JPH01287243A - Ti-al intermetallic compound containing mn and nb and its manufacture - Google Patents
Ti-al intermetallic compound containing mn and nb and its manufactureInfo
- Publication number
- JPH01287243A JPH01287243A JP11624588A JP11624588A JPH01287243A JP H01287243 A JPH01287243 A JP H01287243A JP 11624588 A JP11624588 A JP 11624588A JP 11624588 A JP11624588 A JP 11624588A JP H01287243 A JPH01287243 A JP H01287243A
- Authority
- JP
- Japan
- Prior art keywords
- intermetallic compound
- temperature
- oxidation resistance
- annealing
- compound
- 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.)
- Pending
Links
- 229910021362 Ti-Al intermetallic compound Inorganic materials 0.000 title claims abstract description 13
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 6
- 230000003647 oxidation Effects 0.000 claims abstract description 15
- 238000007254 oxidation reaction Methods 0.000 claims abstract description 15
- 238000000137 annealing Methods 0.000 claims abstract description 11
- 239000011261 inert gas Substances 0.000 claims abstract description 6
- 238000002844 melting Methods 0.000 claims abstract description 6
- 230000008018 melting Effects 0.000 claims abstract description 6
- 239000013078 crystal Substances 0.000 claims abstract description 4
- 238000000034 method Methods 0.000 claims abstract description 3
- 239000011159 matrix material Substances 0.000 claims description 8
- 239000000463 material Substances 0.000 claims description 7
- 229910000765 intermetallic Inorganic materials 0.000 abstract description 17
- 150000001875 compounds Chemical class 0.000 abstract description 3
- 239000007789 gas Substances 0.000 abstract description 3
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 10
- 239000010931 gold Substances 0.000 description 10
- 229910052737 gold Inorganic materials 0.000 description 10
- 229910010038 TiAl Inorganic materials 0.000 description 6
- 238000005204 segregation Methods 0.000 description 4
- 238000004458 analytical method Methods 0.000 description 3
- 238000004453 electron probe microanalysis Methods 0.000 description 3
- 238000010438 heat treatment Methods 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 230000003068 static effect Effects 0.000 description 2
- 229910000831 Steel Inorganic materials 0.000 description 1
- 229910004349 Ti-Al Inorganic materials 0.000 description 1
- 229910004692 Ti—Al Inorganic materials 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- 230000004913 activation Effects 0.000 description 1
- 235000021028 berry Nutrition 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 238000012669 compression test Methods 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000009760 electrical discharge machining Methods 0.000 description 1
- 238000001493 electron microscopy Methods 0.000 description 1
- 230000008030 elimination Effects 0.000 description 1
- 238000003379 elimination reaction Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000000855 fermentation Methods 0.000 description 1
- 230000004151 fermentation Effects 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 239000001307 helium Substances 0.000 description 1
- 229910052734 helium Inorganic materials 0.000 description 1
- 238000011065 in-situ storage Methods 0.000 description 1
- 239000003562 lightweight material Substances 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 238000000879 optical micrograph Methods 0.000 description 1
- 238000010587 phase diagram Methods 0.000 description 1
- 238000010248 power generation Methods 0.000 description 1
- 230000001376 precipitating effect Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000000926 separation method Methods 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 230000004584 weight gain Effects 0.000 description 1
- 235000019786 weight gain Nutrition 0.000 description 1
Landscapes
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は高温耐熱強度材（航空機用タービンエンジン、
発電用ガスクーヒン、自動車用エンジン、高速回転体）
に用いるのに適したＴｉ−ｆＶ系金金属間化合物常温延
性、高温耐酸化性を向上したＭｎ、Ｎｂ添加Ｔｉ−Ａｌ
系金属間化合物及びその製造方法に関するものである。[Detailed Description of the Invention] [Industrial Application Field] The present invention relates to high-temperature heat-resistant strength materials (aircraft turbine engines,
(Gaskuhin for power generation, automobile engines, high-speed rotating bodies)
Ti-fV gold intermetallic compound suitable for use in Mn and Nb-added Ti-Al with improved room temperature ductility and high temperature oxidation resistance
This invention relates to intermetallic compounds and their production methods.
〔従来の技術］
Ｔｉ−Ａｌ系金属間化合物は、金属材料としては、はぼ
最高の高温比強度を持ち、しかも耐食性が高く、軽推の
材料である。Ｍｃｔａｌｌｕｒｇｉｃａｌ Ｔｒａｎｓ
−ａｃｔｉｏｎ、Ｖｏｌ、 ６八（１，９７５） ｐ、
１９９１にば、８００℃で４０ｋｇ／−の高温強度が得
られたことが報告されている。そこで、これらの特性を
利用してＴｉ−Ａｌ系金属間化合物はガスクーヒン部品
、自動車用エンジンのバルブ、ピストンへの適用、高温
用タイスや軸受部品などへの適用が好適と考えられてき
た。[Prior Art] Ti-Al intermetallic compounds have the highest high-temperature specific strength among metal materials, have high corrosion resistance, and are lightweight materials. Mctallurgical Trans
-action, Vol. 68 (1,975) p.
In 1991, it was reported that a high temperature strength of 40 kg/- was obtained at 800°C. Therefore, by utilizing these properties, it has been thought that Ti-Al intermetallic compounds are suitable for application to gasket parts, automobile engine valves, pistons, high-temperature ties, bearing parts, and the like.
Ｔｉ−ＡＩＩ系金属間化合物は状態図」二である組成幅
をもちＴ＋４０〜５０原子％、Δ１６０〜５０原子％で
熱平衡状態においてＬｌ、型構造（基本的には面心正方
構造であるが（００１）方向にＴｉの層、ＡＩの層が交
互に並ぶ構造）の単一相となる。このため単結晶状態で
は温度の上昇と共に強度が増加する異常強化現象が発見
されている。そして多結晶体では高温でも強度が低下し
ないことが知られている。しかしながらＴｉ−へｌ系金
属間化合物の欠点は常温から７００℃付近まで延性が低
いことであり室温で圧縮率が０．４％、７００℃で１．
１％程度であった。Ti-AII intermetallic compounds have a composition range in phase diagram 2, with T + 40 to 50 atomic % and Δ 160 to 50 atomic %, in a thermal equilibrium state, they have an Ll type structure (basically a face-centered square structure, but ( It becomes a single phase structure in which Ti layers and AI layers are arranged alternately in the 001) direction. For this reason, an abnormal strengthening phenomenon has been discovered in which the strength increases with increasing temperature in the single crystal state. It is known that polycrystalline materials do not lose their strength even at high temperatures. However, the drawback of Ti-Helium intermetallic compounds is that their ductility is low from room temperature to around 700°C, with a compressibility of 0.4% at room temperature and 1.5% at 700°C.
It was about 1%.
実用材料としてのＴｉ−Ａｌ系金属間化合物の開発上の
困難は常温延性を如何に確保するかであったがＭｎ添加
が効果があることが発見されている（特開昭６２−２１
５号公報）。しかし、Ｍｎ添加には高温耐酸化性が劣化
するという欠点がある（部具ら、日本金属学会シンポジ
ウム−規則合金・金属間化合物の塑性変形−１９８６年
７月１６日、ｐ１３）ことが報告されている。The difficulty in developing Ti-Al intermetallic compounds as practical materials was how to ensure room-temperature ductility, but it was discovered that adding Mn was effective (Japanese Patent Laid-Open No. 62-21
Publication No. 5). However, it has been reported that Mn addition has the disadvantage of deteriorating high-temperature oxidation resistance (Buppu et al., Japan Institute of Metals Symposium - Plastic Deformation of Ordered Alloys and Intermetallic Compounds - July 16, 1986, p. 13). ing.
Ｔｉ−Ａｌ系金属間化合物は、軽量で、耐熱温度が高く
、耐食性も高いため、高温で使用するタービンブレード
などに好適であるが、常温での延性が小さい（圧縮率０
．４％）ため、圧延、鍛造などによる成形が困難であり
、さらに常温での安全面における信頼性に劣り、実用化
が阻まれていた。本発明はこれらの問題点を克服した高
温耐熱強度材であるＴｉ−Ａｌ系金属間化合物を開発す
ることを課題とする。Ti-Al intermetallic compounds are lightweight, have a high heat resistance, and have high corrosion resistance, so they are suitable for turbine blades used at high temperatures, but they have low ductility at room temperature (compressibility of 0).
．． 4%), making it difficult to form by rolling, forging, etc., and also having poor reliability in terms of safety at room temperature, hindering its practical application. An object of the present invention is to develop a Ti-Al intermetallic compound which is a high-temperature heat-resistant and strong material that overcomes these problems.
本発明は上記の問題点を解決するＴｉ４０〜５０原子％
、Ａｌ６０〜５０原子％にＭｎ１〜４原子％、Ｎｂ０．
１〜２原子％を含有する結晶構造がＬｌ。型規則構造の
高温耐酸化性に富み、常温延性が高く、なおかつ高温強
度を失わないＴｉ−＃Ｊ系金金属間化合物提供するもの
である。The present invention solves the above problems by using Ti40 to 50 atomic %.
, Al60-50 at%, Mn1-4 at%, Nb0.
The crystal structure containing 1 to 2 atomic % is Ll. The present invention provides a Ti-#J-based gold intermetallic compound having a regular structure, excellent in high-temperature oxidation resistance, high room-temperature ductility, and not losing high-temperature strength.
また本発明は不活性ガス雰囲気中でＴｉ４０〜５０原子
％、Ａｌ６０〜５０原子％にＭｎ１〜４原子％、ＮｂＯ
，１〜２原子％を含有させたものを溶融、凝固した後、
規則化焼鈍を行って作製することを特徴とするＭｎ、
Ｎｂ添加Ｔｉ−ｋｌ系金属間化合物材料の製造方法を提
供するものである。In addition, the present invention provides 40 to 50 atomic % of Ti, 60 to 50 atomic % of Al, 1 to 4 atomic % of Mn, and 1 to 4 atomic % of NbO in an inert gas atmosphere.
, after melting and solidifying the material containing 1 to 2 atom%,
Mn characterized by being produced by performing regularization annealing,
A method for manufacturing an Nb-added Ti-kl intermetallic compound material is provided.
Ｔｉ量を４０〜５０原子％の範囲としたのはＴｉ −Ａ
ｌ系金属間化合物の単一相の組成域がこの幅をもってい
るためで、この組成であれば他の相を析出させずに均一
化焼鈍により、Ｔｉ−ＩＶ系金金属間化合物単相で得る
ことができるからである。The reason why the amount of Ti was set in the range of 40 to 50 at% was because Ti-A
This is because the composition range of a single phase of the I-IV series gold intermetallic compound has this width.With this composition, a single phase of the Ti-IV series gold intermetallic compound can be obtained by homogenizing annealing without precipitating other phases. This is because it is possible.
１〜４原子％Ｍｎ、０．１〜２原子％Ｎｂが存在すると
これによって積層欠陥エネルギーを低下させ双晶変形機
構を活発にして常温延性を向上させると共に、Ｔｉ酵化
物の成長を止めて高温耐酸化性を向上させる。The presence of 1 to 4 atom% Mn and 0.1 to 2 atom% Nb lowers the stacking fault energy and activates the twin deformation mechanism to improve room-temperature ductility, and also stops the growth of Ti fermentation products and improves high-temperature ductility. Improves oxidation resistance.
こうして作製したＭｎ、 Ｎｂを含有するＴｉ−ＩＶ系
金金属間化合物常温で３０％近くの、また８００℃で４
０％近くの圧縮率を示し、Ｔｉ−Ａｌ系金属間化合物の
問題点である常温から７００℃付近の低延性を改善した
ものである。The Ti-IV gold intermetallic compound containing Mn and Nb produced in this way has a concentration of nearly 30% at room temperature and 4% at 800°C.
It exhibits a compressibility of nearly 0% and improves the low ductility from room temperature to around 700°C, which is a problem with Ti-Al intermetallic compounds.
本発明のＭｎ、 Ｎｂ添加Ｔｉ−Ａｌ系金属間化合物の
製造方法はＴｉ４０〜５０原子％、ＩＶ６０〜５０原子
％にＭｎ１〜４原子％、Ｎｂ０．１〜２原子％を添加し
たものを一旦真空（１０””ｔｏｒｒ以上）にしＡｒガ
ス雰囲気に置換した環境下で１４００℃〜１５００℃に
加熱し、溶融凝固した後、規則化のため、前記と同様の
不活性ガス雰囲気中において規則化焼鈍を行う。The method for producing the Mn and Nb-added Ti-Al intermetallic compound of the present invention is to add 1 to 4 at% of Mn and 0.1 to 2 at% of Nb to 40 to 50 at% of Ti and 60 to 50 at% of IV, and then vacuum (more than 10" torr) and heated to 1400 to 1500 °C in an Ar gas atmosphere to melt and solidify, and then undergo ordering annealing in the same inert gas atmosphere as above for ordering. conduct.
これはＬｌ、型構造を得るためにはＴｉとＡＩを高温で
拡散させねばならないからである。規則化焼鈍の際の温
度としては８００℃以上でＴｉ−／Ｖ系金金属間化合物
融点以下の単一相域であれば目的を達することができる
が、この中でも９００〜１１００’Ｃの温度範囲が望ま
しい。また、加熱時間としては、規則化のための原子拡
散に時間が必要であるため高温では短時間となるが、完
全に規則化させるためには２４時間以上とすることが望
ましい。得られたＭｎ、Ｎｂ添加Ｔｉ−ＩＶ系金金属間
化合物規則化していることはＸ線デイフラクトメーター
により、各ピークがＴｉ−ＩＶ系金金属間化合物Ｌｌ。This is because Ti and AI must be diffused at high temperatures in order to obtain the Ll type structure. The purpose can be achieved as long as the temperature during ordering annealing is in a single phase range of 800°C or higher and below the melting point of the Ti-/V-based gold intermetallic compound, but within this range, temperatures in the range of 900 to 1100'C are suitable. is desirable. Further, the heating time is short at high temperatures because time is required for atomic diffusion for ordering, but it is desirable to set it to 24 hours or more in order to achieve complete ordering. The obtained Mn and Nb-added Ti-IV gold intermetallic compound was found to be ordered by an X-ray diffractometer, and each peak was found to be Ti-IV gold intermetallic compound Ll.
型構造に相当することを確認すればよい。Just make sure that it corresponds to the type structure.
次に本発明のＭｎ、 Ｎｂ添加Ｔｉ−へｌ系金属間化合
物で常温延性が向上する理由について説明する。Next, the reason why the room-temperature ductility is improved by the Mn- and Nb-added Ti-heli-based intermetallic compound of the present invention will be explained.
Ｍｎ、 Ｎｂ添加により、Ｔｉ−Ａｌ系金属間化合物の
積層欠陥エネルギーが低下するものと考えられる。It is thought that the addition of Mn and Nb lowers the stacking fault energy of the Ti-Al intermetallic compound.
それは変形機構において双晶変形、とくに交叉双晶が活
発になることにより電子顕微鏡観察、超高圧電子顕微鏡
内その場観察等で確かめられている。This has been confirmed by electron microscopy observation and in-situ observation inside an ultra-high-voltage electron microscope, due to the activation of twinning deformation, especially cross twinning, in the deformation mechanism.
発明者らは本合金について電子顕微鏡によるコントラス
ト実験により塑性変形進行中においてこの交叉双晶は双
晶境界上に転位をｐｉｌｅ−ｕｐさせずに逆に転位反応
によりずベリ転位を形成し延性能を高めていることを確
認している。The inventors conducted a contrast experiment using an electron microscope on this alloy and found that during the progress of plastic deformation, these crossed twins do not pile up dislocations on the twin boundaries, but conversely form Berri dislocations without causing a dislocation reaction, improving ductility. I have confirmed that it is increasing.
一例として３種類の試料ＴｉＡ／、、ＴｉＡｌ−４ａｔ
％Ｍｎ。As an example, three types of samples TiA/, TiAl-4at
%Mn.
ＴｉＡＪ ２ａｔ％Ｍｎ−１ａｔ％Ｎｂの均−化焼鈍
後の光学顕微鏡組織写真を第１図に示す。Ｍｎ、 Ｎｂ
の併用添加により、双晶の発生が活発になっていること
が見られる。FIG. 1 shows an optical micrograph of the structure of TiAJ 2at%Mn-1at%Nb after equalization annealing. Mn, Nb
It can be seen that the generation of twins becomes more active due to the combined addition of .
次にＮｂ、 Ｍｎの併用添加により高温耐酸化性が向上
する理由について述べる。第２図に静的空気中にて８０
０℃に保持した３種類の試料ＴｉＡｌ、ＴｉＡｌ−４ａ
む％Ｍｎ、、ＴｉＡｌ−２ａｔ％Ｍｎ−ｆａｔ％Ｎｂの
酸化増量変化、第３図にこれらの試料において８００℃
３２００時間保持によってできた酸化膜のＥＰＭＡ分析
結果を示す。第２図からＭｎ添加によって耐酸化性が劣
化するがＭｎ、 Ｎｂの併用添加において耐酸化性が向
上することが示される。Next, we will discuss the reason why high temperature oxidation resistance is improved by the combined addition of Nb and Mn. Figure 2 shows 80° in static air.
Three types of samples TiAl and TiAl-4a kept at 0°C
%Mn, , TiAl-2at%Mn-fat%Nb.
The EPMA analysis results of the oxide film formed by holding for 3200 hours are shown. FIG. 2 shows that the oxidation resistance deteriorates with the addition of Mn, but the oxidation resistance improves with the combined addition of Mn and Nb.
第３図の各ＥＰＭＡ分析結果において右はじの破線より
右側が７１〜リツクスであり、左側が酸化物にあたる。In each EPMA analysis result in FIG. 3, the right side of the dashed line on the right side corresponds to 71~lix, and the left side corresponds to the oxide.
まず、ＴｉＡｌの場合はマトリックスに続いて酸化層と
のクラックと思われる部分が見られ、さらに続いてＴｉ
酸化物域、へｌ酸化物とＴｉ酸化物の共存域、最後に再
びＴｉ酸化物のみの領域となっている。つまりＴｉ酸化
物がマトリックス側と外表面側に分かれ、その中心にＩ
ＶＶ化物とＴｉ酸化物の共存域があるのが特徴である。First, in the case of TiAl, we can see what appears to be a crack with the oxide layer following the matrix, and then
There is an oxide region, a region where Hel oxide and Ti oxide coexist, and finally a region where only Ti oxide exists again. In other words, the Ti oxide is divided into the matrix side and the outer surface side, and the I
It is characterized by a coexistence region of VV compound and Ti oxide.
これに対し、ＴｉＡｌ−４ａｔ％Ｍｎではマトリックス
に続き、Ｍｎの偏析域があり、それに続く層はＴ ｉ
ｋｌの場合と同じＴｉ酸化物域、へ！酸化物とＴｉ酸化
物の共存域、Ｔｉ酸化物域となっている。この結果より
Ｍｎ添加ＴｉＡｌにおいて高温耐酸化性が劣化する理由
として、Ｍｎのマトリックスと酸化膜との境界における
偏析が酸化膜とマトリックスの密着性を劣化させている
ことが考えられる。On the other hand, in TiAl-4at%Mn, there is a Mn segregation region following the matrix, and the subsequent layer is Ti
The same Ti oxide region as in the case of kl, to! This is a coexistence region of oxide and Ti oxide, and a Ti oxide region. From this result, it is considered that the reason why high-temperature oxidation resistance deteriorates in Mn-doped TiAl is that segregation of Mn at the boundary between the matrix and the oxide film deteriorates the adhesion between the oxide film and the matrix.
Ｍｎ、 Ｎｂ併用添加Ｔｉ八へでばＴｉ１Ｖ−４ａｔ％
Ｍｎの場合に見られたマトリックスと酸化膜との境界に
おけるＭｎの偏析が見られず、最外表面においてＭｎが
出ているのが特徴である。またＴｉ−ｒｉｃｈの酸化物
とＡｆ−ｒｉｃｈの酸化物との分離が起こっており、Ｎ
ｂはＴｉ−ｒｉｃｈ酸化物側に現われている。この様に
、Ｍｎのマトリックス近傍の偏析が無くなったことが高
温耐酸化性向上の要因であると推定される。If Mn and Nb are added together, Ti1V-4at%
The characteristic is that the segregation of Mn at the boundary between the matrix and the oxide film, which was observed in the case of Mn, is not observed, and Mn is exposed at the outermost surface. Also, separation between Ti-rich oxide and Af-rich oxide occurs, and N
b appears on the Ti-rich oxide side. Thus, it is presumed that the elimination of Mn segregation near the matrix is a factor in the improvement in high-temperature oxidation resistance.
（実施例〕 次に本発明の実施例を示す。(Example〕 Next, examples of the present invention will be shown.
純度９９．８ｗｔ％のスポンジＴｉ４９．１ａｔ％（６
２，０ｗｔ％）、純度９９．９９ ｗｔ％のＡＪ４９．
１ａｔ％（３４，９ｗｔ％）にＭｎ１．４ａｔ％（２ｗ
ｔ％） 、ＮｂＯ，４ａｔ％（１ｗｔ％）を添加したち
のを真空溶解炉を用い、−旦真空（１０−’ｔｏｒｒ以
上）にし、Ａｒガス雰囲気に置換した環境下で１５００
℃に加熱し、溶融凝固した後、規則化のため、前記と同
様の不活性ガス雰囲気中において規則化焼鈍を行った。Sponge Ti 49.1 at% (6
2.0 wt%), purity 99.99 wt% AJ49.
1at% (34.9wt%) and Mn1.4at% (2w
t%), NbO, 4at% (1wt%) was added using a vacuum melting furnace, the temperature was reduced to a vacuum (10-'torr or more), and the atmosphere was replaced with an Ar gas atmosphere at 1500 °C.
After heating to 0.degree. C. to melt and solidify, ordering annealing was performed in the same inert gas atmosphere as described above for ordering.
規則化焼鈍の際の温度としては８００℃以上でＴ ｉ
−ＩＶ系金金属間化合物融点以下の単一相域であれば目
的を達することができるが、この中でも１０００℃の温
度範囲を用いた。また、加熱時間としては、完全に規則
化させるために７２時間とした。得られたＭｎ、Ｎｂ添
加ＴｉＡｌ試料が規則化していることはＸ線デイフラク
トメーターにより、各ピークがＴｉＡｌ試料のＬｌ。型
構造に相当することを確認した。The temperature during ordering annealing is 800°C or higher.
Although the objective can be achieved in a single phase range below the melting point of the -IV series gold intermetallic compound, a temperature range of 1000°C was used. Further, the heating time was set to 72 hours to ensure complete regularization. The obtained Mn and Nb-added TiAl sample was found to be ordered by an X-ray diffractometer, and each peak was Ll of the TiAl sample. We confirmed that it corresponds to the type structure.
表１にこうして得られた試料から放電加工にて切り出し
た５φＸ ５ ｍｍの試料を用いて常温圧縮試験を行っ
た耐力及び圧縮率の結果をＴｉＡｌ試料及びＭｎ、、Ｎ
ｂ添加Ｔｉ／Ｖ試料について示す。これよりＴｉＡ／試
料と比較してＭｎ、 Ｎｂ添加により室温延性が大幅に
向上していることが見られる。また、高温耐酸化性の向
上については第２図に示した通りである。Table 1 shows the yield strength and compressibility results of a room temperature compression test using a 5φ x 5 mm sample cut out by electrical discharge machining from the sample thus obtained.
The figure shows the b-added Ti/V sample. It can be seen from this that the addition of Mn and Nb significantly improves the room temperature ductility compared to the TiA/sample. Furthermore, the improvement in high temperature oxidation resistance is as shown in FIG.
本発明によれば高温耐酸化性に富み、常温延性が高く、
なおかつ高温強度を失なわないＴ ｉ−／Ｖ系金金属間
化合物得ることができる。According to the present invention, it has high high temperature oxidation resistance, high room temperature ductility,
Furthermore, it is possible to obtain a Ti-/V-based gold intermetallic compound that does not lose its high-temperature strength.
第１図（ａＬ （ｂ）、 （Ｃ）はＴｉＡｌ、 ＴｉＡ
ｌ−４ａｔ％Ｍｎ、ＴｉＡｌ−２ａｔ％Ｍｎ−ｆａｔ％
Ｎｂの均−化焼鈍後の金属組織を示す光学顕微鏡組織写
真、第２図は静的空気中にて８００℃に保持した３種類
の試料の酸化増量変化を示す図、第３図（ａ）、 （ｂ
）、 （Ｃ）はこれら試料において８００℃，２００時
間保持によってできた酸化膜のＥＰＭＡ分析結果を示す
図である。
特許出願人 新日本製鐵株式会社Figure 1 (aL (b), (C) are TiAl, TiA
l-4at%Mn, TiAl-2at%Mn-fat%
Optical microscopic microstructure photograph showing the metal structure after equalization annealing of Nb, Figure 2 is a diagram showing changes in oxidation weight gain of three types of samples held at 800°C in static air, Figure 3 (a) , (b
) and (C) are diagrams showing the EPMA analysis results of oxide films formed by holding these samples at 800° C. for 200 hours. Patent applicant Nippon Steel Corporation
Claims (3)
Ｍｎ１〜４原子％及びＮｂ０．１〜２原子％含有する結
晶構造がＬ１＿０型規則構造であるＴｉ−Ａｌ系金属間
化合物。(1) Ti40-50 at%, Al60-50 at%,
A Ti-Al intermetallic compound containing 1 to 4 at% of Mn and 0.1 to 2 at% of Nb and having a crystal structure of an L1_0 type regular structure.
原子比率から成るマトリックスにＭｎ１〜４原子％及び
Ｎｂ０．１〜２原子％含有する８００℃における高温高
耐酸化性かつ常温圧縮率が３０％以上のＬ１＿０型規則
構造をもつＴｉ−Ａｌ系金属間化合物。(2) Contains 1 to 4 at% of Mn and 0.1 to 2 at% of Nb in a matrix consisting of 45 to 50 at% of Ti and 50 to 55 at% of Al. High temperature high oxidation resistance at 800°C and room temperature compressibility of 30. % or more of L1_0 type ordered structure.
Ｍｎ１〜４原子％及びＮｂ０．１〜２原子％とを不活性
ガス雰囲気中で溶融、凝固した後、規則化焼鈍を行うこ
とを特徴とする高温強度材料用Ｔｉ−Ａｌ系金属間化合
物の製造方法。(3) Ti40-50 at%, Al60-50 at%,
Production of a Ti-Al intermetallic compound for high-temperature strength materials, characterized by melting and solidifying 1 to 4 atomic % of Mn and 0.1 to 2 atomic % of Nb in an inert gas atmosphere, and then subjecting it to ordering annealing. Method.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11624588A JPH01287243A (en) | 1988-05-13 | 1988-05-13 | Ti-al intermetallic compound containing mn and nb and its manufacture |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11624588A JPH01287243A (en) | 1988-05-13 | 1988-05-13 | Ti-al intermetallic compound containing mn and nb and its manufacture |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH01287243A true JPH01287243A (en) | 1989-11-17 |
Family
ID=14682374
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP11624588A Pending JPH01287243A (en) | 1988-05-13 | 1988-05-13 | Ti-al intermetallic compound containing mn and nb and its manufacture |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH01287243A (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH02118043A (en) * | 1988-10-03 | 1990-05-02 | General Electric Co <Ge> | Titanium-aluminum alloy improved with manganese niobium |
| JPH0466630A (en) * | 1990-07-05 | 1992-03-03 | Honda Motor Co Ltd | Ti-al intermetallic compound excellent in hot workability |
| JPH05200529A (en) * | 1991-08-29 | 1993-08-10 | General Electric Co <Ge> | Directional coagulation casting of aluminum titanium |
| JPH0711369A (en) * | 1991-08-29 | 1995-01-13 | Natl Res Inst For Metals | Polycrystal body of high ductility ti-al intermetallic compound |
| US5451366A (en) * | 1992-07-17 | 1995-09-19 | Sumitomo Light Metal Industries, Ltd. | Product of a halogen containing Ti-Al system intermetallic compound having a superior oxidation and wear resistance |
-
1988
- 1988-05-13 JP JP11624588A patent/JPH01287243A/en active Pending
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH02118043A (en) * | 1988-10-03 | 1990-05-02 | General Electric Co <Ge> | Titanium-aluminum alloy improved with manganese niobium |
| JPH0466630A (en) * | 1990-07-05 | 1992-03-03 | Honda Motor Co Ltd | Ti-al intermetallic compound excellent in hot workability |
| JPH05200529A (en) * | 1991-08-29 | 1993-08-10 | General Electric Co <Ge> | Directional coagulation casting of aluminum titanium |
| JPH0711369A (en) * | 1991-08-29 | 1995-01-13 | Natl Res Inst For Metals | Polycrystal body of high ductility ti-al intermetallic compound |
| US5451366A (en) * | 1992-07-17 | 1995-09-19 | Sumitomo Light Metal Industries, Ltd. | Product of a halogen containing Ti-Al system intermetallic compound having a superior oxidation and wear resistance |
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