JPH0588294B2 - - Google Patents
Info
- Publication number
- JPH0588294B2 JPH0588294B2 JP62236609A JP23660987A JPH0588294B2 JP H0588294 B2 JPH0588294 B2 JP H0588294B2 JP 62236609 A JP62236609 A JP 62236609A JP 23660987 A JP23660987 A JP 23660987A JP H0588294 B2 JPH0588294 B2 JP H0588294B2
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- ductility
- less
- tial
- alloys
- 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.)
- Expired - Lifetime
Links
- 229910045601 alloy Inorganic materials 0.000 claims description 37
- 239000000956 alloy Substances 0.000 claims description 37
- 229910004349 Ti-Al Inorganic materials 0.000 claims description 15
- 229910004692 Ti—Al Inorganic materials 0.000 claims description 15
- 229910052759 nickel Inorganic materials 0.000 claims description 5
- 230000001105 regulatory effect Effects 0.000 claims description 5
- 239000012535 impurity Substances 0.000 claims description 4
- 229910010038 TiAl Inorganic materials 0.000 description 14
- 238000002844 melting Methods 0.000 description 8
- 230000008018 melting Effects 0.000 description 8
- 229910000765 intermetallic Inorganic materials 0.000 description 6
- 239000000203 mixture Substances 0.000 description 6
- 239000000919 ceramic Substances 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 238000005266 casting Methods 0.000 description 4
- 239000000470 constituent Substances 0.000 description 4
- 229910001069 Ti alloy Inorganic materials 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 238000000034 method Methods 0.000 description 3
- 150000001875 compounds Chemical class 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 238000005242 forging Methods 0.000 description 2
- 230000005484 gravity Effects 0.000 description 2
- 238000005495 investment casting Methods 0.000 description 2
- 229910000601 superalloy Inorganic materials 0.000 description 2
- 229910000838 Al alloy Inorganic materials 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910000883 Ti6Al4V Inorganic materials 0.000 description 1
- 229910002056 binary alloy Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000003779 heat-resistant material Substances 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 230000004043 responsiveness Effects 0.000 description 1
- 210000003625 skull Anatomy 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
Landscapes
- Turbine Rotor Nozzle Sealing (AREA)
Description
本発明は、Ti−Al系合金、とくに金属間化合
物TiAlを主要構成相とする合金の改良に関する。
The present invention relates to the improvement of Ti-Al alloys, particularly alloys containing the intermetallic compound TiAl as a main constituent phase.
たとえばタービンブレード、ターボチヤージヤ
ーのホツトホイールやエンジンバルブのように、
回転または往復運動をする部品は、高性能化すな
わち高応答性および高出力の要請にこたえるた
め、ますます軽量化される傾向がある。従つて、
これらの部品に使用する耐熱材料は、単なる強度
ではなく比強度（強度／密度）が重要視され、そ
の向上に努力が注がれている。
このような状況の中で、Ti−Al系合金、とく
に金属間化合物TiAlを主要構成相とするものが
注目されている。金属間化合物TiAlは耐用温度
（応力28.1Kgｆ／mm2の下でクリープ破断寿命1000
時間に相当する温度）が800℃であつて、常用の
Ti合金（Ti−6Al−4V）の耐用温度550℃を上回
り、しかも比重は3.8であつて、Ti合金の比重4.5
よりはセラミツクスのそれ（たとえばSi3N4は
3.2）に近く、一方でセラミツクスにはない延性
を有する上に、比強度はNi基超合金（たとえば、
Inconel−713C）のそれを上回る。
しかし、金属間化合物TiAlを主要構成相とす
るTi−Al系合金は、Ti合金やNi基合金にくらべ
て延性が低く、塑性加工が困難であるという弱点
がある。
そこで、延性を改善するための努力がなされて
いる（たとえば特開昭56−41844号は、Ｖの添加
を開示している）が、未だ実用化には至つていな
い。また、金属間化合物TiAlの融点は鋳造用の
Ni基超合金の融点（通常1250℃〜1400℃）にく
らべて高く、1500℃を超えるため、鋳造に問題が
ある。それは、従来のロストワツクス法によるセ
ラミツクス鋳型を用いた精密鋳造では、活性な
TiAlの1500℃を超える高温の溶湯とセラミツク
ス鋳型とが反応して、目的とする形状の健全な鋳
物を得ることが困難だからである。
For example, turbine blades, turbocharger hot wheels, and engine valves.
2. Description of the Related Art Parts that rotate or reciprocate are becoming increasingly lightweight in order to meet the demands for higher performance, ie, higher responsiveness and higher output. Therefore,
For the heat-resistant materials used in these parts, emphasis is placed on specific strength (strength/density) rather than mere strength, and efforts are being made to improve it. Under these circumstances, Ti--Al alloys, particularly those containing the intermetallic compound TiAl as a main constituent phase, are attracting attention. The intermetallic compound TiAl has a creep rupture life of 1000 under the operating temperature (stress of 28.1 Kgf/ mm2) .
temperature (corresponding to time) is 800℃, and the
The withstand temperature of Ti alloy (Ti-6Al-4V) is higher than 550℃, and the specific gravity is 3.8, while the specific gravity of Ti alloy is 4.5.
rather than that of ceramics (for example, Si 3 N 4 is
3.2), on the other hand, it has a ductility not found in ceramics, and its specific strength is similar to that of Ni-based superalloys (e.g.
Inconel−713C). However, Ti-Al alloys containing the intermetallic compound TiAl as a main constituent phase have a disadvantage in that they have lower ductility than Ti alloys and Ni-based alloys, and are difficult to plastically work. Therefore, efforts have been made to improve the ductility (for example, JP-A-56-41844 discloses the addition of V), but this has not yet been put to practical use. In addition, the melting point of the intermetallic compound TiAl is
This is higher than the melting point of Ni-based superalloys (usually 1250°C to 1400°C), exceeding 1500°C, which poses problems in casting. In precision casting using ceramic molds using the conventional lost wax method, active
This is because the molten TiAl at a temperature of over 1500°C reacts with the ceramic mold, making it difficult to obtain a sound casting with the desired shape.
本発明は、上記した問題のひとつの解決策を提
案するものであつて、その目的は、金属間化合物
TiAlを主要構成相とするTi−Al系合金の延性を
高めて、塑性加工を容易にするとともに、合金の
融点を下げ鋳造性を向上させた軽量耐熱合金を提
供することにある。
The present invention proposes a solution to the above-mentioned problems, and its purpose is to
The object of the present invention is to provide a lightweight, heat-resistant alloy that improves the ductility of a Ti-Al alloy having TiAl as its main constituent phase, facilitates plastic working, lowers the melting point of the alloy, and improves castability.
本発明の延性と鋳造性を改善したTi−Al系合
金は、第一の発明においては、Al：32〜38％
（重量％、以下同じ）に加えてNi：0.05〜3.0％を
含有し、残部が実質的にTiからなる合金組成を
有する。第二の発明においては、Al：32〜38％
に加えてNi：0.05〜3.0％およびSi：0.05〜3.0％
を含有し、残部が実質的にTiからなる合金組成
を有する。さらに第三の発明においては、Al：
32〜38％に加えて、Ni：0.05〜3.0％およびSi：
0.05〜3.0％の１種または２種と、Ｂ：0.005〜0.3
％とを含有し、残部が実質的にTiからなる合金
組成を有する。いずれの場合も、不純物はＣ：
0.2％以下、Ｏ：0.3％以下、Ｎ：0.2％以下に規制
することが好ましい。
本発明のTi−Al系合金から所望の機械構造部
品を製造する手段としては、鋳造はもちろん、鍛
造も採用できる。
In the first invention, the Ti-Al alloy with improved ductility and castability of the present invention has an Al content of 32 to 38%.
(wt%, the same applies hereinafter) and Ni: 0.05 to 3.0%, and has an alloy composition in which the remainder substantially consists of Ti. In the second invention, Al: 32-38%
In addition to Ni: 0.05-3.0% and Si: 0.05-3.0%
It has an alloy composition in which the remainder consists essentially of Ti. Furthermore, in the third invention, Al:
32-38% plus Ni: 0.05-3.0% and Si:
0.05-3.0% of one or two types and B: 0.005-0.3
%, with the remainder essentially consisting of Ti. In either case, the impurity is C:
It is preferable to limit the content to 0.2% or less, O: 0.3% or less, and N: 0.2% or less. As a means of manufacturing desired mechanical structural parts from the Ti-Al alloy of the present invention, not only casting but also forging can be employed.
本発明のTi−Al系合金において、上記の合金
組成を選択した理由は、つぎのとおりである。
Al：32〜38％
金属間化合物TiAl（Υ相）を与える化学量論組
成はTi36％であつて、Ti−Al二元合金におい
てTiAlが単相で存在するのは、Al：34〜40％
の範囲である。この範囲内でも、Alが38％を
超えると延性が低下して目的に反するので、こ
れを上限とする。一方、34％よりもAlが少な
いTiリツチの組成になるとTi3Al（α2相）が生
成する。この化合物は微量であれば延性の向上
に役立つもののそれ自体は脆いため、多量にな
ると脆化が起る。そこで、32％を下限にした。
Ni：0.05〜3.0％
Si：0.05〜3.0％
NiおよびSiは、TiAl相に固溶して延性を高め
る。この作用は、それぞれ0.05％から認められ
る。しかし、TiAl相に固溶できるNiおよびSi
はそれぞれ3.0％までであり、これ以上の添加
は延性の低下をもたらすため、それぞれの上限
をここに置いた。NiおよびSiはまた、合金の
融点を低下させるはたらきをする。
Ｂ：0.005〜0.3％以下
ＢはTiAlの化合物の粒界を強化し、延性を高
めるとともに結晶粒を微細化して、強度の向上
をもたらす。この効果は、0.005％という少量
の添加で得られる。一方、多量になると脆いホ
ウ化物相の生成を招いて延性が低下するので、
0.3％の上限を定めた。ＢもNiおよびSiと同様
に、合金の融点を低下させる作用がある。
Ｃ：0.2％以下
ＣはTiと炭化物TiCを形成し、合金の強度を高
めるが、一方、合金の延性を著しく低下させる
ため、その上限を0.2％に規制した。
Ｏ：0.3％以下
Ｎ：0.2％以下
ＯおよびＮはTiAlに固溶して合金の強度を高
めるが、一方で合金の延性を著しく低下させる
ため、その上限をそれぞれ0.3％および0.2％に
規制した。
The reason for selecting the above alloy composition in the Ti-Al alloy of the present invention is as follows. Al: 32~38% The stoichiometric composition that gives the intermetallic compound TiAl (Υ phase) is Ti36%, and TiAl exists as a single phase in the Ti-Al binary alloy because Al: 34~40%.
is within the range of Even within this range, if Al exceeds 38%, the ductility decreases and is contrary to the purpose, so this is set as the upper limit. On the other hand, when the Ti-rich composition becomes less than 34% Al, Ti 3 Al (α 2 phase) is formed. Although this compound is useful in improving ductility in a small amount, it is brittle in itself, so if it is in a large amount, embrittlement will occur. Therefore, the lower limit was set at 32%. Ni: 0.05-3.0% Si: 0.05-3.0% Ni and Si dissolve in the TiAl phase to improve ductility. This effect is observed starting from 0.05%. However, Ni and Si, which can be solid-solubilized in the TiAl phase,
is up to 3.0%, and since adding more than this will result in a decrease in ductility, the upper limit for each is set here. Ni and Si also serve to lower the melting point of the alloy. B: 0.005 to 0.3% or less B strengthens the grain boundaries of the TiAl compound, increases ductility, and refines crystal grains to improve strength. This effect can be obtained by adding as little as 0.005%. On the other hand, if the amount is too large, it will lead to the formation of a brittle boride phase and reduce ductility.
The upper limit was set at 0.3%. Like Ni and Si, B also has the effect of lowering the melting point of the alloy. C: 0.2% or less C forms a carbide TiC with Ti and increases the strength of the alloy, but on the other hand, it significantly reduces the ductility of the alloy, so the upper limit was regulated to 0.2%. O: 0.3% or less N: 0.2% or less O and N solidly dissolve in TiAl and increase the strength of the alloy, but on the other hand, they significantly reduce the ductility of the alloy, so the upper limits were regulated to 0.3% and 0.2%, respectively. .
表に示す組成のTi−Al系合金を溶製した。溶
解は、Arガス雰囲気中でプラズマアークを熱源
とし、水冷銅ルツボをそなえたスカル炉を用いて
実施した。No.１〜３は第一の発明、No.４および５
は第二の発明、No.６〜９は第三の発明の例であ
り、No.10および11は比較のために掲げた既知の技
術に従う例である。
合金のインゴツトから試験片を切り出して、
900℃における引張試験と示差熱分析装置による
融点（液相線および固相線）測定を行つた。結果
を表に合わせて示す。これによれば、本発明の合
金が改善された延性を有することが明らかであ
る。また、本発明の合金の融点は比較合金にくら
べて低く、No.８およびNo.９では比較合金No.10より
約50℃も低くなつている。
No.７の合金については、30％および50％の据込
み加工を行つた。その結果、アプセツト量50％に
おいても、試験片表面の割れは認められなかつ
た。
No.９およびNo.11の合金については、ロストワツ
クス法によるセラミツクス鋳型を用いて、ターボ
チヤージヤー用のホツトホイールを精密鋳造し
た。比較合金No.11を用いたホツトホイールでは、
翼部において鋳型とTiAl溶湯との反応が起つて
健全なホツトホイールを得ることができなかつた
のに対し、本発明の合金No.９を用いたホツトホイ
ールでは鋳型との反応が無く、健全なホツトホイ
ールが得られた。
A Ti-Al alloy having the composition shown in the table was produced. Melting was carried out in an Ar gas atmosphere using a skull furnace equipped with a water-cooled copper crucible and using a plasma arc as a heat source. Nos. 1 to 3 are the first invention, Nos. 4 and 5
is the second invention, Nos. 6 to 9 are examples of the third invention, and Nos. 10 and 11 are examples according to known techniques listed for comparison. Cut out a test piece from an alloy ingot,
A tensile test at 900°C and melting point (liquidus and solidus) measurements were performed using a differential thermal analyzer. The results are shown in the table. It is clear that the alloy of the present invention has improved ductility. Furthermore, the melting points of the alloys of the present invention are lower than those of comparative alloys, and those of No. 8 and No. 9 are about 50° C. lower than that of comparative alloy No. 10. For alloy No. 7, 30% and 50% upsetting was performed. As a result, no cracks were observed on the surface of the test piece even when the foreset amount was 50%. For alloys No. 9 and No. 11, hot wheels for turbochargers were precision cast using ceramic molds using the lost wax method. For hot wheels using comparative alloy No. 11,
A reaction between the mold and the TiAl molten metal occurred in the wing section, making it impossible to obtain a sound hot wheel, whereas the hot wheel using alloy No. 9 of the present invention had no reaction with the mold and was unable to obtain a sound hot wheel. A hot wheel was obtained.
【表】【table】
本発明により、高い耐熱性および比強度を有す
るTi−Al系合金の延性と鋳造性が高められ、塑
性加工および精密鋳造が容易になつた。延性の向
上は、製品の信頼性の問題を著しく軽減すること
になる。
本発明の合金を使用すれば、種々の回転または
往復運動系の機械部品、たとえば航空機用ジエツ
トエンジンや産業用ガスタービンのブレード、単
車または自動車エンジンの吸排気弁、ロツカーア
ーム、コンロツド、ターボチヤージヤーのホツト
ホイールなどが、容易に鍛造や鋳造によつて製造
できる。
According to the present invention, the ductility and castability of a Ti-Al alloy having high heat resistance and specific strength have been improved, and plastic working and precision casting have become easier. Improved ductility will significantly reduce product reliability problems. The alloy of the present invention can be used in various rotating or reciprocating mechanical parts, such as blades of aircraft jet engines and industrial gas turbines, intake and exhaust valves of motorcycle or automobile engines, rocker arms, connecting rods, and turbochargers. Yar hot wheels can be easily manufactured by forging or casting.
Claims (1)
有し、残部が実質的にTiからなる延性および鋳
造性を改善したTi−Al系合金。 ２ 不純物を、Ｃ：0.2％以下、Ｏ：0.3％以下、
Ｎ：0.2％以下に規制した特許請求の範囲第１項
のTi−Al系合金。 ３ Al：32〜38％に加えてNi：0.05〜3.0％およ
ひSi：0.05〜3.0％を含有し、残部が実質的にTi
からなる延性および鋳造性を改善したTi−Al系
合金。 ４ 不純物を、Ｃ：0.2％以下、Ｏ：0.3％以下、
Ｎ：0.2％以下に規制した特許請求の範囲第３項
のTi−Al系合金。 ５ Al：32〜38％に加えて、Ni：0.05〜3.0％お
よひSi：0.05〜3.0％の１種または２種と、Ｂ：
0.005〜0.3％とを含有し、残部が実質的にTiから
なる延性および鋳造性を改善したTi−Al系合金。 ６ 不純物を、Ｃ：0.2％以下、Ｏ：0.3％以下、
Ｎ：0.2％以下に規制した特許請求の範囲第５項
のTi−Al系合金。[Claims] 1. A Ti-Al alloy containing 0.05-3.0% Ni in addition to 32-38% Al, with the remainder being substantially Ti, with improved ductility and castability. 2 Impurities: C: 0.2% or less, O: 0.3% or less,
N: Ti-Al alloy according to claim 1, which is regulated to 0.2% or less. 3 In addition to Al: 32-38%, it contains Ni: 0.05-3.0% and Si: 0.05-3.0%, with the remainder being substantially Ti.
A Ti-Al alloy with improved ductility and castability. 4 Impurities: C: 0.2% or less, O: 0.3% or less,
N: Ti-Al alloy according to claim 3, which is regulated to 0.2% or less. 5 In addition to Al: 32-38%, one or two of Ni: 0.05-3.0% and Si: 0.05-3.0%, and B:
A Ti-Al alloy containing 0.005 to 0.3% of Ti, the remainder being substantially Ti, with improved ductility and castability. 6 Impurities: C: 0.2% or less, O: 0.3% or less,
N: The Ti-Al alloy according to claim 5, which is regulated to 0.2% or less.
Priority Applications (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP23660987A JPS6479335A (en) | 1987-09-20 | 1987-09-20 | Ti-al alloy |
| US07/120,070 US4849168A (en) | 1986-11-12 | 1987-11-12 | Ti-Al intermetallics containing boron for enhanced ductility |
| EP87116728A EP0275391B1 (en) | 1986-11-12 | 1987-11-12 | Titanium-aluminium alloy |
| DE8787116728T DE3781394T2 (en) | 1986-11-12 | 1987-11-12 | TITAN ALUMINUM ALLOY. |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP23660987A JPS6479335A (en) | 1987-09-20 | 1987-09-20 | Ti-al alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS6479335A JPS6479335A (en) | 1989-03-24 |
| JPH0588294B2 true JPH0588294B2 (en) | 1993-12-21 |
Family
ID=17003177
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP23660987A Granted JPS6479335A (en) | 1986-11-12 | 1987-09-20 | Ti-al alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6479335A (en) |
Families Citing this family (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0261017A (en) * | 1988-08-27 | 1990-03-01 | Yakichirou Shiozaki | Titanium-aluminum alloy |
| JPH0818151B2 (en) | 1988-11-11 | 1996-02-28 | 大同特殊鋼株式会社 | Joining method and joining part of Ti-Al alloy and structural steel |
| US5045406A (en) * | 1989-06-29 | 1991-09-03 | General Electric Company | Gamma titanium aluminum alloys modified by chromium and silicon and method of preparation |
| US5252150A (en) * | 1990-05-18 | 1993-10-12 | Toyota Jidosha Kabushiki Kaishi | Process for producing nitrogen containing Ti--Al alloy |
| WO2015119927A1 (en) * | 2014-02-05 | 2015-08-13 | Borgwarner Inc. | TiAl ALLOY, IN PARTICULAR FOR TURBOCHARGER APPLICATIONS, TURBOCHARGER COMPONENT, TURBOCHARGER AND METHOD FOR PRODUCING THE TiAl ALLOY |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CA621884A (en) * | 1961-06-13 | I. Jaffee Robert | Titanium-high aluminum alloys | |
| JPS63111152A (en) * | 1986-10-30 | 1988-05-16 | Natl Res Inst For Metals | Si-added intermetallic compound tia1-base heat-resisting alloy |
-
1987
- 1987-09-20 JP JP23660987A patent/JPS6479335A/en active Granted
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CA621884A (en) * | 1961-06-13 | I. Jaffee Robert | Titanium-high aluminum alloys | |
| JPS63111152A (en) * | 1986-10-30 | 1988-05-16 | Natl Res Inst For Metals | Si-added intermetallic compound tia1-base heat-resisting alloy |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS6479335A (en) | 1989-03-24 |
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