JP3225252B2 - Method for producing particle-dispersed sintered titanium-based composite material - Google Patents
Method for producing particle-dispersed sintered titanium-based composite materialInfo
- Publication number
- JP3225252B2 JP3225252B2 JP04265992A JP4265992A JP3225252B2 JP 3225252 B2 JP3225252 B2 JP 3225252B2 JP 04265992 A JP04265992 A JP 04265992A JP 4265992 A JP4265992 A JP 4265992A JP 3225252 B2 JP3225252 B2 JP 3225252B2
- Authority
- JP
- Japan
- Prior art keywords
- powder
- composite material
- titanium
- alloy
- matrix
- 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
- 239000010936 titanium Substances 0.000 title claims description 38
- 239000002131 composite material Substances 0.000 title claims description 36
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 title claims description 24
- 229910052719 titanium Inorganic materials 0.000 title claims description 15
- 238000004519 manufacturing process Methods 0.000 title claims description 12
- 239000000843 powder Substances 0.000 claims description 56
- 239000011159 matrix material Substances 0.000 claims description 30
- 238000000034 method Methods 0.000 claims description 27
- 229910045601 alloy Inorganic materials 0.000 claims description 25
- 239000000956 alloy Substances 0.000 claims description 25
- 229910001069 Ti alloy Inorganic materials 0.000 claims description 18
- 239000002245 particle Substances 0.000 claims description 17
- 239000000203 mixture Substances 0.000 claims description 11
- 238000006243 chemical reaction Methods 0.000 claims description 8
- 238000005245 sintering Methods 0.000 claims description 8
- 229910018084 Al-Fe Inorganic materials 0.000 claims description 4
- 229910018192 Al—Fe Inorganic materials 0.000 claims description 4
- 239000006185 dispersion Substances 0.000 claims description 2
- MTPVUVINMAGMJL-UHFFFAOYSA-N trimethyl(1,1,2,2,2-pentafluoroethyl)silane Chemical compound C[Si](C)(C)C(F)(F)C(F)(F)F MTPVUVINMAGMJL-UHFFFAOYSA-N 0.000 description 18
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 12
- 239000000463 material Substances 0.000 description 8
- 239000000919 ceramic Substances 0.000 description 7
- 229910052796 boron Inorganic materials 0.000 description 6
- 238000002156 mixing Methods 0.000 description 6
- 229910052782 aluminium Inorganic materials 0.000 description 5
- 150000001875 compounds Chemical class 0.000 description 5
- 229910052742 iron Inorganic materials 0.000 description 5
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 4
- 229910052799 carbon Inorganic materials 0.000 description 4
- 239000002994 raw material Substances 0.000 description 4
- 229910000599 Cr alloy Inorganic materials 0.000 description 3
- 229910000883 Ti6Al4V Inorganic materials 0.000 description 3
- 238000001513 hot isostatic pressing Methods 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000011812 mixed powder Substances 0.000 description 3
- 238000004663 powder metallurgy Methods 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 238000009694 cold isostatic pressing Methods 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 239000012467 final product Substances 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 239000012535 impurity Substances 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 239000007769 metal material Substances 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 230000003014 reinforcing effect Effects 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 229910000838 Al alloy Inorganic materials 0.000 description 1
- 229910000521 B alloy Inorganic materials 0.000 description 1
- 235000017166 Bambusa arundinacea Nutrition 0.000 description 1
- 235000017491 Bambusa tulda Nutrition 0.000 description 1
- 241001330002 Bambuseae Species 0.000 description 1
- 229910000640 Fe alloy Inorganic materials 0.000 description 1
- 235000015334 Phyllostachys viridis Nutrition 0.000 description 1
- 229910000756 V alloy Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 239000011425 bamboo Substances 0.000 description 1
- 238000013329 compounding Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 239000011261 inert gas Substances 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 239000004570 mortar (masonry) Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 238000010298 pulverizing process Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
Landscapes
- Powder Metallurgy (AREA)
Description
【０００１】[0001]
【産業上の利用分野】この発明は、高温での機械的性質
に優れ、航空、宇宙用機器等に使用されるチタン基焼結
材料、具体的には炭化チタン（TiＣ）または硼化チタン
（TiＢ）の粒子が分散したTi基焼結複合材料、の製造方
法に関する。BACKGROUND OF THE INVENTION The present invention relates to a titanium-based sintered material having excellent mechanical properties at high temperatures and used for aviation and space equipment, specifically, titanium carbide (TiC) or titanium boride ( The present invention relates to a method for producing a Ti-based sintered composite material in which particles of TiB) are dispersed.
【０００２】[0002]
【従来の技術】Ti−６Al−４Ｖ合金に代表されるチタン
合金は、軽量で比強度が高く、航空、宇宙機器用の材料
として既に広く実用化されている。しかし、従来のチタ
ン合金の耐用温度は高々600 ℃までで、ニッケル基耐熱
合金等に較べて使用可能温度域が狭い。例えば、高性能
の航空機用ガスタービンエンジン、あるいは宇宙往還機
のような超高速飛翔体に用いるには、600 ℃を超えて10
00℃程度までの使用に耐える軽量高強度材料が必要とさ
れるが、従来のチタン合金ではこのような要請には応え
られない。2. Description of the Related Art Titanium alloys represented by Ti-6Al-4V alloys are lightweight and have high specific strength, and have already been widely used as materials for aviation and space equipment. However, the service temperature of conventional titanium alloys is up to 600 ° C. at most, and the usable temperature range is narrower than that of nickel-base heat-resistant alloys. For example, for use in high-performance aircraft gas turbine engines or ultra-high-speed vehicles such as spacecraft, temperatures above 600 ° C
A lightweight and high-strength material that can withstand use up to about 00 ° C. is required, but conventional titanium alloys cannot meet such demands.
【０００３】金属材料の高温強度を高める手法の一つ
に、微細化合物の析出を利用する析出強化があり、鉄合
金やアルミニウム合金では盛んに利用されている。しか
し、チタン合金ではこの析出強化の効果は期待できな
い。それは、Tiと化合物を形成するFe、Co、Ni等の元素
のチタン中での拡散速度がきわめて大きいため、析出物
が粗大化してしまうからである。One of the techniques for increasing the high-temperature strength of a metal material is precipitation strengthening utilizing precipitation of a fine compound, and is widely used in iron alloys and aluminum alloys. However, this effect of precipitation strengthening cannot be expected with titanium alloys. This is because the diffusion rate of elements such as Fe, Co, and Ni, which form a compound with Ti, in titanium is extremely high, and the precipitates are coarsened.
【０００４】チタン合金の強化法としては、溶融チタン
合金と強化粒子（TiＣ、TiＢ等のセラミックス粒子) と
を混ぜ合わせて複合材料とする技術も考えられる。しか
し、この方法では、チタンがあまりにも活性な金属であ
るために合金 (マトリックス) と強化相 (セラミックス
粒子) との界面に生成する粗い反応相や凝固偏析による
不均一性が問題となる。As a method of strengthening a titanium alloy, a technique of mixing a molten titanium alloy with reinforcing particles (ceramic particles such as TiC and TiB) to form a composite material is also conceivable. However, in this method, since titanium is a too active metal, there is a problem of a coarse reaction phase generated at the interface between the alloy (matrix) and the reinforcing phase (ceramic particles) and non-uniformity due to solidification segregation.
【０００５】さらに、チタン合金粉末にセラミック粒子
を直接混合して焼結する粉末冶金法もあるが、均一混合
の困難さや合金マトリックスとセラミック粒子との密着
性の悪さが機械的性質に影響し、実用に耐える材料の製
造は困難である。[0005] Furthermore, there is a powder metallurgy method in which ceramic particles are directly mixed with titanium alloy powder and then sintered. However, difficulties in uniform mixing and poor adhesion between the alloy matrix and the ceramic particles affect mechanical properties. It is difficult to produce a material that can withstand practical use.
【０００６】[0006]
【発明が解決しようとする課題】本発明は、軽量で比強
度が高いチタン合金をベースとして、セラミック粒子を
分散させた高温強度の高い複合金属材料を製造すること
を課題としてなされたもので、その具体的な目的は、前
記のように種々の問題のある溶解法または直接混合の粉
末冶金法に代わる新しい製造方法を提供することにあ
る。SUMMARY OF THE INVENTION The object of the present invention is to produce a composite metal material having high strength at high temperatures in which ceramic particles are dispersed, based on a titanium alloy which is lightweight and has high specific strength. A specific object of the present invention is to provide a new production method which can replace the problematic melting method or the direct mixing powder metallurgy method as described above.
【０００７】[0007]
【課題を解決するための手段】本発明の要旨は、下記
(1)および(2) の製造方法にある。The gist of the present invention is as follows.
The manufacturing method of (1) and (2).
【０００８】(1)チタンの粉末、母合金粉末としてのAl
３ Ti粉末ならびにCr ３ Ｃ ２ 、Cr ７ Ｃ ３ およびCr ２３ Ｃ ６
のいずれか１種以上の粉末を混合して圧粉体とし、これ
を焼結して内部反応によりTiＣをチタン合金マトリック
ス中に生成させることを特徴とする粒子分散型Ti−Al−
Cr系焼結チタン基複合材料の製造方法。(1) Titanium powder, Al as mother alloy powder
3 Ti powder and Cr 3 C 2 , Cr 7 C 3 and Cr 23 C 6
A particle-dispersed Ti-Al- powder, characterized by mixing one or more powders into a green compact, sintering it, and generating TiC in a titanium alloy matrix by an internal reaction.
A method for producing a Cr-based sintered titanium-based composite material.
【０００９】(2)チタンの粉末、母合金粉末としてのAl
３ Ti粉末ならびにFeＢおよびFe ２ Ｂのいずれか１種以上
の粉末またはこれらとＢ（ボロン）の混合粉末を混合し
て圧粉体とし、これを焼結して内部反応によりTiＢをチ
タン合金マトリックス中に生成させることを特徴とする
粒子分散型Ti−Al−Fe系チタン基焼結複合材料の製造方
法。(2) Al as titanium powder and mother alloy powder
3 Ti powder and any one or more of Fe B and Fe 2 B
Or a mixed powder of B (boron) and a powder thereof , and sintering the compact to form TiB in a titanium alloy matrix by an internal reaction. -A method for producing a Fe-based titanium-based sintered composite material.
【００１０】まず、上記(1) の製造方法について説明す
る。First, the manufacturing method (1) will be described.
【００１１】この方法によって製造される複合材料は、
Ti−Al−Cr合金のマトリックスに、焼結工程で析出した
TiＣが微細に分散したものである。この場合のTiＣの含
有量は１〜15重量％ (以下、重量％を単に％と記す) で
あるのが望ましい。１％より少ないと強度向上の効果が
得られず、15％を超えると複合材料の靱性が低下する。The composite material produced by this method comprises:
Precipitated in the sintering process on the matrix of Ti-Al-Cr alloy
TiC is finely dispersed. In this case, the content of TiC is desirably 1 to 15% by weight (hereinafter, the weight% is simply referred to as%). If it is less than 1%, the effect of improving the strength cannot be obtained, and if it exceeds 15%, the toughness of the composite material decreases.
【００１２】炭素含有物質としては、Cr ３ Ｃ ２ 、Cr７Ｃ
３およびCr２３Ｃ６の粉末の１種または２種以上を用
い、また、母合金としてはAl３Ti粉末を用いるのが望ま
しい。これらの粉末の配合量を調整することによって、
最終製品である複合材料のTiＣの含有量、ならびにマト
リックスのチタン合金のAlおよびCrの含有量を目標の範
囲に収めることができる。As the carbon-containing substance , Cr 3 C 2 , Cr 7 C
It is desirable to use one or more of powders of 3 and Cr 23 C 6 , and to use Al 3 Ti powder as a master alloy. By adjusting the amount of these powders,
The content of TiC in the final composite material and the content of Al and Cr in the titanium alloy of the matrix can be within target ranges.
【００１３】なお、使用する粉末の大きさは、チタン粉
末で 100メッシュアンダー、炭素含有粉末で 200メッシ
ュアンダー、Al3Ti 粉末で 100メッシュアンダー程度が
適当である。The size of the powder used is suitably about 100 mesh under for titanium powder, about 200 mesh under for carbon-containing powder, and about 100 mesh under for Al 3 Ti powder.
【００１４】製品の複合材料のマトリックスとなるチタ
ン合金のAl含有量は 1〜10％、Cr含有量は１〜20％とす
るのがよい。AlおよびCrが１％未満の合金では十分な機
械的強度が得られない。一方、Alが10％、Crが20％をそ
れぞれ超えると、脆いAl化合物やCr化合物が生成しマト
リックスの靱性が低下する。It is preferable that the titanium content, which is the matrix of the composite material of the product, has an Al content of 1 to 10% and a Cr content of 1 to 20%. If the alloy contains less than 1% of Al and Cr, sufficient mechanical strength cannot be obtained. On the other hand, when Al exceeds 10% and Cr exceeds 20%, brittle Al compounds and Cr compounds are formed, and the toughness of the matrix decreases.
【００１５】次に前記(2) の製造方法について説明す
る。Next, the manufacturing method (2) will be described.
【００１６】この方法で得られるのは、Ti−Al−Fe合金
のマトリックスにTiＢが析出分散した複合材料である。
この場合、TiＢの含有量も、前記TiＣと同じ理由で１〜
15％とするのが望ましい。A composite material obtained by this method is one in which TiB is precipitated and dispersed in a matrix of a Ti—Al—Fe alloy.
In this case, the content of TiB is also 1 to
It is desirable to be 15%.
【００１７】(2) の製造方法では、Ｂ含有粉末としてFe
Ｂおよび Fe2Ｂの１種以上の粉末またはこれらとＢ（ボ
ロン）粉末の混合粉末を使用し、また、母合金粉末とし
ては前記の Al3Ti粉末を用いるのがよい。これの粉末の
配合量を調整することによって、最終製品である複合材
料のTiＢの含有量、ならびにマトリックスのチタン合金
のAlおよびFeの含有量を目標の範囲に収めるようにす
る。なお、使用する粉末の大きさは、Ｂ含有粉末を 200
メッシュアンダー程度とする外、前記(1) の製法の場合
と同じ程度でよい。In the production method (2), Fe is used as the B-containing powder.
It is preferable to use one or more powders of B and Fe 2 B or a mixed powder of these and B (boron) powder, and to use the above-mentioned Al 3 Ti powder as the mother alloy powder. By adjusting the amount of the powder, the content of TiB in the composite material as the final product and the content of Al and Fe in the titanium alloy of the matrix are kept within the target ranges. The size of the powder used is 200 B for the B-containing powder.
In addition to the mesh under level, the same level as in the case of the production method (1) may be used.
【００１８】製品の複合材料のマトリックスとなるチタ
ン合金のAl含有量は、この場合も１〜10％とし、Feの含
有量は 1〜15％とするのがよい。それぞれ 1％未満では
マトリックスの強度が十分でなく、Feが15％を超えると
脆いFe化合物が生成する。In this case, the Al content of the titanium alloy serving as the matrix of the composite material of the product is preferably 1 to 10%, and the Fe content is preferably 1 to 15%. If each is less than 1%, the strength of the matrix is not sufficient, and if Fe exceeds 15%, brittle Fe compounds are formed.
【００１９】上記(1) および(2) のいずれの方法でも、
まず、チタンの粉末と母合金粉末、および炭素含有粉末
またはボロン含有粉末を、最終製品 (複合材料) の目標
組成に合わせて配合し混合した後、例えば冷間静水圧プ
レス（ＣＩＰ）法により、所定の形状にプレス成形して
圧粉体を作製し、これを真空中あるいは不活性ガス雰囲
気中において焼結する。焼結の条件としては、温度1000
〜1300℃程度で 1〜４時間程度保持するのがよい。この
焼結の過程で、チタン粉末、母合金粉末、および炭素含
有粉末またはボロン含有粉末が相互に反応し、チタン合
金のマトリックスにTiＣまたはTiＢが析出して均一微細
に分散した複合材料が得られる。In any of the above methods (1) and (2),
First, a titanium powder, a mother alloy powder, and a carbon-containing powder or a boron-containing powder are blended and mixed according to a target composition of a final product (composite material), and then, for example, by a cold isostatic press (CIP) method. A green compact is produced by press molding into a predetermined shape, and this is sintered in a vacuum or in an inert gas atmosphere. The sintering conditions are temperature 1000
It is preferable to maintain the temperature at about 1300 ° C. for about 1 to 4 hours. During the sintering process, the titanium powder, the master alloy powder, and the carbon-containing powder or the boron-containing powder react with each other, and TiC or TiB precipitates in the titanium alloy matrix to obtain a uniformly finely dispersed composite material. .
【００２０】複合材料の強度、延性、靱性等の機械的性
質を更に上げるために、焼結した後に熱間静水圧プレス
（ＨＩＰ）で処理して、さらに高密度化させるのが望ま
しい。In order to further increase the mechanical properties such as the strength, ductility, and toughness of the composite material, it is desirable that the material be sintered and then subjected to a hot isostatic pressing (HIP) to further increase the density.
【００２１】[0021]
【作用】本発明方法は、溶解法ではなく粉末冶金法によ
り、しかも、セラミック粒子を直接混合する方法ではな
く、内部反応で生成させることによって微細に析出分散
させることを特徴とする。この方法により、均一でマト
リックスとセラミック粒子の密着性に優れたチタン基複
合材料が得られる。The method of the present invention is characterized in that the particles are finely precipitated and dispersed by a powder metallurgy method instead of a melting method, and by an internal reaction rather than a method of directly mixing ceramic particles. According to this method, a titanium-based composite material having uniformity and excellent adhesion between the matrix and the ceramic particles can be obtained.
【００２２】Al3Tiの母合金粉末を使用して(1) の方法
により複合材料を製造する場合には、焼結の際に、 Ti
＋ Al3Ti＋(Cr3C2, Cr7C3, Cr23C6)が、Ti−Al−Cr合金
のマトリックスと、TiＣの析出分散粒子に変化する。従
って、使用する粉末原料の化学組成を考慮し、その配合
量を調整すれば、任意のマトリックス組成とTiＣの分散
量をもつ複合材料が製造できる。When a composite material is manufactured by the method of (1) using the Al 3 Ti master alloy powder, Ti
+ Al 3 Ti + (Cr 3 C 2 , Cr 7 C 3 , Cr 23 C 6 ) changes into a matrix of a Ti—Al—Cr alloy and precipitation-dispersed particles of TiC. Therefore, a composite material having an arbitrary matrix composition and a dispersed amount of TiC can be manufactured by adjusting the compounding amount in consideration of the chemical composition of the used powder raw material.
【００２３】このようにして得られる複合材料では、Al
はマトリックスの強度を向上させ、Crはβ相を安定化さ
せてTiＣ粒子とマトリックスとの密着性を向上させる。
析出したTiＣは、機械的に混合したTiＣと比較してマト
リックスとの密着性がきわめて優れているから、本発明
の複合材料は高温域まで優れた機械的特性を示す。In the composite material thus obtained, Al
Improves the strength of the matrix, and Cr stabilizes the β phase to improve the adhesion between the TiC particles and the matrix.
Since the deposited TiC has extremely excellent adhesion to the matrix as compared with the mechanically mixed TiC, the composite material of the present invention exhibits excellent mechanical properties up to a high temperature range.
【００２４】この複合材料は、種々の用途に使用できる
が、その使用目的に応じてマトリックス組成と粒子分散
量を選定すればよい。特に、600 ℃を超えるような高温
での使用が予想される場合には、前述のようにマトリッ
クスが１〜10％のAlと 1〜20％のCrを含有し、残部がTi
および不可避不純物からなるTi基合金であって、TiＣが
1〜15％分散したものとするのが望ましい。The composite material can be used for various applications, and the matrix composition and the amount of dispersed particles may be selected according to the purpose of use. In particular, when use at a high temperature exceeding 600 ° C. is expected, as described above, the matrix contains 1 to 10% of Al and 1 to 20% of Cr, and the balance is Ti.
And Ti-based alloy consisting of unavoidable impurities,
It is desirable to have 1 to 15% dispersion.
【００２５】(2) の方法の場合には、FeＢおよび Fe2Ｂ
の１種以上、あるいはこれらとＢの混合粉末を用いるの
で、分散粒子がTiＢになるが、その生成原理は (1)の方
法の場合と同じである。この場合、母合金粉末として A
l3Tiの粉末を使用すれば、マトリックスはTi−Al−Fe合
金となる。このマトリックスをAl含有量が 1〜10％、Fe
含有量が 1〜15％で、残部がTiと不可避不純物からなる
合金とし、析出分散するTiＢの含有量を 1〜15％とすれ
ば、高温強度の高い複合材料となる。In the case of the method (2), FeB and Fe 2 B
Or a mixed powder of these and B is used, so that the dispersed particles become TiB, but the generation principle is the same as in the case of the method (1). In this case, A
Using powder of l 3 Ti, matrix becomes Ti-Al-Fe alloy. This matrix contains 1-10% Al, Fe
If the content is 1 to 15% and the balance is an alloy consisting of Ti and unavoidable impurities, and the content of TiB precipitated and dispersed is 1 to 15%, a composite material with high high-temperature strength is obtained.
【００２６】[0026]
【実施例１】チタン粉末、 Al3Tiの母合金粉末および C
r3C2粉末を原料として、Ti−Al−Cr合金マトリックスに
TiＣが析出分散した複合材料を製造した。Example 1 Titanium powder, Al 3 Ti mother alloy powder and C
r 3 C 2 powder as raw material to form Ti-Al-Cr alloy matrix
A composite material in which TiC was precipitated and dispersed was manufactured.
【００２７】Al3Ti 母合金粉末は、小板状アルミニウム
とスポンジチタンを Al3Tiの組成になるように配合し、
アーク溶解して50mmφ×10mm厚のボタンインゴットを作
製し、これを乳鉢で 150メッシュ以下に粉砕して用い
た。The Al 3 Ti mother alloy powder is obtained by mixing platelet-like aluminum and sponge titanium so as to have a composition of Al 3 Ti,
An arc was melted to produce a button ingot having a diameter of 50 mmφ × 10 mm, which was crushed with a mortar to 150 mesh or less and used.
【００２８】チタン粉末は市販の 100メッシュアンダー
の粉末、Cr3C2 も同じく市販の 280メッシュアンダーの
粉末を使用した。The titanium powder used was a commercially available powder of 100 mesh under, and the Cr 3 C 2 was also a commercially available powder of 280 mesh under.
【００２９】上記の粉末を、最終組成がTi−５％Al−13
％Cr−10％TiＣの組成となるように、即ち、Ti粉末：10
31ｇ、Al3Ti 粉末： 108ｇ、 Cr3C2粉末：200 ｇを配合
し、混合した後、冷間静水圧プレス（ＣＩＰ）により成
形して圧粉体とし、10-6torr以下の真空度で1573Ｋ×４
hrの真空焼結を行った。その後、さらに高密度化させる
ために1203Ｋで３hrのＨＩＰ処理を行った。The above powder was mixed with a final composition of Ti-5% Al-13.
% Cr-10% TiC, that is, Ti powder: 10%
31 g, Al 3 Ti powder: 108 g, Cr 3 C 2 powder: 200 g were blended and mixed, and then molded by cold isostatic pressing (CIP) to obtain a green compact, and a degree of vacuum of 10 -6 torr or less 1573K × 4
hr vacuum sintering. Then, HIP processing was performed at 1203 K for 3 hours to further increase the density.
【００３０】図１に示すのは、上記の方法で得られた複
合材料のミクロ組織である。図示のように反応生成した
TiＣ (図中の10μm 程度の粒子) が微細に、かつ均一に
分散している。FIG. 1 shows the microstructure of the composite material obtained by the above method. Reaction generated as shown
TiC (particles of about 10 μm in the figure) are finely and uniformly dispersed.
【００３１】表１に、上記実施例で製造した複合材料の
室温におけるヤング率と 773Ｋにおける引張強さを、溶
解法で製造したセラミック粒子を含まないTi−６Al−４
Ｖ合金のそれらと比較して示す。Ti−６Al−４Ｖ合金と
比較して、室温におけるヤング率は25％も向上し、ま
た、 773Ｋにおける引張強さも著しく高い値を示してい
る。Table 1 shows the Young's modulus at room temperature and the tensile strength at 773 K of the composite material manufactured in the above example.
Shown in comparison with those of the V alloy. Compared with the Ti-6Al-4V alloy, the Young's modulus at room temperature is improved by 25%, and the tensile strength at 773K also shows a remarkably high value.
【００３２】[0032]
【実施例２】チタン粉末、 Al3Tiの母合金粉末、および
FeＢとＢとからなる粉末を原料として、Ti−Al−Fe合金
マトリックスにTiＢが析出分散した複合材料を製造し
た。Example 2 Titanium powder, Al 3 Ti mother alloy powder, and
Using a powder composed of FeB and B as a raw material, a composite material in which TiB was precipitated and dispersed in a Ti-Al-Fe alloy matrix was manufactured.
【００３３】使用したチタン粉末と Al3Tiの母合金粉末
は、実施例１で用いたものと同じである。FeＢは、アー
ク溶解したFe−48％Ｂ合金を 350メッシュアンダーに粉
砕した粉末である。The used titanium powder and Al 3 Ti mother alloy powder are the same as those used in Example 1. FeB is a powder obtained by pulverizing an arc-melted Fe-48% B alloy into a 350 mesh under.
【００３４】上記の原料粉を、最終組成がTi−５％Al−
2.5％Fe−６％TiＢの組成になるように、即ち、Ti粉
末： 673ｇ、Al3Ti 粉末：62ｇ、Fe−Ｂ粉末：44ｇを配
合し、混合した後、冷間静水圧プレス（ＣＩＰ）により
成形して圧粉体とし、10-6torr以下の真空度で1573Ｋ×
４hrの真空焼結を行った。その後、さらに高密度化させ
るために1203Ｋで３hrのＨＩＰ処理を施した。The above-mentioned raw material powder was prepared by adding a final composition of Ti-5% Al-
A composition of 2.5% Fe-6% TiB, that is, 673 g of Ti powder, 62 g of Al 3 Ti powder and 44 g of Fe-B powder are blended and mixed, and then cold isostatic pressing (CIP). Into a green compact with a vacuum of 10 -6 torr or less at 1573K ×
Vacuum sintering was performed for 4 hours. Thereafter, in order to further increase the density, HIP treatment was performed at 1203 K for 3 hours.
【００３５】図２に、上記の方法で得られた複合材料の
ミクロ組織を示す。図中の笹の葉状の析出物が反応生成
したTiＢで、マトリックスに均一に分散していることが
わかる。表１に、実施例２で製造した複合材料の室温に
おけるヤング率と 773Ｋにおける引張強さを併記する。
この材料もTi−６Al−４Ｖ合金と比較して、室温でのヤ
ング率が約50％向上し、773 Ｋにおける引張強さも高
い。FIG. 2 shows the microstructure of the composite material obtained by the above method. It can be seen that bamboo leaf-like precipitates in the figure are TiB produced by the reaction and are uniformly dispersed in the matrix. Table 1 also shows the Young's modulus at room temperature and the tensile strength at 773 K of the composite material produced in Example 2.
This material also has about a 50% improvement in Young's modulus at room temperature and a higher tensile strength at 773 K as compared to the Ti-6Al-4V alloy.
【００３６】[0036]
【表１】 [Table 1]
【００３７】[0037]
【発明の効果】本発明の方法によれば、マトリックスと
の密着性に優れたTiＣまたはTiＢの析出粒子が微細に分
散したチタン基複合材料が製造できる。この材料は、軽
量で比強度が高く、既存のチタン合金が使用できない高
温域でも優れた機械的性質を維持できるから、航空機用
ガスタービンエンジン部材、自動車排気系部材等に広く
使用できる。According to the method of the present invention, a titanium-based composite material having finely dispersed TiC or TiB precipitated particles having excellent adhesion to a matrix can be produced. This material is lightweight, has high specific strength, and can maintain excellent mechanical properties even in a high temperature region where existing titanium alloys cannot be used, and thus can be widely used for aircraft gas turbine engine members, automobile exhaust system members, and the like.
【図１】本発明方法によって製造したTi−５％Al−13％
Cr−10％TiＣの組成の複合材料のミクロ組織を示す図で
ある。FIG. 1 Ti-5% Al-13% produced by the method of the present invention
It is a figure which shows the microstructure of the composite material of a composition of Cr-10% TiC.
【図２】本発明方法によって製造したTi−５％Al− 2.5
％Fe−６％TiＢの組成の複合材料のミクロ組織を示す図
である。FIG. 2 shows Ti-5% Al-2.5 produced by the method of the present invention.
FIG. 3 is a diagram showing a microstructure of a composite material having a composition of% Fe-6% TiB.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 江村 聡 茨城県つくば市千現１丁目２番１号科学 技術庁金属材料技術研究所筑波支所内 (72)発明者 河部 義邦 茨城県つくば市千現１丁目２番１号科学 技術庁金属材料技術研究所筑波支所内 (72)発明者 海江田 義也 東京都目黒区中目黒２丁目３番12号科学 技術庁金属材料技術研究所内 (56)参考文献 特開 平５−5142（ＪＰ，Ａ) 特開 平３−229837（ＪＰ，Ａ) 特開 平４−247845（ＪＰ，Ａ) 特開 平３−193842（ＪＰ，Ａ) (58)調査した分野(Int.Cl.7，ＤＢ名) B22F 3/10 B22F 1/00 C22C 1/05 ──────────────────────────────────────────────────続 き Continuing on the front page (72) Inventor Satoshi Emura 1-2-1, Sengen, Tsukuba, Ibaraki Pref., National Institute of Metals and Materials Tsukuba Branch, Science and Technology Agency (72) Inventor Yoshikuni Kawabe 1 Sengen, Tsukuba, Ibaraki Tsukuba Branch, National Institute for Metals Sciences, National Research Institute of Science and Technology (Chome 2-1) (72) Inventor Yoshiya Kaieda 2-3-12, Nakameguro, Meguro, Tokyo, Japan JP-A-5-5142 (JP, A) JP-A-3-229837 (JP, A) JP-A-4-247845 (JP, A) JP-A-3-193842 (JP, A) (58) Fields investigated (Int .Cl. 7 , DB name) B22F 3/10 B22F 1/00 C22C 1/05
Claims (3)
粉末ならびにCr ３ Ｃ ２ 、Cr ７ Ｃ ３ およびCr ２３ Ｃ ６ のい
ずれか１種以上の粉末を混合して圧粉体とし、これを焼
結して内部反応によりTiＣをチタン合金マトリックス中
に生成させることを特徴とする粒子分散型Ti−Al−Cr系
焼結チタン基複合材料の製造方法。1. Al 3 Ti as a titanium powder and a mother alloy powder
Powder and Cr 3 C 2, Cr 7 C 3 and Cr 23 C 6 Neu
A particle-dispersed Ti-Al-Cr-based sintering characterized in that one or more powders are mixed to form a green compact, which is sintered and TiC is generated in a titanium alloy matrix by an internal reaction. A method for producing a titanium-based composite material.
粉末ならびにFeＢおよびFe ２ Ｂのいずれか１種以上の粉
末またはこれらとＢ粉末の混合粉末を混合して圧粉体と
し、これを焼結して内部反応によりTiＢをチタン合金マ
トリックス中に生成させることを特徴とする粒子分散型
Ti−Al−Fe系焼結チタン基複合材料の製造方法。2. Al 3 Ti as a titanium powder and a mother alloy powder
Powder and powder of one or more of FeB and Fe 2 B
Powder or a mixture of B powder and B powder to form a green compact, which is sintered and TiB is generated in a titanium alloy matrix by an internal reaction, and is a particle dispersion type.
A method for producing a Ti-Al-Fe-based sintered titanium-based composite material.
ン合金中のAlが１〜10重量％である請求項１または２に
記載の複合材料の製造方法。3. The process for producing a composite material according to claim 1 or 2 Al titanium alloy matrix of the produced composite material is 1-10 wt%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP04265992A JP3225252B2 (en) | 1992-02-28 | 1992-02-28 | Method for producing particle-dispersed sintered titanium-based composite material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP04265992A JP3225252B2 (en) | 1992-02-28 | 1992-02-28 | Method for producing particle-dispersed sintered titanium-based composite material |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH05239507A JPH05239507A (en) | 1993-09-17 |
| JP3225252B2 true JP3225252B2 (en) | 2001-11-05 |
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ID=12642144
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|---|---|---|---|
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| JP3354468B2 (en) * | 1997-12-12 | 2002-12-09 | 住友チタニウム株式会社 | Method for producing particle-dispersed sintered titanium matrix composite |
| CN113182520B (en) * | 2021-03-31 | 2022-09-02 | 北京科技大学 | Titanium product with titanium carbide reinforced titanium-based composite material hardened layer and preparation method |
| CN117802341A (en) * | 2024-01-10 | 2024-04-02 | 重庆理工大学 | Inner and outer double-layer coupling reinforced TiAl-based composite material and preparation method thereof |
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|---|---|
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