JPH03199358A - Manufacture of high toughness ti-al intermetallic compound series ti alloy material - Google Patents
Manufacture of high toughness ti-al intermetallic compound series ti alloy materialInfo
- Publication number
- JPH03199358A JPH03199358A JP33938889A JP33938889A JPH03199358A JP H03199358 A JPH03199358 A JP H03199358A JP 33938889 A JP33938889 A JP 33938889A JP 33938889 A JP33938889 A JP 33938889A JP H03199358 A JPH03199358 A JP H03199358A
- Authority
- JP
- Japan
- Prior art keywords
- phase
- alloy material
- holding
- intermetallic compound
- toughness
- 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
- 239000000956 alloy Substances 0.000 title claims abstract description 32
- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 21
- 238000004519 manufacturing process Methods 0.000 title claims description 5
- 229910021362 Ti-Al intermetallic compound Inorganic materials 0.000 title 1
- 238000001816 cooling Methods 0.000 claims abstract description 11
- 239000000243 solution Substances 0.000 claims description 10
- 230000001590 oxidative effect Effects 0.000 claims description 6
- 239000006104 solid solution Substances 0.000 claims description 5
- 229910010038 TiAl Inorganic materials 0.000 claims description 3
- 239000012535 impurity Substances 0.000 claims description 2
- 230000032683 aging Effects 0.000 abstract description 10
- 229910004349 Ti-Al Inorganic materials 0.000 abstract 1
- 229910004692 Ti—Al Inorganic materials 0.000 abstract 1
- 239000007787 solid Substances 0.000 abstract 1
- 238000000034 method Methods 0.000 description 9
- 229910000765 intermetallic Inorganic materials 0.000 description 8
- 238000007796 conventional method Methods 0.000 description 6
- 238000001556 precipitation Methods 0.000 description 5
- 238000000137 annealing Methods 0.000 description 3
- 238000011160 research Methods 0.000 description 3
- 238000005452 bending Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- 229910000713 I alloy Inorganic materials 0.000 description 1
- -1 and then Substances 0.000 description 1
- 239000000919 ceramic Substances 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 238000001035 drying Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000007429 general method Methods 0.000 description 1
- 238000007654 immersion Methods 0.000 description 1
- 239000011261 inert gas Substances 0.000 description 1
- 238000009434 installation Methods 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 238000013001 point bending Methods 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 150000003839 salts Chemical class 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Landscapes
- Powder Metallurgy (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
この発明は、Ｔ ｉ Ａｊ７金属間化合物系Ｔｉ合金材
の靭性を強度の低下なく向上させる方法に関するもので
ある。DETAILED DESCRIPTION OF THE INVENTION [Industrial Application Field] The present invention relates to a method for improving the toughness of a Ti Aj7 intermetallic compound-based Ti alloy material without reducing its strength.
従来、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Ｔ ｉ Ａｌ金属間化合物系Ｔｉ合金材の適用が提案
され、種々検討されており、その中で一般的方法として
は、ＡＪ：４８原子％を含有し、残りがＴｉと不可避不
純物からなる代表組成を有するＴｉ合金材に、例えば真
空中、温度：１３００℃に３日間保持後放冷の条件で焼
鈍処理を施した状態での適用が考えられている。In the past, the application of Ti alloy materials based on TiAl intermetallic compounds to the manufacture of parts such as turbine blades and automobile turbocharger rotors that require light weight and heat resistance has been proposed, and various studies have been conducted. As a general method, a Ti alloy material having a typical composition containing 48 at. It is considered to be applied in an annealed state.
しかし、上記の従来方法で製造されたＴｉＡｌ金属間化
合物系Ｔｉ合金材は、α相（Ｔｉ固溶体相およびＴ ｉ
ａ Ａ ＩＩ固溶体相の総称）とγ相（Ｔ ｉ ＡＪ７
金属間化合物相）の層状組織をもつものの、これを構成
するγ相の厚さが平均厚さで５〜ｌＯｍと粗く、これが
原因できわめて脆く、欠は易いものであるために、実用
温度である７００℃以上の高温側では問題はないが、７
００℃以下から室温までの低温側では機械加工や研磨、
さらに運搬や組み込み、取付けなどの取り扱いなどには
細心の注意が要求されるのが現状である。However, the TiAl intermetallic compound-based Ti alloy material produced by the above conventional method has α phase (Ti solid solution phase and Ti
a Generic term for A II solid solution phase) and γ phase (T i AJ7
Although it has a layered structure of intermetallic compound phase), the thickness of the γ phase that makes up this layer is rough with an average thickness of 5 to 10m, which makes it extremely brittle and easily chipped, so it cannot be used at practical temperatures. There is no problem at high temperatures above 700℃, but
On the low temperature side from below 00℃ to room temperature, machining, polishing,
Furthermore, the current situation is that extreme care is required when handling such as transportation, assembly, and installation.
そこで、本発明者等は、上述のような観点から、上記の
Ｔ ｉ ＡＪ７金属間化合物系Ｔｊ合金材に着目し、こ
れのもつ強度を低下させることなく、靭性の向上をはか
るべく研究を行なった結果、上記の従来方性における上
記条件の焼鈍処理に代って、真空または不活性ガスなど
の非酸化性雰囲気中、１２００〜１４８０℃の範囲内の
所定温度二Ｔ℃に所定時間保持後、水冷、ガス冷却、ガ
ス強制冷却、ソルトバス浸漬などによる急冷の条件での
溶体化処理と、
これに引続いて、同じく非酸化性雰囲気中、６５０℃〜
（Ｔ”Ｃ−１００℃）の範囲内の所定温度に所定時間保
持後、同じく急冷の条件での時効処理、を施すと、上記
の溶体化処理で９５面積％以上がα相で占められた組織
となり、この溶体化処理組織に対する上記時効処理でγ
相の厚さが、従来方法で得られる層状組織におけるγ相
の厚さよりも著しく薄い層状組織となり、このような微
細な層状組織の７１合金材はすぐれた靭性を具備するよ
うになり、かつ強度も高いという研究結果を得たのであ
る。Therefore, from the above-mentioned viewpoint, the present inventors focused on the T i AJ7 intermetallic compound-based Tj alloy material and conducted research to improve its toughness without reducing its strength. As a result, instead of the annealing treatment under the above conditions in the conventional annealing process, annealing treatment was performed at a predetermined temperature within the range of 1200 to 1480 °C for a predetermined time in a non-oxidizing atmosphere such as vacuum or inert gas, and then , solution treatment under rapid cooling conditions such as water cooling, gas cooling, gas forced cooling, and salt bath immersion, followed by solution treatment at 650°C to 650°C in the same non-oxidizing atmosphere.
After holding at a predetermined temperature within the range of (T"C - 100℃) for a predetermined period of time, aging treatment under the same rapid cooling conditions was performed, and as a result of the solution treatment described above, more than 95 area% was occupied by the α phase. The above aging treatment of this solution-treated structure results in γ
The thickness of the phase is significantly thinner than the thickness of the γ phase in the layered structure obtained by conventional methods, and the 71 alloy material with such a fine layered structure has excellent toughness and strength. The research results showed that it was also high.
この発明は、上記研究結果にもとづいてなされたもので
あって、
Ａｆｆ：８８〜５０原子％。This invention was made based on the above research results, and Aff: 88 to 50 atom%.
を含有し、残りがＴｉと不可避不純物からなる７１合金
材に、
非酸化雰囲気中、１２００〜１４８０℃の範囲内の所定
温度＝Ｔ℃に所定時間保持後急冷の条件で溶体化処理を
施して、α相が９５面積％以上を占める組織とし、
ついで、同じく非酸化性雰囲気中、６５０℃〜（Ｔ ’
Ｃ−１００℃）の範囲内の所定温度に所定時間保持後、
同じく急冷の時効処理を施して、α相とγ相の層状組織
からなり、かつγ相の平均厚さを０．０２〜１ｕｍとす
ることにより、高靭性を有するＴｉＡｊＪ金属間化合物
系Ｔｉ合金材を製造する方法に特徴を有するものである
。71 alloy material, the remainder of which is Ti and unavoidable impurities, is subjected to solution treatment in a non-oxidizing atmosphere under conditions of rapid cooling after holding at a predetermined temperature in the range of 1200 to 1480 °C for a predetermined time = T °C. , α phase occupies 95% by area or more, and then heated at 650°C to (T') in the same non-oxidizing atmosphere.
After holding at a predetermined temperature within the range of C-100℃ for a predetermined time,
A TiAjJ intermetallic compound-based Ti alloy material with high toughness is produced by similarly performing a rapid cooling aging treatment and having a layered structure of α phase and γ phase, with an average thickness of γ phase of 0.02 to 1 um. It is characterized by the method of manufacturing it.
つぎに、この発明の方法において、製造条件を上記の通
りに限定した理由を説明する。Next, the reason why the manufacturing conditions are limited as described above in the method of this invention will be explained.
（ａ）７１合金材のＡｊ７含有量
その含有量が３８原子％未満では、別のＴｉ固溶体相で
あるβ相が出現するようになり、α相からなるＴｉ固溶
体相の割合を９５面積％以上にすることができず、α相
の割合が９５面積％未満では、後の時効処理工程でのγ
相の析出が不十分となり、所望の強度を確保することが
できず、一方その含有量が５０原子％を越えると、溶体
化処理で５面積％以上のγ相が現われるようになり、そ
の分だけ時効処理での微細な層状組織の形成が困難とな
って、著しい靭性向上効果が得られないことから、その
含有量を３８〜５０原子％と定めた。(a) Aj7 content of 71 alloy material When the content is less than 38 at%, another Ti solid solution phase, β phase, appears, and when the proportion of Ti solid solution phase consisting of α phase is increased to 95 area% or more. If the ratio of α phase is less than 95 area%, γ
The precipitation of the phase becomes insufficient, making it impossible to secure the desired strength. On the other hand, if the content exceeds 50 atomic %, 5 area % or more of γ phase will appear during solution treatment, and the However, since it becomes difficult to form a fine layered structure during aging treatment, and a significant toughness improvement effect cannot be obtained, the content is set at 38 to 50 at %.
（ｂ） 溶体化処理温度
その温度が１２００℃未満では、α相が９５面積％以上
を占める組織を形成することができず、この場合上記の
通り後工程の時効処理でγ相の析出が不十分となり、高
強度を得るのが困難となるものであり、一方その温度が
Ｉ４８０℃を越えると、７１合金材に部分溶融現象が発
生したり、β相が現われたりすることから、その温度を
１２００〜１４８０℃と定めた。(b) Solution treatment temperature If the temperature is less than 1200°C, a structure in which the α phase accounts for 95% or more by area cannot be formed, and in this case, as mentioned above, the subsequent aging treatment will prevent the precipitation of the γ phase. On the other hand, if the temperature exceeds 480°C, partial melting may occur in the 71 alloy material or β phase may appear, so it is difficult to obtain high strength. The temperature was set at 1200 to 1480°C.
（ｃ） 時効処理温度
その温度が６５０℃未満では、γ相の析出反応が非常に
遅く析出が不十分となって所望の高強度および高−靭性
を確保することができず、一方その温度が（Ｔ ’Ｃ−
１００℃）を越えると、γ相の析出が不十分となり高強
度および高靭性の確保は困難となることから、その温度
を６５０〜（Ｔ℃−１００℃）と定めた。(c) Aging treatment temperature If the temperature is lower than 650°C, the precipitation reaction of the γ phase is very slow and the precipitation is insufficient, making it impossible to secure the desired high strength and toughness. (T'C-
If the temperature exceeds 100°C, precipitation of the γ phase becomes insufficient and it becomes difficult to ensure high strength and toughness. Therefore, the temperature was set at 650 to (T°C - 100°C).
つぎに、この発明の方法を実施例により具体的に説明す
る。Next, the method of the present invention will be specifically explained using examples.
通常のアーク溶解炉を用い、Ａ「雰囲気中でそれぞれ第
１表に示される成分組成をもった溶湯を調製し、セラミ
ック鋳型に遠心鋳造して、断面＝１２ｍｍ Ｘ １２ｍ
ｍ、長さニア０關の寸法をもったＴｉ合金材を形威し、
ついで、これらのＴｉ合金材に、同じく第１表に示され
る条件で溶体化処理を施し、この時点で金属Ｗ４微鏡を
用いてα相の面積率を測定し、引続いて同じく第１表に
示される条件で時効処理を施すことにより本発明法１〜
５をそれぞれ実施し、ＴｉＡｊ７金属間化合物系Ｔｉ合
金材を製造した。Using a normal arc melting furnace, prepare molten metals having the compositions shown in Table 1 in an A atmosphere, and centrifugally cast them into a ceramic mold with a cross section of 12 mm x 12 m.
A Ti alloy material with dimensions of m, length near 0 is formed,
Next, these Ti alloy materials were subjected to solution treatment under the same conditions shown in Table 1, and at this point, the area ratio of the α phase was measured using a metal W4 microscope. Methods 1 to 1 of the present invention can be obtained by aging treatment under the conditions shown in
5 was carried out, respectively, to produce a TiAj7 intermetallic compound-based Ti alloy material.
また、比較の目的で、第１表に示される組成をもったＴ
ｉ合金材に、溶体化処理および１時効処理に代って、Ｉ
Ｘ １Ｏ−５Ｐａの真空中、温度： １３００℃に３
日間保持後空冷の条件での焼夕屯処理を施すことにより
従来法を実施し、同じ（Ｔ ｉ Ａｌ金属間化合物系Ｔ
ｉ合金材を製造した。Also, for comparison purposes, T
I alloy material, instead of solution treatment and 1 aging treatment, I
In a vacuum of X 1O-5Pa, temperature: 3 to 1300℃
The conventional method was carried out by carrying out a drying treatment under the condition of air cooling after holding for one day, and the same (T i Al intermetallic compound system T
An i-alloy material was manufactured.
ついで、この結果得られた各種のＴｉ合金材について、
強度を評価する目的で引張強さを測定し、また靭性を評
価する目的で、試験片寸法：１０ｍｍＸ２關Ｘ６０ｍｍ
、曲げ半径：８ｍ＋＊の条件で３点曲げ試験を行ない、
曲げ部に割れが発生した時点の曲げ角度を測定した。Next, regarding the various Ti alloy materials obtained as a result,
To measure tensile strength for the purpose of evaluating strength and for the purpose of evaluating toughness, test piece dimensions: 10 mm x 2 mm x 60 mm
, A three-point bending test was conducted under the conditions of bending radius: 8m+*,
The bending angle at the point at which a crack occurred in the bent part was measured.
さらに、上記の各種Ｔｉ合金材について、金属顕微鏡お
よび電子顕微鏡による組織観察を行ない、γ相の平均厚
さを測定した。また第１図に本発明法４で得られたＴｉ
合金材、そして第２図に従来法で得られたＴｉ合金材の
金属顕微鏡による組織写真（５００倍）を示した。以上
のＡｐｌ定結定結箱１表に示した。Furthermore, the structures of the various Ti alloy materials mentioned above were observed using a metallurgical microscope and an electron microscope, and the average thickness of the γ phase was measured. Figure 1 also shows the Ti obtained by method 4 of the present invention.
Fig. 2 shows a microstructure photograph (500x magnification) of a Ti alloy material obtained by a conventional method using a metallurgical microscope. It is shown in Table 1 of the Apl fastening box above.
第１表に示される結果から、本発明法１〜５で製造され
たＴｉ合金材は、従来法で製造されたＴｉ合金材と同等
の強度を有し、かつγ相の厚さがこれより一段と薄い微
細な層状組織をもち、このことは第１図および第２図の
金属顕微鏡による組織写真にも示されており、これによ
り一段とすぐれた靭性をもつことが明らかである。From the results shown in Table 1, the Ti alloy materials manufactured by methods 1 to 5 of the present invention have the same strength as the Ti alloy materials manufactured by the conventional method, and the thickness of the γ phase is greater than this. It has a thinner fine layered structure, which is also shown in the microstructure photographs taken with a metallurgical microscope in FIGS. 1 and 2, and it is clear that it has even better toughness.
上述のように、この発明の方法によれば、Ｔ ｆ Ａｌ
金属間化合物系Ｔｉ合金材におけるα相とγ相の層状組
織を微細化することができ、これによって靭性の著しい
向上がもたらされるので、軽量にして耐熱性が要求され
る技術分野での広範な適用を可能とするものである。As mentioned above, according to the method of the present invention, T f Al
The layered structure of α and γ phases in intermetallic Ti alloy materials can be refined, resulting in a significant improvement in toughness, making it useful in a wide range of technical fields that require light weight and heat resistance. This makes it possible to apply it.
第１図は本発明法４により製造されたＴｉ合金材の金属
顕微鏡による組織写真、第２図は従来法により製造され
たＴｉ合金材の金属顕微鏡による組織写真である。FIG. 1 is a microstructure photograph taken using a metallurgical microscope of a Ti alloy material produced by method 4 of the present invention, and FIG. 2 is a microstructure photograph taken using a metallurgical microscope of a Ti alloy material produced according to a conventional method.
Claims (1)
材に、 非酸化性雰囲気中、１２００〜１４８０℃の範囲内の所
定温度：Ｔ℃に所定時間保持後急冷の条件で溶体化処理
を施し、Ｔｉ固溶体相（α相）が９５面積％以上を占め
る組織とし、 ついで、非酸化性雰囲気中、６５０℃〜（Ｔ℃−１００
℃）の範囲内の所定温度に所定時間保持後急冷の時効処
理を施し、α相とγ相（ＴｉＡｌ相）からなり、かつγ
相の平均厚さが０．０２〜１μｍの微細な層状組織（ラ
メラー組織）とすること、を特徴とする高靭性ＴｉＡｌ
金属間化合物系Ｔｉ合金材の製造法。(1) A Ti alloy material containing Al: 38 to 50 at%, with the remainder being Ti and unavoidable impurities, in a non-oxidizing atmosphere at a predetermined temperature within the range of 1200 to 1480 °C for a predetermined time at T °C After holding, solution treatment is carried out under conditions of rapid cooling to obtain a structure in which the Ti solid solution phase (α phase) occupies 95% or more by area, and then heated at 650°C to (T°C -100°C) in a non-oxidizing atmosphere.
After holding at a predetermined temperature within the range of
High toughness TiAl characterized by having a fine layered structure (lamellar structure) with an average phase thickness of 0.02 to 1 μm
A method for producing an intermetallic Ti alloy material.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1339388A JP2687641B2 (en) | 1989-12-27 | 1989-12-27 | High toughness TiA (1) Method for producing intermetallic compound-based Ti alloy material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1339388A JP2687641B2 (en) | 1989-12-27 | 1989-12-27 | High toughness TiA (1) Method for producing intermetallic compound-based Ti alloy material |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH03199358A true JPH03199358A (en) | 1991-08-30 |
| JP2687641B2 JP2687641B2 (en) | 1997-12-08 |
Family
ID=18326999
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1339388A Expired - Lifetime JP2687641B2 (en) | 1989-12-27 | 1989-12-27 | High toughness TiA (1) Method for producing intermetallic compound-based Ti alloy material |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2687641B2 (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5540792A (en) * | 1992-05-12 | 1996-07-30 | Forschungszentrum Julich Gmbh | Components based on intermetallic phases of the system titanium-aluminum and process for producing such components |
| US5580665A (en) * | 1992-11-09 | 1996-12-03 | Nhk Spring Co., Ltd. | Article made of TI-AL intermetallic compound, and method for fabricating the same |
| US5768679A (en) * | 1992-11-09 | 1998-06-16 | Nhk Spring R & D Center Inc. | Article made of a Ti-Al intermetallic compound |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN100500907C (en) * | 2007-04-02 | 2009-06-17 | 北京科技大学 | Heat treatment process for large size as-cast high-Nb TiAl-base alloy to obtain complete lamellar structure |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH03197654A (en) * | 1989-12-25 | 1991-08-29 | Nippon Steel Corp | Method for forming finer crystal grain of titanium/ aluminum intermetallic compound |
-
1989
- 1989-12-27 JP JP1339388A patent/JP2687641B2/en not_active Expired - Lifetime
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH03197654A (en) * | 1989-12-25 | 1991-08-29 | Nippon Steel Corp | Method for forming finer crystal grain of titanium/ aluminum intermetallic compound |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5540792A (en) * | 1992-05-12 | 1996-07-30 | Forschungszentrum Julich Gmbh | Components based on intermetallic phases of the system titanium-aluminum and process for producing such components |
| US5580665A (en) * | 1992-11-09 | 1996-12-03 | Nhk Spring Co., Ltd. | Article made of TI-AL intermetallic compound, and method for fabricating the same |
| US5701575A (en) * | 1992-11-09 | 1997-12-23 | Nhk Spring Co., Ltd. | Article made of a Ti-Al intermetallic compound, and method for fabrication of same |
| US5768679A (en) * | 1992-11-09 | 1998-06-16 | Nhk Spring R & D Center Inc. | Article made of a Ti-Al intermetallic compound |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2687641B2 (en) | 1997-12-08 |
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