善のためにはある程度必
要であるが、多量に存在しすぎると、逆に延性に悪影響
を及ぼすことが分かった。一方、強度向上のためには、
α2 相の存在は望ましいことが分かった。 （ｂ）．Ａｌ濃度４０〜６０原子％において、Ｎｂを１
〜１５原子％添加してＴｉ−Ａｌ系合金の特性を調査し
たところ、次のことが明らかになった。The reason for this is that, as mentioned above, Al
When the concentration decreases, the crystal axis ratio approaches 1, but on the other hand, the proportion of the α 2 phase, which is the second layer, may increase. That is, it was found that the α 2 phase is required to some extent to improve the ductility, but if it is present in a large amount, it adversely affects the ductility. On the other hand, in order to improve strength,
It has been found that the presence of the α 2 phase is desirable. (B). Nb is 1 at an Al concentration of 40 to 60 atomic%.
As a result of investigating the characteristics of the Ti-Al-based alloy with the addition of -15 atomic%, the following facts were revealed.
【００１７】イ）．Ｎｂは主にＴｉと置換し、（Ｔｉ，
Ｎｂ）Ａｌで表記される合金系を形成する。この結果、
組織，機械的特性はＴｉ−Ａｌ２元素と類似のものにな
る。即ち、Ａｌ濃度５０原子％未満の合金の機械的特性
が優れており、強度はＡｌ濃度が減少するほど向上す
る。一方、延性はＡｌ濃度４８原子％付近が最も優れて
おり、さらにＡｌ濃度が減少すると低下する。これは、
Ｔｉ−Ａｌ２元系と同様にα2 相の割合が増加しすぎる
ためと考えられる。A). Nb is mainly replaced with Ti, and (Ti,
Nb) Form an alloy system represented by Al. As a result,
The structure and mechanical properties are similar to those of Ti-Al2 element. That is, the alloy having an Al concentration of less than 50 atomic% has excellent mechanical properties, and the strength improves as the Al concentration decreases. On the other hand, the ductility is most excellent when the Al concentration is around 48 atomic%, and decreases when the Al concentration further decreases. this is,
It is considered that the ratio of the α 2 phase increases too much as in the Ti-Al binary system.
【００１８】Ｎｂを添加した合金の機械的特性はＡｌ濃
度４８原子％程度でＮｂ添加量１０原子％程度の合金が
最も優れているが、Ｔｉ−Ａｌ２元系と比較した場合、
強度は若干向上するものの、延性は大差ない。 ロ）．耐酸化性は大幅に改善され、上記合金ではＴｉ−
Ａｌ２元系合金と比べると酸化増量値で言って１／１０
程度になる。 （ｃ）．Ａｌ濃度４０〜６０原子％において、Ｃｒを１
〜１２原子％添加したＴｉ−Ａｌ系合金の特性を調査し
たところ、次のことが明らかになった。 (a) ，(b) の合金と同様にＡｌ濃度５０原子％未満の合
金の機械的特性が優れている。更に、詳細に言うと（Ｃ
ｒ添加量が３原子％以下の場合）：Regarding the mechanical properties of the alloy containing Nb, the alloy having an Al concentration of about 48 atomic% and the amount of Nb added of about 10 atomic% is the best, but when compared with the Ti-Al binary system,
Although the strength is slightly improved, the ductility is not so different. B). Oxidation resistance is greatly improved and Ti-
Compared with Al2 binary alloy, it is 1/10 in terms of oxidation weight increase value.
It will be about. (C). When the Al concentration is 40 to 60 atomic%, Cr is 1
When the characteristics of the Ti-Al-based alloy added with -12 atom% were investigated, the following facts were revealed. Like the alloys (a) and (b), the alloys having an Al concentration of less than 50 atomic% have excellent mechanical properties. Furthermore, in detail (C
(When the amount of r added is 3 atomic% or less):
【００１９】Ａｌ濃度４８原子％付近では従来技術で見
られたように延性は向上するが、強度は向上しない。一
方、Ａｌ濃度４６原子％以下では強度は向上するが、延
性は低下する。これは、Ｔｉ−Ａｌ２元系と同様にＡｌ
濃度の減少に伴ない、α2 相の割合が増加したためと考
えられる。（Ｃｒ添加量が３〜８原子％の場合）：When the Al concentration is around 48 atomic%, the ductility is improved, but the strength is not improved as seen in the prior art. On the other hand, when the Al concentration is 46 atomic% or less, the strength is improved but the ductility is decreased. This is similar to the Ti-Al binary system
It is considered that the proportion of α 2 phase increased with the decrease in concentration. (When the added amount of Cr is 3 to 8 atomic%):
【００２０】Ａｌ濃度４８原子％付近では延性が低下す
る。これはＴｉ合金においてβ安定化元素であるＣｒを
多量に添加したため、α2 相の割合が必要以上に低下し
すぎ、γ単相合金に近づいたためと考えられる。Ductility decreases when the Al concentration is around 48 atomic%. It is considered that this is because a large amount of Cr, which is a β-stabilizing element, was added to the Ti alloy, so that the ratio of α 2 phase was excessively decreased and became close to the γ single-phase alloy.
【００２１】一方、Ａｌ濃度４０〜４６原子％では延性
・強度とも向上する。この合金の組織はγ相とβ相（Ｂ
ＣＣ構造の固溶性）の２相組織であり、Ａｌ濃度の減少
によりγ相の結晶軸比は１に近づき、第２相であるβ相
の割合は増加する。機械的特性が改善した理由として
は、材料因子的にはＴｉ−Ａｌ２元系合金と同様にγ相
の結晶軸比が１に近づき、多相組織となることにより延
性が向上したことが考えられる。また、第２相の割合が
増加することにより、強度が向上したことが考えられ
る。なお、β層はα2 層と異なり、多量に存在しても延
性には悪影響を及ぼすことがないことが分かった。（Ｃ
ｒ添加量が８原子％以上の場合）：On the other hand, when the Al concentration is 40 to 46 atomic%, both ductility and strength are improved. The structure of this alloy is γ phase and β phase (B
It has a two-phase structure (solid solubility of CC structure), and the crystal axis ratio of the γ phase approaches 1 and the proportion of the β phase, which is the second phase, increases due to the decrease in Al concentration. The reason why the mechanical properties are improved is that, as a material factor, the crystal axis ratio of the γ phase approaches 1 as in the case of the Ti-Al binary alloy, and the ductility is improved due to the multiphase structure. .. Further, it is considered that the strength was improved by increasing the proportion of the second phase. It was found that, unlike the α 2 layer, the β layer does not adversely affect the ductility even if it is present in a large amount. (C
(When the amount of r added is 8 atomic% or more):
【００２２】Ａｌ濃度にかかわらず延性は低下する。こ
れは、Ｃｒ添加量の増加に伴い、非常に脆いＣｒ2 Ｔｉ
相（Ｃ15型のラーベス相）が多量に生成するためと考え
られる。また、（ｃ）の合金の耐酸化性は次の通りであ
る。 （Ｃｒ添加量が３原子％以下の場合）：Ｔｉ−Ａｌ２元
系合金と大差なく、７００℃以上になると急激に劣化す
る。 （Ｃｒ添加量が３原子％以上の場合）：Ｔｉ−Ａｌ２元
系よりは優れているが、（ｂ）の合金でＮｂを１０原子
％添加したものと比べると、かなり劣る。The ductility decreases regardless of the Al concentration. This is because Cr 2 Ti, which is extremely brittle as the amount of Cr added increases.
It is considered that this is because a large amount of phase (C15 type Laves phase) is generated. Further, the oxidation resistance of the alloy (c) is as follows. (When the amount of Cr added is 3 atomic% or less): There is not much difference from the Ti-Al binary alloy, and it deteriorates rapidly at 700 ° C or higher. (When the amount of Cr added is 3 atomic% or more): Although it is superior to the Ti-Al binary system, it is considerably inferior to the alloy of (b) in which 10 atomic% of Nb is added.
【００２３】（ｄ）．（ｃ）において延性・強度ともに
改善が認められた合金（Ａｌ濃度４４原子％程度，Ｃｒ
濃度５原子％程度）にＮｂを８原子程度添加した合金の
特性は次の通りである。 イ）．組織は（Ｃ）の合金と同様に、γ＋βの２相組織
である。 ロ）．延性は（ｃ）と大差ないものの、強度は（ｃ）の
合金よりさらに優れている。(D). Alloys with improved ductility and strength in (c) (Al concentration about 44 atomic%, Cr
The characteristics of the alloy obtained by adding about 8 atoms of Nb to the concentration (about 5 atomic%) are as follows. I). Similar to the alloy of (C), the structure is a γ + β two-phase structure. B). The ductility is not so different from that of (c), but the strength is further superior to that of the alloy of (c).
【００２４】ハ）．耐酸化性は（ｃ）の合金よりはるか
に優れており、（ｂ）の合金とほぼ同等である。即ち、
Ａｌ濃度を４４原子％程度とし、Ｃｒを５原子％程度，
Ｎｂを８原子％程度添加したＴｉ−Ａｌ系合金はγ＋β
の２相組織であり、延性については従来技術の合金とほ
ぼ同等であるものの、強度及び耐酸化性では従来技術の
合金をはるかに陵駕することがわかった。C). The oxidation resistance is far superior to that of the alloy of (c) and almost the same as that of the alloy of (b). That is,
Al concentration is about 44 atomic%, Cr is about 5 atomic%,
The Ti-Al based alloy containing about 8 atomic% of Nb has γ + β
It has been found that the alloy has a two-phase structure and its ductility is almost the same as that of the alloy of the prior art, but its strength and oxidation resistance are far superior to those of the alloy of the prior art.
【００２５】（ｅ）．（ｄ）の合金にＴａを添加した合
金、具体的にはＡｌ濃度４４原子％程度で，Ｃｒを５原
子％程度，Ｎｂを８原子％程度，Ｔａを３原子％程度添
加した合金の特性は次の通りである。 イ）．組織は、（ｃ），（ｄ）の合金と同様にγ＋βの
２相組織である。(E). The characteristics of the alloy in which Ta is added to the alloy of (d), specifically, the alloy in which the Al concentration is about 44 atomic%, Cr is about 5 atomic%, Nb is about 8 atomic%, and Ta is about 3 atomic% have the following characteristics. It is as follows. I). The structure is a γ + β two-phase structure similar to the alloys of (c) and (d).
【００２６】ロ）．延性は（ｄ）の合金に較べると若干
劣るものの、強度は（ｄ）の合金よりもさらに向上す
る。また、この向上程度は高温域において、特に顕著で
ある。 ハ）．耐酸化性は（ｄ）の合金とほぼ同等である。 即ち、この合金は（ｄ）の合金とほぼ同等の特性を持つ
が、（ｄ）と較べると特に高温域において高強度であ
り、逆に常温域においては延性は若干劣る。本発明は、
上記知見等に基づくいてなされたもので、B). The ductility is slightly inferior to the alloy of (d), but the strength is further improved as compared with the alloy of (d). Further, this degree of improvement is particularly remarkable in the high temperature range. C). The oxidation resistance is almost the same as the alloy of (d). That is, although this alloy has almost the same characteristics as the alloy of (d), it has a higher strength than that of (d) especially in a high temperature region, and on the contrary, has a slightly poor ductility in a normal temperature region. The present invention is
It was made based on the above findings,
【００２７】（１）Ｔｉ：３４〜５２原子％，Ａｌ：４
０〜４６原子％，Ｃｒ：３〜８原子％，Ｎｂ：５〜１２
原子％を含有することを特徴とするＴｉ−Ａｌ系金属間
化合物合金（第１化合物合金）、あるいは(1) Ti: 34 to 52 atomic%, Al: 4
0 to 46 atomic%, Cr: 3 to 8 atomic%, Nb: 5 to 12
Ti-Al-based intermetallic compound alloy (first compound alloy) characterized by containing atomic%, or
【００２８】（２）Ｔｉ：３０〜５１原子％，Ａｌ：４
０〜４６原子％，Ｃｒ：３〜８原子％，Ｎｂ：５〜１２
原子％，Ｔａ：１〜４原子％を含有することを特徴とす
るＴｉ−Ａｌ系金属間化合物合金（第２化合物合金）で
ある。(2) Ti: 30 to 51 at%, Al: 4
0 to 46 atomic%, Cr: 3 to 8 atomic%, Nb: 5 to 12
It is a Ti-Al-based intermetallic compound alloy (second compound alloy) characterized by containing atomic% and Ta: 1 to 4 atomic%.
【００２９】[0029]
【作用】以下、上記Ｔｉ−Ａｌ系金属間化合物合金を構
成する各成分量の限定理由を各成分の作用と共に説明す
る。 （１）ＴｉThe reason for limiting the amount of each component constituting the above Ti-Al intermetallic compound alloy will be described below together with the action of each component. (1) Ti
【００３０】前記第１化合物合金においては、Ｔｉ濃度
が５２原子％を越えると、非常に脆い相，即ちＣｒ2 Ｔ
ｉ相（ラーベス相）及びＮｂ2 Ａｌ相（シグマ相）が多
量に生成するため、延性が低下する。一方、Ｔｉ濃度が
３４原子％未満になると、γ相の割合が増加し、β相の
割合が必要以上に減少しすぎる。また、同時にγ相の結
晶軸比が大きくなるため、延性，強度とも低下する。In the first compound alloy, when the Ti concentration exceeds 52 atomic%, a very brittle phase, that is, Cr 2 T.
Since the i phase (Laves phase) and the Nb 2 Al phase (sigma phase) are produced in large amounts, the ductility decreases. On the other hand, when the Ti concentration is less than 34 atomic%, the proportion of the γ phase increases and the proportion of the β phase decreases excessively. At the same time, since the crystal axis ratio of the γ phase increases, both ductility and strength decrease.
【００３１】前記第２化合物においては、Ｔｉ濃度が５
１原子％を越えると、非常に脆い相，即ちＣｒ2 Ｔｉ相
（ラーベス相）及び（Ｎｂ，Ｔａ）2 Ａｌ相（シグマ
相）が多量に生成するため、延性が低下する。一方、Ｔ
ｉ濃度が３０原子％未満になると、γ相の割合が増加
し、β相の割合が必要以上に減少しすぎる。また、同時
にγ相の結晶軸比が大きくなるため、延性，強度とも低
下する。 （２）ＡｌIn the second compound, the Ti concentration is 5
If it exceeds 1 atomic%, a very brittle phase, that is, a Cr 2 Ti phase (Laves phase) and a (Nb, Ta) 2 Al phase (sigma phase) are formed in large amounts, and thus ductility decreases. On the other hand, T
If the i concentration is less than 30 atomic%, the ratio of the γ phase increases and the ratio of the β phase excessively decreases. At the same time, since the crystal axis ratio of the γ phase increases, both ductility and strength decrease. (2) Al
【００３２】前記第１，第２化合物合金において、Ａｌ
濃度が４６原子％を越えると、γ相の割合が増加し、β
相の割合が必要以上に減少しすぎる。また、同時にγ相
の結晶軸比が大きくなるため、延性・強度とも低下す
る。一方、Ａｌ濃度が４０原子％未満になると、非常に
脆い相，即ちＣｒ2 Ｔｉ相（ラーベス相）及びＮｂ2 Ａ
ｌ相（シグマ相）が多量に生成するため、延性が低下す
る。 （３）ＣｒIn the first and second compound alloys, Al
When the concentration exceeds 46 atomic%, the ratio of γ phase increases and β
The proportion of phases is reduced too much. At the same time, since the crystal axis ratio of the γ phase increases, both ductility and strength decrease. On the other hand, when the Al concentration is less than 40 atomic%, a very brittle phase, that is, Cr 2 Ti phase (Laves phase) and Nb 2 A
Since a large amount of l phase (sigma phase) is generated, ductility is reduced. (3) Cr
【００３３】前記第１，第２化合物合金において、β相
を安定化させる働きを持つが、Ｃｒ濃度が８原子％を越
えると、非常に脆い，Ｃｒ2 Ｔｉ相（ラーベス相）が多
量に生成するため、延性が低下する。一方、３原子％未
満になると、添加効果が認められなくなる。 （４）ＮｂIn the first and second compound alloys, it has a function of stabilizing the β phase, but when the Cr concentration exceeds 8 atomic%, a very brittle Cr 2 Ti phase (Laves phase) is formed in a large amount. Therefore, the ductility decreases. On the other hand, if it is less than 3 atomic%, the effect of addition cannot be recognized. (4) Nb
【００３４】前記第１，第２化合物合金において、強度
並びに耐酸化性を向上させる働きを持つが、Ｎｂ濃度が
１２原子％を越えると、非常に脆いＮｂ2 Ａｌ層（シグ
マ層）が多量に生成するため、延性が低下する。一方、
５原子未満になると、添加効果が認められなくなる。 （５）ＴａIn the first and second compound alloys, it has a function of improving strength and oxidation resistance, but when the Nb concentration exceeds 12 atomic%, a very brittle Nb 2 Al layer (sigma layer) is formed in a large amount. As a result, ductility decreases. on the other hand,
If it is less than 5 atoms, the effect of addition cannot be recognized. (5) Ta
【００３５】前記第２化合物合金において、強度（特に
高温域での）をさらに向上させる働きをもつが、Ｔａ濃
度が４原子％を越えると、非常に脆い（Ｎｂ，Ｔａ）2
Ａｌ相（シグマ相）が多量に生成するため、延性が低下
する。一方、１原子未満になると、添加効果が認められ
なくなる。The second compound alloy has a function of further improving the strength (especially in a high temperature range), but when the Ta concentration exceeds 4 atomic%, it is extremely brittle (Nb, Ta) 2
Since a large amount of Al phase (sigma phase) is generated, ductility is reduced. On the other hand, if it is less than 1 atom, the effect of addition cannot be recognized.
【００３６】[0036]
【実施例】以下、本発明の実施例について説明する。EXAMPLES Examples of the present invention will be described below.
【００３７】純度９９．９％のスポンジチタン，純度９
９．９９％のＡｌ，純度９９．９％のＣｒ，純度９９．
９％のＮｂ，及び純度９９．９％のＴａを原料として用
い、非消耗電極式アーク溶解炉によって、下記「表１」
に示す化学組成のインゴットを溶製した。Titanium sponge with a purity of 99.9%, purity 9
9.99% Al, purity 99.9% Cr, purity 99.
Using 9% Nb and Ta with a purity of 99.9% as raw materials, a non-consumable electrode type arc melting furnace was used, and the following "Table 1" was used.
An ingot having the chemical composition shown in Figure 1 was melted.
【００３８】[0038]
【表１】 次に、このインゴットを１０００℃で５０時間焼鈍した
後、機械加工により外径４ｍｍ標点間距離１８ｍｍの引
張試験片を切り出して引張試験を実施した。[Table 1] Next, after annealing this ingot at 1000 ° C. for 50 hours, a tensile test piece having an outer diameter of 4 mm and a gauge length of 18 mm was cut out by machining to perform a tensile test.
【００３９】また、同じインゴットにより１５ｍｍ×２
０ｍｍ×２ｍｍの平板状の酸化試験片を切り出し、コメ
リー紙で１０００番まで研磨した後、酸化試験を行っ
た。試験温度は９００℃であり、大気中で１００時間保
持した後の酸化増量値により耐酸化性を評価した。Also, 15 mm × 2 by the same ingot
A 0 mm × 2 mm flat plate-shaped oxidation test piece was cut out, and after being polished up to No. 1000 with comery paper, an oxidation test was performed. The test temperature was 900 ° C., and the oxidation resistance was evaluated by the value of the increased amount of oxidation after holding in the atmosphere for 100 hours.
【００４０】なお、上記「表１」には、比較のためＴｉ
−Ａｌ２元系材で最も特性が優れいているＴｉ５２原子
％Ａｌ４８原子％を含有する合金（γ＋α2 の２相組
織）、従来技術であるＣｒを添加した合金，具体的には
組成Ｔｉ５０原子％Ａｌ４８原子％Ｃｒ２原子％の合金
（γ＋α2 の２相組織）、及び同様に従来技術であるＮ
ｂを添加した合金，具体的には組成Ｔｉ４８原子％Ａｌ
４８原子％Ｎｂ４原子％の合金（γ＋α2 の２相組織）
について、同様の試験を実施した結果を併記した。In Table 1 above, Ti is used for comparison.
Alloys containing the most characteristic is not excellent Ti52 at% Al48% by atom -Al2 ternary material (gamma + alpha 2 of the two-phase structure), the addition of Cr is prior art alloys, in particular a composition Ti50 atomic% Al48 Alloy with 2 % atomic% Cr (two-phase structure of γ + α 2 ), and also the prior art N
b-added alloy, specifically Ti 48 at.% Al
48 at% Nb4 at% alloy (γ + α 2 two-phase structure)
For, the results of carrying out the same test are also shown.
【００４１】上記「表１」に示めされる結果からも明ら
かのように、本発明の合金は比較材に比べて、室温及び
８００℃において延性を低下させることなしに著しく優
れた強度を示している。また、耐酸化性も比較材に比べ
ると著しく優れている。As is clear from the results shown in the above "Table 1", the alloy of the present invention exhibits remarkably excellent strength at room temperature and 800 ° C without lowering ductility, as compared with the comparative material. ing. Also, the oxidation resistance is remarkably superior to that of the comparative material.
【００４２】[0042]
【発明の効果】以上詳述した如く本発明によれば、高強
度で延性に富み、また耐酸化性も優れ、航空機用エンジ
ン，発電用ガスタービン等の性能を向上を図ることがで
きる等産業上極めて有用なＴｉ−Ａｌ系金属間化合物合
金を提供できる。Industrial Applicability As described in detail above, according to the present invention, it is possible to improve the performance of aircraft engines, gas turbines for power generation, etc. because of high strength, ductility, and excellent oxidation resistance. A very useful Ti-Al-based intermetallic compound alloy can be provided.
Claims (2)
４６原子％，Ｃｒ：３〜８原子％，Ｎｂ：５〜１２原子
％を含有することを特徴とするＴｉ−Ａｌ系金属間化合
物合金。1. Ti: 34 to 52 atomic%, Al: 40 to
46 at%, Cr: 3 to 8 at%, Nb: 5 to 12 at%, Ti-Al based intermetallic compound alloy.
４６原子％，Ｃｒ：３〜８原子％，Ｎｂ：５〜１２原子
％，Ｔａ：１〜４原子％を含有することを特徴とするＴ
ｉ−Ａｌ系金属間化合物合金。2. Ti: 30-51 atomic%, Al: 40-
T containing 46 atomic%, Cr: 3 to 8 atomic%, Nb: 5 to 12 atomic%, Ta: 1 to 4 atomic%.
i-Al-based intermetallic compound alloy.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP12351692A JPH05320791A (en) | 1992-05-15 | 1992-05-15 | Ti-al intermetallic compound alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP12351692A JPH05320791A (en) | 1992-05-15 | 1992-05-15 | Ti-al intermetallic compound alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH05320791A true JPH05320791A (en) | 1993-12-03 |
Family
ID=14862551
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP12351692A Pending JPH05320791A (en) | 1992-05-15 | 1992-05-15 | Ti-al intermetallic compound alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH05320791A (en) |
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1996012827A1 (en) * | 1994-10-25 | 1996-05-02 | Mitsubishi Jukogyo Kabushiki Kaisha | TiAl INTERMETALLIC COMPOUND ALLOY AND PROCESS FOR PRODUCING THE ALLOY |
| US6294132B1 (en) | 1996-10-28 | 2001-09-25 | Mitsubishi Heavy Industries Ltd. | TiAl intermetallic compound-based alloy |
| WO2003080888A1 (en) * | 2002-03-27 | 2003-10-02 | Japan Science And Technology Agency | HEAT-RESISTANT MATERIAL Ti ALLOY MATERIAL EXCELLENT IN RESISTANCE TO CORROSION AT HIGH TEMPERATURE AND TO OXIDATION |
| JP2009144247A (en) * | 2007-12-13 | 2009-07-02 | Gkss-Forschungszentrum Geesthacht Gmbh | Titanium aluminide alloy and working method thereof, and structural parts produced using the titanium aluminide alloy |
| WO2009113335A1 (en) * | 2008-03-12 | 2009-09-17 | 三菱重工業株式会社 | Tial-based alloy, process for production of the same, and rotor blade comprising the same |
| CN103710606A (en) * | 2013-12-16 | 2014-04-09 | 北京工业大学 | Novel beta-gamma TiAl intermetallic compound material containing Cr and high Nb content and preparation method of material |
| CN103820697A (en) * | 2014-03-10 | 2014-05-28 | 北京工业大学 | Multi-alloying beta-phase-solidified high Nb-TiAl alloy and preparation method thereof |
| CN103834844A (en) * | 2014-03-12 | 2014-06-04 | 北京工业大学 | V and Mn alloyed beta-phase solidified high Nb-TiAl alloy and preparation method thereof |
| CN107354344A (en) * | 2017-07-14 | 2017-11-17 | 哈尔滨工业大学 | A kind of β is single-phase to solidify TiAl-base alloy and its organizational controls method |
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1992
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Cited By (15)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1996012827A1 (en) * | 1994-10-25 | 1996-05-02 | Mitsubishi Jukogyo Kabushiki Kaisha | TiAl INTERMETALLIC COMPOUND ALLOY AND PROCESS FOR PRODUCING THE ALLOY |
| US6051084A (en) * | 1994-10-25 | 2000-04-18 | Mitsubishi Jukogyo Kabushiki Kaisha | TiAl intermetallic compound-based alloys and methods for preparing same |
| US6294132B1 (en) | 1996-10-28 | 2001-09-25 | Mitsubishi Heavy Industries Ltd. | TiAl intermetallic compound-based alloy |
| WO2003080888A1 (en) * | 2002-03-27 | 2003-10-02 | Japan Science And Technology Agency | HEAT-RESISTANT MATERIAL Ti ALLOY MATERIAL EXCELLENT IN RESISTANCE TO CORROSION AT HIGH TEMPERATURE AND TO OXIDATION |
| US7138189B2 (en) | 2002-03-27 | 2006-11-21 | Japan Science And Technology Agency | Heat-resistant Ti alloy material excellent in resistance to corrosion at high temperature and to oxidation |
| EP2075349A3 (en) * | 2007-12-13 | 2009-09-09 | Gkss-Forschungszentrum Geesthacht Gmbh | Titanium aluminide alloys |
| JP2009144247A (en) * | 2007-12-13 | 2009-07-02 | Gkss-Forschungszentrum Geesthacht Gmbh | Titanium aluminide alloy and working method thereof, and structural parts produced using the titanium aluminide alloy |
| EP2145967A3 (en) * | 2007-12-13 | 2010-04-21 | Gkss-Forschungszentrum Geesthacht Gmbh | Titanium aluminide alloys |
| EP2423341A1 (en) * | 2007-12-13 | 2012-02-29 | Helmholtz-Zentrum Geesthacht Zentrum für Material- und Küstenforschung GmbH | Titanium aluminide alloys |
| WO2009113335A1 (en) * | 2008-03-12 | 2009-09-17 | 三菱重工業株式会社 | Tial-based alloy, process for production of the same, and rotor blade comprising the same |
| CN103710606A (en) * | 2013-12-16 | 2014-04-09 | 北京工业大学 | Novel beta-gamma TiAl intermetallic compound material containing Cr and high Nb content and preparation method of material |
| CN103710606B (en) * | 2013-12-16 | 2016-07-06 | 北京工业大学 | A kind of containing Cr height Nb β-γ TiAl intermetallic compound material and preparation method thereof |
| CN103820697A (en) * | 2014-03-10 | 2014-05-28 | 北京工业大学 | Multi-alloying beta-phase-solidified high Nb-TiAl alloy and preparation method thereof |
| CN103834844A (en) * | 2014-03-12 | 2014-06-04 | 北京工业大学 | V and Mn alloyed beta-phase solidified high Nb-TiAl alloy and preparation method thereof |
| CN107354344A (en) * | 2017-07-14 | 2017-11-17 | 哈尔滨工业大学 | A kind of β is single-phase to solidify TiAl-base alloy and its organizational controls method |
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