JPS63140049A - Forming method for ti-al intermetallic compound member - Google Patents
Forming method for ti-al intermetallic compound memberInfo
- Publication number
- JPS63140049A JPS63140049A JP61288074A JP28807486A JPS63140049A JP S63140049 A JPS63140049 A JP S63140049A JP 61288074 A JP61288074 A JP 61288074A JP 28807486 A JP28807486 A JP 28807486A JP S63140049 A JPS63140049 A JP S63140049A
- Authority
- JP
- Japan
- Prior art keywords
- powder
- mixture
- intermetallic compound
- temp
- pores
- 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
- 229910021362 Ti-Al intermetallic compound Inorganic materials 0.000 title claims abstract description 8
- 238000000034 method Methods 0.000 title claims description 32
- 239000000843 powder Substances 0.000 claims abstract description 45
- 239000000203 mixture Substances 0.000 claims abstract description 17
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 13
- 239000000956 alloy Substances 0.000 claims abstract description 13
- 238000010438 heat treatment Methods 0.000 claims abstract description 8
- 229910018131 Al-Mn Inorganic materials 0.000 claims abstract description 6
- 229910018461 Al—Mn Inorganic materials 0.000 claims abstract description 6
- 229910000765 intermetallic Inorganic materials 0.000 claims description 12
- 229910004349 Ti-Al Inorganic materials 0.000 claims description 9
- 229910004692 Ti—Al Inorganic materials 0.000 claims description 9
- 238000000465 moulding Methods 0.000 claims description 4
- 239000011148 porous material Substances 0.000 abstract description 12
- 229910052782 aluminium Inorganic materials 0.000 abstract description 7
- 229910052748 manganese Inorganic materials 0.000 abstract description 4
- 238000005275 alloying Methods 0.000 abstract description 3
- 239000002775 capsule Substances 0.000 abstract description 3
- 238000005245 sintering Methods 0.000 abstract description 2
- 238000007731 hot pressing Methods 0.000 abstract 1
- 230000001105 regulatory effect Effects 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 9
- 238000007872 degassing Methods 0.000 description 7
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 7
- 239000010931 gold Substances 0.000 description 7
- 229910052737 gold Inorganic materials 0.000 description 7
- 230000006835 compression Effects 0.000 description 6
- 238000007906 compression Methods 0.000 description 6
- 238000001125 extrusion Methods 0.000 description 6
- 238000004519 manufacturing process Methods 0.000 description 6
- 238000005538 encapsulation Methods 0.000 description 4
- 238000002156 mixing Methods 0.000 description 4
- 238000004663 powder metallurgy Methods 0.000 description 4
- 229910052796 boron Inorganic materials 0.000 description 3
- 230000003647 oxidation Effects 0.000 description 3
- 238000007254 oxidation reaction Methods 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- 229910000914 Mn alloy Inorganic materials 0.000 description 2
- 229910010038 TiAl Inorganic materials 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 238000009689 gas atomisation Methods 0.000 description 2
- 239000011521 glass Substances 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 229910052758 niobium Inorganic materials 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 229910052726 zirconium Inorganic materials 0.000 description 2
- 229910000838 Al alloy Inorganic materials 0.000 description 1
- 229910021330 Ti3Al Inorganic materials 0.000 description 1
- 229910000756 V alloy Inorganic materials 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 238000009694 cold isostatic pressing Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 238000001513 hot isostatic pressing Methods 0.000 description 1
- 238000010191 image analysis Methods 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000009931 pascalization Methods 0.000 description 1
- 238000003672 processing method Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 230000001629 suppression Effects 0.000 description 1
- 238000003826 uniaxial pressing Methods 0.000 description 1
- 229910052720 vanadium Inorganic materials 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］
本発明は、粉末冶金法によるＴｉ−Ａｌ系金属間化合物
部材の成形法に関するもので、詳しくはカプセルを用い
ない熱間静水圧圧縮処理（以下、ＨＩＰ処理と称する。Detailed Description of the Invention [Industrial Field of Application] The present invention relates to a method for forming Ti-Al intermetallic compound members using a powder metallurgy method, and more specifically, a hot isostatic pressing process ( Hereinafter, this will be referred to as HIP processing.
）を施した成形法に関する。).
［従来の技術および
発明が解決しようとする問題点］
従来、Ｔｉ−Ａｌ系金属間化合物（ＴｉＡｌｉ、Ｔ ｉ
３Ａ Ｑ等）は、優れた高温強度及び耐酸化性を有す
ることが知られている。しかし、この部材は、常温およ
び高温で展延性に乏しいので、従来の加工技術では成形
することが困難であり、実用材料に供することができな
いという問題点があった。[Prior art and problems to be solved by the invention] Conventionally, Ti-Al based intermetallic compounds (TiAli, Ti
3A Q, etc.) are known to have excellent high temperature strength and oxidation resistance. However, since this member has poor malleability at room temperature and high temperature, it is difficult to mold using conventional processing techniques, and there is a problem in that it cannot be used as a practical material.
これを解決する手段として、たとえば、Ｔ ｉ ３７％
（以下、％はｆｆｌｆｉ％を示ず、）−Ａｌ合金部材を
側圧付加押出法等の特別な押出加工方法により実現しよ
とする試みがなされているが、実用化に至っていない。As a means to solve this problem, for example, T i 37%
(Hereinafter, % does not indicate ffflfi%.) Attempts have been made to realize -Al alloy members using special extrusion processing methods such as lateral pressure extrusion methods, but they have not been put to practical use.
また、他の手段として、特願昭６０−２１３３８６号に
記載されているような、粉末冶金法によるＴｉ−Ａｌ系
金属間化合物部材の成形法、およびこの改良としてガラ
スカプセルを用いた［（Ｉ Ｐ処理を利用することによ
り、Ｔｉ−Ａｌ系金属間化合物を製造する方法が本発明
者らにより提案されている、しかし、前者では成形体内
に空孔が多く発生することがあり、一方、後者では空孔
を無くずことができるが、カプセリングの工程が煩雑で
あり、また、コストアップを招く。In addition, as another means, a method of forming a Ti-Al intermetallic compound member by a powder metallurgy method, as described in Japanese Patent Application No. 60-213386, and an improvement thereof using a glass capsule [(I The present inventors have proposed a method for producing Ti-Al intermetallic compounds by using P treatment. However, the former may generate many pores in the molded body, while the latter Although the pores can be eliminated, the encapsulation process is complicated and costs increase.
本発明は、上記した先の出願発明の改良および検討の結
果なされたもので、カプセルをしなくても空孔の発生を
無くすことができるＴｉ−Ａｌ系金金属間化合物部材成
形法を提供することを目的とする。The present invention has been made as a result of improvements and studies on the above-mentioned previously filed invention, and provides a method for molding Ti-Al based gold intermetallic compound members that can eliminate the generation of pores without encapsulation. The purpose is to
し問題点を解決するための手段および作用］上記問題点
を解決するためになされた本発明は、Ａｌ１４〜６３重
斌％、Ｍ ｎ ０．１〜５重量％、残部Ｔｉの割合で、
Ａｌｌ粉末、Ａｌ−Ｍｎ合金粉末、Ｍｎ粉末のうちいず
れかを２以上選択してＴｉ粉末に混合し、またはＡｌ−
Ｍｎ合金粉末にＴｉ粉末を混合し、この混合物を密閉容
器に収納して脱気し、混合物の固相線以下の温度で加熱
焼成してＴｉ−Ａｌ系金金属間化合物形成する成形法で
あって、
５５０℃〜６５０℃までの昇温条件を、０．０１〜２０
°Ｃ／ｗｉｎに設定することを特徴とするＴｉ−Ａｌ系
金金属間化合物部材成形法を要旨とする。[Means and operations for solving the problems] The present invention, which was made to solve the above problems, has a composition in which the proportions of Al are 14 to 63% by weight, Mn is 0.1 to 5% by weight, and the balance is Ti.
Select two or more of All powder, Al-Mn alloy powder, and Mn powder and mix with Ti powder, or Al-
This is a molding method in which Ti powder is mixed with Mn alloy powder, this mixture is stored in a closed container, degassed, and heated and fired at a temperature below the solidus line of the mixture to form a Ti-Al based gold intermetallic compound. Then, the temperature increase condition from 550℃ to 650℃ was set to 0.01 to 20℃.
The gist of this article is a method for forming a Ti-Al based gold intermetallic compound member, which is characterized by setting the temperature at °C/win.
ここで、昇温速度の温度範囲は、少なくとも、５５０℃
〜６５０℃までを制９ｇする必要があるが、本発明の効
果を一層向上させるには、４５０℃〜７００℃を制御す
ることが望ましい、また、Ｍ ｎ、■、Ｚｒ、Ｂ、Ｎｂ
の１種または２種以上を以下の割合で、Ｔｉとの合金粉
末、Ａｌ−Ｍｎとの合金粉末、Ａｌとの合金粉末、ある
いはそれらの元素の単独粉末として添加して、延性効果
を付加してもよい。Here, the temperature range of the heating rate is at least 550°C
It is necessary to control the temperature up to 650°C, but in order to further improve the effects of the present invention, it is desirable to control the temperature between 450°C and 700°C.
One or more of these elements are added in the following ratios as an alloy powder with Ti, an alloy powder with Al-Mn, an alloy powder with Al, or a single powder of these elements to add a ductility effect. You can.
１≦ＭＯ≦５．１≦■≦５
１≦Ｚｒ≦５ ．０．００５≦Ｂ≦３
１≦Ｎｂ≦３０
以下、本発明の主たる工程を、第１図、さらに、その変
形例を第２図に示す。1≦MO≦5.1≦■≦5 1≦Zr≦5 . 0.005≦B≦3 1≦Nb≦30 Below, the main steps of the present invention are shown in FIG. 1, and a modified example thereof is shown in FIG.
（Ｔｉ粉末の製造工程り
第１図において、Ｔｉ粉末は、常法の粉末冶金法による
製造手段や、鋳塊等の切削で製作されたものを用いるこ
とができ、その粒度を１μｍ〜１０００μｍに調整した
ものを用いる。(Manufacturing process of Ti powder In Fig. 1, Ti powder can be manufactured by a conventional powder metallurgy method or by cutting an ingot, etc., and the particle size is set to 1 μm to 1000 μm. Use the adjusted one.
この場合、必要に応じて、Ｔｉと、Ａ１１．Ｖ、Ｎｂ、
Ｂなどの合金粉末を用いてもよい。In this case, Ti and A11. V, Nb,
An alloy powder such as B may also be used.
（Ａ１１．Ｍｎ粉末の製造工程■）
Ａｌ粉末は、常法の粉末製造法により作られ、望ましく
は、価格の点からガスアトマイズ法がよい０粒度は０．
１μｍから１０００μｍに調整する。(A11. Manufacture process of Mn powder ■) Al powder is made by a conventional powder manufacturing method, and desirably, the gas atomization method is preferable from the viewpoint of cost.
Adjust from 1 μm to 1000 μm.
Ｍｎは、Ａｌと合金化して合金粉末とするが、Ｍｎを単
独の粉末として形成する。Although Mn is alloyed with Al to form an alloy powder, Mn is formed as a single powder.
なお、必要に応じて、Ａｌと、■、Ｍｎ、Ｎｂ、Ｂなど
の合金粉末を用いてもよい。Note that alloy powders of Al, Mn, Nb, B, etc. may be used as necessary.
（混合工程■）
つぎに、Ａｌ１４〜６３％、Ｍ ｎ ０．１〜５％、残
部Ｔｉの割合になるようにＴｉ粉末、Ａｌｌ粉末、Ａｌ
−Ｍｎ合金粉末、Ｍｎ粉末を適宜選択して、混合機で混
合する。(Mixing process ■) Next, Ti powder, All powder, Al
-Mn alloy powder and Mn powder are appropriately selected and mixed in a mixer.
上記のような混合割合にするのは、Ａｌが１４％〜６３
％の範囲外では、Ｔｉ５Ａｌ、ＴｉＡｌ、およびＴ ｉ
Ａ Ｑ ３系の金属間化合物の単相あるいは２相とな
らないからであり、また、Ｍｎが０．１％以下では、カ
ーケンドル効果による空孔の発生を抑制できず、Ｍｎ５
％以上では成形体の延性を低下させるからである。The above mixing ratio is achieved when Al is 14% to 63%.
%, Ti5Al, TiAl, and T i
This is because the A Q 3 type intermetallic compound does not form a single phase or two phases. Also, if Mn is less than 0.1%, the generation of vacancies due to the Kirkendall effect cannot be suppressed, and Mn5
% or more, the ductility of the molded article decreases.
上記混合割合は、より一層強度、耐熱性、および空孔の
抑制を増大させるには、望ましくはＡｌ２５％〜４５％
、Ｍ ｎ ０．５％〜４％、Ｔｉ ５１％〜７４．５％
で、特に望ましくは、Ａｌ ３０％〜４２％、Ｍｎ１％
〜３％、Ｔｉ ５５％〜６９％である。The above mixing ratio is desirably 25% to 45% Al in order to further increase strength, heat resistance, and suppression of pores.
, Mn 0.5% to 4%, Ti 51% to 74.5%
Particularly preferably Al 30% to 42%, Mn 1%
3%, Ti 55% to 69%.
（脱気工程■）
つぎに、混合物を容器に収納して真空ポンプ等により脱
気処理を行う、これは、粉末表面の吸着ガス、吸着水を
除去するとともに、後の工程における酸化を防止するこ
とにある。この脱気後の真空状態は、後のＨＩＰ処理■
まで保持する必要がある。(Degassing process ■) Next, the mixture is stored in a container and degassed using a vacuum pump, etc. This removes adsorbed gas and water on the powder surface and prevents oxidation in the subsequent process. There is a particular thing. This vacuum state after degassing is the result of the subsequent HIP process.
need to be held until
（高温高圧処理■） つぎに、高温高圧処理としてＨＩＰ処理を行なう。(High temperature and high pressure treatment■) Next, HIP processing is performed as high temperature and high pressure processing.
ＨＩＰ処理条ｐトについては、合金化が進行する温度範
囲、すなわち、５５０〜６５０℃の温度範囲における昇
温速度を０．０１〜２０°Ｃ／＋ｓｉｎに設定し、その
後、７００℃以上で固相線以下の温度に、１０分間〜１
００時間程度保持する。For the HIP treated strip, the temperature increase rate in the temperature range where alloying progresses, that is, the temperature range of 550 to 650°C, is set to 0.01 to 20°C/+sin, and then the temperature is set at 700°C or higher. At a temperature below the phase line for 10 minutes ~ 1
Hold for about 00 hours.
このような加熱条件としたのは、上記温度範囲では、合
金化が促進されるためであり、また、昇温速度の範囲を
上記のように設定したのは、０．０１°Ｃ／■ｉｎでは
、長時間かかり、不経済であり、２０℃／ｗｉｎ以上で
は、空孔が多く発生ずるからである。The heating conditions were set in this manner because alloying is promoted in the above temperature range, and the heating rate range was set as 0.01°C/in. This is because it takes a long time and is uneconomical, and at temperatures above 20° C./win, many pores are generated.
なお、０．０１〜ｂ
囲を、４５０〜７００℃の範囲に広げることで、一層空
孔の抑制効果を促進することができる。Note that by widening the 0.01 to b range to a range of 450 to 700°C, the effect of suppressing pores can be further promoted.
また、７００℃以上で、かつ、固相線以下の温度に保持
するのは、化合物反応および焼結を促進するには、７０
０℃以上にすることが必要である一方で、液相線以上で
は、材料が溶解し、・部品としての形状が保てないから
である。In addition, maintaining the temperature at 700°C or higher and below the solidus line is necessary to promote compound reaction and sintering.
While it is necessary to keep the temperature above 0°C, if the temperature is above the liquidus line, the material will melt and the shape of the part will not be maintained.
ＨＩ Ｐ処理の圧力は、空孔を押しつぶすために、少な
くとも、２００ ｋｇｆ／ｃボに設定する。The pressure of the HIP process is set to at least 200 kgf/c to crush the pores.
上記ＨＩＰ処理で、Ｔｉ中にＡｌを拡散させることによ
りＴｉ−Ａｌ系金金属間化合物形成する。In the above HIP process, a Ti-Al based gold intermetallic compound is formed by diffusing Al into Ti.
このとき、カーケンドル効果、つまりＡｌｌの拡散によ
り空孔が発生し易い状態になるが、Ｍｎを添加し、昇温
速度を上記のように設定することにより、空孔の発生が
抑制されて、僅かに発生した空孔も高圧処理によりつぶ
される。At this time, vacancies are likely to be generated due to the Kirkendall effect, that is, diffusion of All, but by adding Mn and setting the temperature increase rate as described above, the generation of vacancies is suppressed, and only a small amount of vacancies are generated. The pores generated in the process are also crushed by high-pressure treatment.
上述したｌから■の処理工程により、ＴｉＡ（１および
Ｔ１３Ａｌｉの金属間化合物が形成されるが、このとき
、Ｔｉの割合が大きい場合に、Ｔｉ３Ａｌをマトリクス
としてＴｉＡｌが分散状態になり、一方、Ｔｉの割合が
少ない場合に逆になる。Through the treatment steps 1 to 2 described above, an intermetallic compound of TiA(1 and T13Ali) is formed. At this time, when the proportion of Ti is large, TiAl becomes dispersed with Ti3Al as a matrix; The opposite is true when the proportion of is small.
本発明の主たる工程は以上であるが、必要に応じて、第
２図に示す処理を加えてもよい。The main steps of the present invention have been described above, but the processing shown in FIG. 2 may be added if necessary.
（他の金属、合金の粉末製造工程■）
Ｔｉ−Ａｌ系金金属間化合物部材必要な添加元素、たと
えば、延性改良に効果のある、Ｍｏ、■、Ｚｒ、Ｂ、Ｎ
ｂのうち１種以上を、それらの単体または合金粉末とし
てＴｉ粉末およびＡｌ粉末と同時に混合する。(Powder production process for other metals and alloys ■) Ti-Al based gold intermetallic compound members Necessary additive elements, such as Mo, ■, Zr, B, N, which are effective in improving ductility
One or more of b are mixed together with the Ti powder and the Al powder, either alone or as an alloy powder.
このとき、各元素の添加量は、Ｍｏ１〜５％、■１〜５
％、Ｚｒ１〜５％、Ｂｏ、００５〜３％、Ｎｂ１〜３０
％、であり、いずれの元素においても下限値以下では延
性改良の効果がみちれず、上限値以上では、延性改良の
効果がほぼ飽和し、強度特性も低下する。At this time, the amount of each element added is Mo1-5%, ■1-5%
%, Zr1-5%, Bo, 005-3%, Nb1-30
%, and below the lower limit of any element, the effect of improving ductility is not noticeable, and above the upper limit, the effect of improving ductility is almost saturated, and the strength properties also deteriorate.
（圧縮工程■）
混合工程■後の混合体を冷間静水圧プレスや一軸プレス
を行い、真密度を６０％〜９５％にする。(Compression step (■)) The mixture after the mixing step (■) is subjected to cold isostatic pressing or uniaxial pressing to bring the true density to 60% to 95%.
このとき、真密度が６０％以下では、圧縮後に圧ｍ体と
しての形状が保てなく、また、９５％以上では、脱気処
理■の実効を得られない。At this time, if the true density is less than 60%, the shape of the compressed body cannot be maintained after compression, and if it is more than 95%, the degassing treatment (2) cannot be effectively achieved.
（真空封入工程■）
脱気処理■後の圧縮体を缶などの容器に真空状態で封入
する。(Vacuum Encapsulation Process ■) The compressed body after the degassing treatment ■ is sealed in a container such as a can in a vacuum state.
（繊密１ヒ処理工程■；押出）
脱気工程■後の混合体または圧縮体を常法の押出加工や
ポットプレスにて緻密化して１００％の真密度にする。(Detailed 1st processing step (■; Extrusion)) The mixture or compressed body after the degassing step (2) is densified by conventional extrusion processing or pot press to achieve 100% true density.
（Ｎｅａｒ Ｎｅｔ ５ｈａｐｅ成形工程Ｘ）緻密
化処理工程■を経た圧縮体を所望の部品形状又はそれに
近い形状に、冷間または熱間鍛造、あるいは、ｍ械加工
にて成形する。(Near Net 5hape forming process
この処理は、脱気工程■後に、所望により、粉末鍛造等
でＮｅａｒ Ｎｅｔ ５ｈａｐｅしてもよい。In this treatment, after the degassing step (1), if desired, Near Net 5hape may be performed by powder forging or the like.
（仕上成形工程ＸＩ） ’
高温、高圧処理工程ｖ後に、機械加工等により最終製品
の形状に仕上げる。(Final forming process XI) 'After the high temperature and high pressure treatment process v, the final product shape is finished by machining etc.
［発明の効果］
以上説明したように、本発明によれば、Ｔｉ−Ａｌ系金
金属間化合物部材優れた高温強度および耐酸化性を活か
すとともに、粉末冶金法により所望の形状に容易に成形
することができる。しかも、ＨＩＰ処理におけるガラス
カプセルによる封入工程を省略しても、空孔の発生を抑
制することができるので、製造を容易にすることができ
る。[Effects of the Invention] As explained above, according to the present invention, Ti-Al based gold intermetallic compound members can take advantage of their excellent high temperature strength and oxidation resistance, and can be easily formed into a desired shape by powder metallurgy. be able to. Moreover, even if the encapsulation step using a glass capsule in the HIP process is omitted, the generation of pores can be suppressed, so that manufacturing can be facilitated.
［実施例］ 以下、本発明の一実施例について説明する。[Example] An embodiment of the present invention will be described below.
まず、ハンター法による４８メツシユ以下のスポンプＴ
ｉと、アルゴンを用いたガスアトマイズ法による１００
メツシユ以下のＩｌｌ粉末、Ａｌ−Ｍｎ合金粉末、Ａｌ
−Ｖ合金粉末とを製造しＴｉ系とＡｌ系の粉末の割合を
重址分率で６４： ３６にして、■型混合機によって混
合した。この粉末を一軸プレスにて圧縮成形し、その真
密度を８０％にした。First, the spump T of 48 mesh or less by the hunter method
i and 100 by gas atomization method using argon.
Ill powder below mesh, Al-Mn alloy powder, Al
-V alloy powder was prepared, and the ratio of Ti-based powder and Al-based powder was adjusted to a weight fraction of 64:36, and mixed using a ■ type mixer. This powder was compression molded using a uniaxial press to give a true density of 80%.
つぎに、第３図に示すように、圧縮成形体１０をアルミ
ニウム製の直径６８ ｍ ｍの缶１１に装入し、缶端部
１１ａに脱気用バイブ１２を溶接した。Next, as shown in FIG. 3, the compression molded body 10 was placed in an aluminum can 11 having a diameter of 68 mm, and a degassing vibrator 12 was welded to the can end 11a.
この後、パイプ１２に真空ポンプ（図示省略）を接続し
、４５０℃で１時間加熱した状態で１Ｏ−３Ｔｏｒｒ以
下の真空度まで脱気処理を行った。Thereafter, a vacuum pump (not shown) was connected to the pipe 12, and the tube was heated at 450° C. for 1 hour to perform deaeration treatment to a degree of vacuum of 1 O −3 Torr or less.
つぎに、上記脱気用パイプ１２を圧着することにより圧
縮成形体１０を缶１１内で真空封入した。Next, the compression molded body 10 was vacuum-sealed in the can 11 by compressing the deaeration pipe 12 .
この封入後の圧縮成形体１１を押出温度４００℃、押出
比１５で押出加工を行い、直径１８ｍｍの押出棒を得た
。この押出棒は、Ｔｉ相とＡｌ１相とが混合状態にあり
、Ｔｉ−Ａｌの金属間化合物相が殆どみあたらず、また
、組織中に空洞はＩ［ｌｌ察されなかった。This encapsulated compression molded body 11 was extruded at an extrusion temperature of 400° C. and an extrusion ratio of 15 to obtain an extruded rod having a diameter of 18 mm. In this extruded rod, the Ti phase and the Al1 phase were in a mixed state, almost no Ti-Al intermetallic compound phase was observed, and no cavities were observed in the structure.
つぎに、押出棒の外周部を被覆しているアルミニウム部
材を切削除去した後に、冷却鍛造により完成品に近い形
状への成形（Ｎｅａｒ ＮｅｔＳ ｈ ａ ｐ ｅ
）を行った。Next, after cutting and removing the aluminum member covering the outer periphery of the extruded rod, it is cooled and forged into a shape close to the finished product (Near NetShape).
) was carried out.
つぎに、鍛造部材をＨＩＰ処理した。このときのＨＩＰ
処理条件として、第４図に示すようなプログラムを採用
した。Next, the forged member was subjected to HIP treatment. HIP at this time
As the processing conditions, a program as shown in FIG. 4 was adopted.
すなわち、常温〜４５０℃までを３０°Ｃ／＋ａｉｎ（
０１→Ａｌ、０２ →Ａ ２．０３ →Ａ ３、ｏ４→
Ａ４）の昇温速度で加熱し、さらに４５０°Ｃ〜７００
°Ｃまでを４つの異なった昇温速度、０．１℃／ ｌｌ
ｌ１ｎ （Ａ ｌ−”Ｂ）、４℃／ ＋ｗｉｎ （Ａ
２ →Ｂ ）、１５℃／ ｗｉｎ （Ａ ３−Ｂ）、３
０℃／ ｗｉｎ （Ａ ４ →Ｂ ）の昇温速度で加熱
し、さらに、１８００にｇｆ／ｃｒｒｆの加圧下におい
て１３００℃で２時間保持した（Ｃ→Ｄ）、次に、１３
００°Ｃから常温まで降温速度を３０°Ｃ／ｗｉｎで冷
却した（Ｄ→Ｅ）。In other words, from room temperature to 450°C at 30°C/+ain (
01 → Al, 02 → A 2.03 → A 3, o4 →
Heat at the temperature increase rate of A4) and further heat to 450°C to 700°C.
4 different heating rates up to °C, 0.1 °C/ll
l1n (A l-”B), 4℃/ +win (A
2 → B), 15℃/win (A 3-B), 3
It was heated at a temperature increase rate of 0°C/win (A 4 →B ), and further held at 1300°C for 2 hours under a pressure of 1800 gf/crrf (C → D), then 13
The temperature was lowered from 00°C to room temperature at a rate of 30°C/win (D→E).
上記した工程で、第１表に示す試料１から１２のように
、成分、昇温時間を変えて、Ｔｉ−Ａｌ系金金属間化合
物部材形成し、該部材について画像解析装置にて、空孔
率の測定を行ない、この結果を比較例ともに、第１表に
併記する。なあ、空孔率１％以下を良好（○）し、それ
以上を不良（×）として判定した。In the above steps, Ti-Al based gold intermetallic compound members were formed by changing the components and heating time as in Samples 1 to 12 shown in Table 1, and the members were analyzed using an image analysis device to form pore-filled parts. The results are listed in Table 1 together with comparative examples. Incidentally, a porosity of 1% or less was judged as good (◯), and a porosity of 1% or less was judged as bad (x).
第１表から明らかなように、Ｍｎを添加し、かつ、４０
０℃から７５０℃の昇温速度を１５℃／＋ｓｉｎ以下に
することにより、空孔率を１％以下に抑制できる。As is clear from Table 1, Mn is added and 40
By setting the temperature increase rate from 0° C. to 750° C. to 15° C./+sin or less, the porosity can be suppressed to 1% or less.
すなわち、ＴｉとＡｌとが金属間化合物を形成するに際
して、Ｍｎの添加、昇温速度の制御により、カーケンド
ル効果によって生じ易い空孔は抑制され、僅かに発生し
た空孔は、加圧により押しつぶされて観察されず、緻密
な組織となっていた。That is, when Ti and Al form an intermetallic compound, by adding Mn and controlling the temperature increase rate, vacancies that are likely to be generated due to the Kirkendall effect are suppressed, and the few vacancies that are generated are crushed by pressure. It was not observed that it had a dense structure.
上記処理により得られた製品について検査した結果、高
温強度では、室温にて、３９ｋｇｆ／−の引っ張り強さ
が得られた。As a result of testing the product obtained by the above treatment, a tensile strength of 39 kgf/- was obtained at room temperature in terms of high temperature strength.
また、第２表に示すように、Ｍｎとともに、■、Ｍｏ、
Ｚｒ、Ｂを添加することによっても、同様に空孔率を抑
制することができる。In addition, as shown in Table 2, along with Mn, ■, Mo,
Porosity can be similarly suppressed by adding Zr and B.
第１図は本発明の成形法を示す工程図、第２図は第１図
の変形例を示す工程図、第３１Ｊは本発明の一実施例に
よる工程を説明する説明図、第４図は同実施例による高
温高圧処理における加熱工程を示ず線し１である、FIG. 1 is a process diagram showing the molding method of the present invention, FIG. 2 is a process diagram showing a modification of FIG. 1, FIG. The heating process in the high temperature and high pressure treatment according to the same example is not shown and is 1.
Claims (1)
残部Ｔｉの割合で、Ａｌ粉末、Ａｌ−Ｍｎ合金粉末、Ｍ
ｎ粉末のうちいずれかを２以上選択してＴｉ粉末に混合
し、またはＡｌ−Ｍｎ合金粉末にＴｉを混合し、この混
合物を密閉容器に収納して脱気し、混合物の固相線以下
の温度で加熱焼成してＴｉ−Ａｌ系金属間化合物を形成
する成形法であって、 ５５０℃〜６５０℃までの昇温条件を、０．０１〜２０
℃／ｍｉｎに設定することを特徴とするＴｉ−Ａｌ系金
属間化合物部材の成形法。(1) Al 14-63% by weight, Mn 0.1-5% by weight,
Al powder, Al-Mn alloy powder, M
Select two or more of n powders and mix them with Ti powder, or mix Ti with Al-Mn alloy powder, store this mixture in a closed container and degas it, and make the mixture below the solidus line. A forming method in which a Ti-Al based intermetallic compound is formed by heating and baking at a temperature of 0.01 to 20
A method for forming a Ti-Al intermetallic compound member, characterized in that the molding rate is set at ℃/min.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61288074A JPH0791603B2 (en) | 1986-12-03 | 1986-12-03 | Method for forming Ti-Al intermetallic compound member |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61288074A JPH0791603B2 (en) | 1986-12-03 | 1986-12-03 | Method for forming Ti-Al intermetallic compound member |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS63140049A true JPS63140049A (en) | 1988-06-11 |
| JPH0791603B2 JPH0791603B2 (en) | 1995-10-04 |
Family
ID=17725473
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP61288074A Expired - Lifetime JPH0791603B2 (en) | 1986-12-03 | 1986-12-03 | Method for forming Ti-Al intermetallic compound member |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0791603B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR2653783A1 (en) * | 1989-10-27 | 1991-05-03 | Mtu Muenchen Gmbh | PROCESS FOR THE METALLURGY PRODUCTION OF POWDERS OF MOLDED PIECES FROM INTERMETALLIC COMPOUNDS. |
| US5370839A (en) * | 1991-07-05 | 1994-12-06 | Nippon Steel Corporation | Tial-based intermetallic compound alloys having superplasticity |
-
1986
- 1986-12-03 JP JP61288074A patent/JPH0791603B2/en not_active Expired - Lifetime
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR2653783A1 (en) * | 1989-10-27 | 1991-05-03 | Mtu Muenchen Gmbh | PROCESS FOR THE METALLURGY PRODUCTION OF POWDERS OF MOLDED PIECES FROM INTERMETALLIC COMPOUNDS. |
| US5370839A (en) * | 1991-07-05 | 1994-12-06 | Nippon Steel Corporation | Tial-based intermetallic compound alloys having superplasticity |
| US5518690A (en) * | 1991-07-05 | 1996-05-21 | Nippon Steel Corporation | Tial-based intermetallic compound alloys and processes for preparing the same |
| US5648045A (en) * | 1991-07-05 | 1997-07-15 | Nippon Steel Corporation | TiAl-based intermetallic compound alloys and processes for preparing the same |
| US5846351A (en) * | 1991-07-05 | 1998-12-08 | Nippon Steel Corporation | TiAl-based intermetallic compound alloys and processes for preparing the same |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0791603B2 (en) | 1995-10-04 |
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