JPS6159390B2 - - Google Patents
Info
- Publication number
- JPS6159390B2 JPS6159390B2 JP13706682A JP13706682A JPS6159390B2 JP S6159390 B2 JPS6159390 B2 JP S6159390B2 JP 13706682 A JP13706682 A JP 13706682A JP 13706682 A JP13706682 A JP 13706682A JP S6159390 B2 JPS6159390 B2 JP S6159390B2
- Authority
- JP
- Japan
- Prior art keywords
- temperature
- alloy
- shape memory
- superelastic
- solution treatment
- 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
Links
- 239000000956 alloy Substances 0.000 claims description 41
- 229910045601 alloy Inorganic materials 0.000 claims description 26
- KHYBPSFKEHXSLX-UHFFFAOYSA-N iminotitanium Chemical compound [Ti]=N KHYBPSFKEHXSLX-UHFFFAOYSA-N 0.000 claims description 16
- 229910001000 nickel titanium Inorganic materials 0.000 claims description 16
- 229910052742 iron Inorganic materials 0.000 claims description 9
- 230000035882 stress Effects 0.000 claims description 9
- 230000002427 irreversible effect Effects 0.000 claims description 8
- 238000004519 manufacturing process Methods 0.000 claims description 8
- 230000032683 aging Effects 0.000 claims description 7
- 229910052804 chromium Inorganic materials 0.000 claims description 7
- 229910052802 copper Inorganic materials 0.000 claims description 7
- 229910052748 manganese Inorganic materials 0.000 claims description 7
- 239000011159 matrix material Substances 0.000 claims description 7
- 229910052759 nickel Inorganic materials 0.000 claims description 7
- 229910052750 molybdenum Inorganic materials 0.000 claims description 6
- 229910052758 niobium Inorganic materials 0.000 claims description 6
- 229910000510 noble metal Inorganic materials 0.000 claims description 6
- 229910052715 tantalum Inorganic materials 0.000 claims description 6
- 229910052720 vanadium Inorganic materials 0.000 claims description 6
- 229910052726 zirconium Inorganic materials 0.000 claims description 6
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 5
- 238000010791 quenching Methods 0.000 claims description 4
- 230000000171 quenching effect Effects 0.000 claims description 4
- 238000001816 cooling Methods 0.000 claims 2
- 230000009466 transformation Effects 0.000 description 10
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 9
- 239000000243 solution Substances 0.000 description 8
- 239000000463 material Substances 0.000 description 6
- 230000000694 effects Effects 0.000 description 5
- 239000000203 mixture Substances 0.000 description 4
- 238000005482 strain hardening Methods 0.000 description 4
- 238000004804 winding Methods 0.000 description 4
- 238000010438 heat treatment Methods 0.000 description 3
- 238000000034 method Methods 0.000 description 3
- 229910052719 titanium Inorganic materials 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- 238000005242 forging Methods 0.000 description 2
- 229910000734 martensite Inorganic materials 0.000 description 2
- 238000011084 recovery Methods 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 description 1
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 239000012300 argon atmosphere Substances 0.000 description 1
- 239000012298 atmosphere Substances 0.000 description 1
- 235000011089 carbon dioxide Nutrition 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000006355 external stress Effects 0.000 description 1
- 229910002804 graphite Inorganic materials 0.000 description 1
- 239000010439 graphite Substances 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 239000005457 ice water Substances 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 239000011261 inert gas Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000011259 mixed solution Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 230000001376 precipitating effect Effects 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000002250 progressing effect Effects 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 239000010453 quartz Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N silicon dioxide Inorganic materials O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 238000005491 wire drawing Methods 0.000 description 1
Description
〔技術分野〕
本発明は超弾性と非可逆形状記憶性（以下形状
記憶性と略記）の優れたNi―Ti基合金材とその
製造方法に関するものである。
〔従来技術とその問題点〕
NiとTiを原子比で１：１又はその近傍でNiと
Tiを含むNi―Ti合金及びこれらにＶ、Cr、Mn、
Fe、Co、Cu、Zr、Nb、Mo、Ta又は貴金族を添
加したNi―Ti基合金は室温付近の特定の温度で
マルテンサイト変態を起し、これに伴つて超弾性
と形状記憶性というユニークな現象を示すことが
知られている。この超弾性を高性能バネ材とし、
形状記憶性を温度センサー、アクチユエーター又
はこれ等を兼ねる素子として実用化が進められて
いるが、そのためには充分な性能、例えば残留歪
が少なく、寿命が長い材料が要求されている。
〓〓〓〓〓
Ni―Ti基合金材の超弾性や形状記憶性の向上
には、転位すべりをできるだけ起さずに応力誘起
マルテンサイト変態を進行させることが有効であ
ることが金属学的に予測できる。これを達成する
ためには、Ni―Ti基合金に冷間加工を加えて加
工硬化させ、これに再結晶を起さない温度及び時
間、例えば400℃の温度で30分間の形状記憶処理
を施す方法が提案されている。このような方法で
得られたNi―Ti基合金材は、冷間加工によつて
形成された集合組織が形状記憶処理によつて消失
しないため、転位すべりの発生が困難であり、か
つ外部応力による応力誘起変態はそれほど影響を
受けずに進行する。その結果、変態温度以上では
良好な超弾性を、変態温度をまたいで良好な形状
記憶性を得ることができる。
しかしながらこのような方法は冷間加工を充分
に施すことが前提条件であるため、細線や薄板の
ように加工が内部にまで容易に施される場合には
有効であるが、太線や厚板或いはバルク形状のよ
うに加工が内部にまで均一に施されないものや、
Ni含有量が51.0at％を越えて硬くなり、組成的に
冷間加工が困難なものでは充分な冷間加工が不可
能なため実施できない欠点がある。
〔問題点の解決手段とその作用〕
本発明はこれに鑑み種々研究の結果、合金の母
相中に微細なNi3Ti相を分散析出させ、かつ内部
応力が均一であることにより、冷間加工を必要と
せず、良好な超弾性と形状記憶性が得られること
を知見し、超弾性、形状記憶性Ni―Ti基合金材
とその製造方法を開発したものである。
即ち、本願第１発明のNi―Ti基合金材は、
Ni50.0〜52.0at％、残部Tiからなる合金の母相中
に微細なNi3Ti相を分散析出させ、かつ内部応力
が均一であることを特徴とするものである。
又本願第２発明のNi―Ti基合金材は、Ni50.0〜
52.0at％、残部Tiからなる合金のNi又はTi含有量
の1.0at％以下をＶ、Cr、Mn、Fe、Co、Cu、
Zr、Nb、Mo、Ta及び貴金族から選ばれる元素の
１種又は２種以上で置換した合金の母相中に微細
なNi3Ti相を分散析出させ、かつ内部応力が均一
であることを特徴とするものである。
また本願第１発明及び第２発明に係るNi―Ti
基合金材の製造方法は、それぞれ前記組成範囲の
合金を700〜1100℃の温度で溶体化処理した後、
300〜600℃の温度で時効処理することを特徴とす
るものである。
しかして本願第１発明及び第２発明のNi―Ti
基合金材において、合金の組成範囲を上記の如く
限定したのは次の理由によるものである。
第１発明のNi含有量を50.0〜52.0at％と限定し
たのは、Ni含有量が50.0at％未満では充分な超弾
性と形状記憶性が得られず、52.0at％を超える
と、加工性が著しく低下し、熱間鍛造においても
割れを生ずるため、実用価値がないとの判断によ
るものである。また第２発明の合金について、第
１発明合金のNi又はTi含有量の1.0at％以下を
Ｖ、Cr、Mn、Fe、Co、Cu、Zr、Nb、Mo、Ta
及び貴金族の何れか１種又は２種以上で置換する
のは、Ｖ、Cr、Mn、Fe、Co及びCuによる置換
は、合金の超弾性及び形状記憶性をあまり変化さ
せることなく、変態温度を下げ、変態温度を低温
側にコントロールすることができる効果を有し、
Zr、Nb、Mo、Ta及び貴金族による置換は合金の
超弾性及び形状記憶性をあまり変化させることな
く耐食性を向上する効果を有するが、それ等元素
の置換量の合計が、Ni又はTi含有量の1at％を越
えると、加工性を損なうばかりか、超弾性及び形
状記憶性をも劣化するためである。
又第１発明及び第２発明合金において、合金の
母相中に微細なNi3Ti相を分散析出させて、かつ
内部応力が均一であることとするのは、超弾性及
び形状記憶性を劣化させることなく、転位すべり
の発生を困難にして、残留歪を少なくするためで
ある。
また本願第１発明及び第２発明に係る、Ni―
Ti基合金材の製造方法において、上記Ni―Ti基
合金を700〜1100℃の温度で溶体化処理した後、
300〜600℃の温度で時効処理するのは、合金の母
相中に微細なNi3Ti相を分散析出させて、かつ内
部応力が均一であることとするためである。しか
して溶体化処理温度を700〜1100℃と限定したの
は処理温度が700℃未満では溶体化が充分に行わ
れず、1100℃を越えると一部に溶融が生じたり、
又は変形を起すようになるためである。
溶体化処理は不活性ガス、例えばアルゴン雰囲
気中で700〜1100℃の温度に加熱する。この温度
範囲内であれば同様の結果が得られ、加熱時間も
0.5〜10時間の範囲内であれば同様の結果が得ら
〓〓〓〓〓
れる。
焼入れも空気焼入れ程度で所定の特性を得るこ
とができるが、再現性を確保する点から水焼入れ
することが望ましい。
また溶体化処理後の時効処理温度を300〜600℃
と限定したのは、300℃未満の温度では時効析出
が不充分で、良好な特性が得られず、600℃を越
える温度ではNi3Ti単相の領域に入るため、良好
な特性が得られないためである。尚、処理時間は
処理材の大きさにもよるが400℃の温度で１〜10
時間の範囲内であれば同様の結果が得られ、実用
的には350〜450℃の温度で１〜２時間で良好な結
果が得られる。
〔実施例〕
以下、本発明を実施例について詳細に説明す
る。
第１表に示す組成の合金を1000℃の温度に加熱
して水焼入れした後、500℃の温度で１時間時効
処理し、これについてマルテンサイト逆変態点
（Af点）、超弾性及び形状記憶性を測定した。そ
の結果を第１表に併記した。尚、参考のため溶体
化処理後の超弾性及び形状記憶性を測定し、その
結果を第１表に併記した。
各合金は常法により黒鉛ルツボを用いて真空高
周波溶解炉により溶解し、水冷鋳型に鋳造した鋳
塊に熱間鍛造と熱間圧延を加えた後中間焼鈍と冷
間伸線加工を繰返して直径1.0mmの線に仕上げ
た。ただし、本発明合金No.５については、伸線加
工が困難であつたため、圧延加工により厚さ１mm
の板に仕上げ、これより砥石切断によつて幅３
mm、長さ150mmに切断して板状試料とした。これ
等線材及び板材について表面のスケールを除去し
た後、アルゴン雰囲気中、1000℃の温度で１時間
溶体化処理し、氷水中に焼入れ、これを石英管内
に装入して500℃の温度で１時間時効処理した。
形状記憶性は線材又は板材を直径10mmの鉄製棒
に変態温度より20℃以上低い温度で巻き付け、そ
のままの状態で棒から外し、温水中で加熱して変
態温度以上になつた時の直線形状への回復度を角
度により測定し、該角度が175゜以上のものを◎
印で、135゜以上、175゜未満のものを〇印、135
゜未満のものを△印で示した。尚、変態温度が室
温以下のものについてはドライアイスとアルコー
ルの混合液中で巻付けを行つた。
また超弾性は線材又は板材を直径10mmの鉄製棒
に変態温度より高い温度で巻き付けた後、巻き付
け力を除去し、その際のスプリングバツクで回復
した後の角度を測定し、形状記憶性と同様にして
示した。
[Technical Field] The present invention relates to a Ni--Ti base alloy material with excellent superelasticity and irreversible shape memory properties (hereinafter abbreviated as shape memory properties), and a method for producing the same. [Prior art and its problems] Ni and Ti are mixed in an atomic ratio of 1:1 or close to that.
Ni-Ti alloy containing Ti and V, Cr, Mn,
Ni-Ti base alloys containing Fe, Co, Cu, Zr, Nb, Mo, Ta, or noble metals undergo martensitic transformation at a specific temperature around room temperature, resulting in superelasticity and shape memory properties. It is known to exhibit a unique phenomenon. This superelasticity is used as a high-performance spring material,
The practical use of shape memory as a temperature sensor, actuator, or an element that also serves as both is progressing, but materials with sufficient performance, such as low residual strain and long life, are required for this purpose. 〓〓〓〓〓
Metallurgically, it can be predicted that promoting stress-induced martensitic transformation while minimizing dislocation slippage is effective in improving the superelasticity and shape memory of Ni-Ti-based alloy materials. To achieve this, the Ni-Ti base alloy is cold-worked to work harden it, and then subjected to shape memory treatment at a temperature and time that does not cause recrystallization, for example at 400°C for 30 minutes. A method is proposed. In the Ni-Ti base alloy material obtained by this method, the texture formed by cold working does not disappear by shape memory treatment, so it is difficult for dislocation slip to occur and it is resistant to external stress. The stress-induced transformation proceeds without much influence. As a result, good superelasticity can be obtained above the transformation temperature, and good shape memory properties can be obtained beyond the transformation temperature. However, since such a method requires sufficient cold working, it is effective for thin wires and thin plates where processing can be easily applied to the inside, but it is effective for thick wires, thick plates, etc. Items that are not uniformly processed inside, such as bulk shapes,
If the Ni content exceeds 51.0 at%, it becomes hard and difficult to cold work due to its composition, there is a drawback that sufficient cold working is impossible and cannot be performed. [Means for solving the problems and their effects] In view of this, the present invention has been developed as a result of various studies, and has been developed by dispersing and precipitating fine Ni 3 Ti phases in the matrix of the alloy and by making the internal stress uniform. We discovered that good superelasticity and shape memory can be obtained without the need for processing, and developed a superelastic and shape memory Ni-Ti base alloy material and its manufacturing method. That is, the Ni-Ti base alloy material of the first invention of the present application is
It is characterized by having a fine Ni 3 Ti phase dispersed and precipitated in the matrix of an alloy consisting of 50.0 to 52.0 at% Ni and the balance Ti, and having uniform internal stress. Moreover, the Ni-Ti base alloy material of the second invention of the present application has Ni50.0~
V, Cr, Mn, Fe, Co, Cu, Cr, Mn, Fe, Co, Cu,
Fine Ni 3 Ti phase is dispersed and precipitated in the matrix of the alloy substituted with one or more elements selected from Zr, Nb, Mo, Ta, and noble metals, and the internal stress is uniform. It is characterized by: In addition, the Ni-Ti according to the first invention and the second invention of the present application
The method for producing the base alloy materials includes solution treatment of alloys having the above composition ranges at a temperature of 700 to 1100°C, and then
It is characterized by aging treatment at a temperature of 300 to 600°C. However, the Ni-Ti of the first invention and the second invention of the present application
The reason why the composition range of the alloy in the base alloy material is limited as described above is as follows. The reason why the Ni content in the first invention was limited to 50.0 to 52.0 at% is that if the Ni content is less than 50.0 at%, sufficient superelasticity and shape memory properties cannot be obtained, and if it exceeds 52.0 at%, the workability becomes difficult. This was determined to be of no practical value because it significantly lowers the temperature and causes cracks even during hot forging. Regarding the alloy of the second invention, 1.0 at% or less of the Ni or Ti content of the first invention alloy is replaced by V, Cr, Mn, Fe, Co, Cu, Zr, Nb, Mo, Ta.
Replacement with one or more of the noble metals is V, Cr, Mn, Fe, Co, and Cu, without significantly changing the superelasticity and shape memory properties of the alloy. It has the effect of lowering the temperature and controlling the transformation temperature to the low temperature side.
Substitution with Zr, Nb, Mo, Ta, and noble metals has the effect of improving corrosion resistance without significantly changing the superelasticity and shape memory of the alloy. This is because if the content exceeds 1 at%, not only processability is impaired, but also superelasticity and shape memory properties are deteriorated. In addition, in the first and second invention alloys, the fine Ni 3 Ti phase is dispersed and precipitated in the matrix of the alloy and the internal stress is uniform, which deteriorates superelasticity and shape memory. This is to make it difficult for dislocation slip to occur and to reduce residual strain. In addition, Ni-
In the method for producing a Ti-based alloy material, after solution-treating the Ni-Ti-based alloy at a temperature of 700 to 1100°C,
The reason why the aging treatment is carried out at a temperature of 300 to 600°C is to disperse and precipitate a fine Ni 3 Ti phase in the matrix of the alloy and to make the internal stress uniform. However, the reason why the solution treatment temperature was limited to 700 to 1100℃ is that if the treatment temperature is less than 700℃, solution treatment will not be performed sufficiently, and if it exceeds 1100℃, some parts will melt.
Or, it may cause deformation. Solution treatment involves heating to a temperature of 700 to 1100°C in an inert gas atmosphere, such as argon. Similar results can be obtained within this temperature range, and the heating time can also be reduced.
Similar results can be obtained within the range of 0.5 to 10 hours〓〓〓〓〓
It can be done. Predetermined properties can be obtained by air quenching, but water quenching is preferable in order to ensure reproducibility. In addition, the aging treatment temperature after solution treatment is 300 to 600℃.
The reason for this limitation is that at temperatures below 300°C, aging precipitation is insufficient and good properties cannot be obtained, and at temperatures above 600°C, the Ni 3 Ti single phase enters the region, making it difficult to obtain good properties. This is because there is no The processing time depends on the size of the treated material, but the processing time is 1 to 10 minutes at a temperature of 400℃.
Similar results can be obtained within the range of time, and practically good results can be obtained at a temperature of 350 to 450°C for 1 to 2 hours. [Example] Hereinafter, the present invention will be described in detail with reference to Examples. The alloy having the composition shown in Table 1 was heated to a temperature of 1000℃ and water quenched, and then aged at a temperature of 500℃ for 1 hour. The sex was measured. The results are also listed in Table 1. For reference, the superelasticity and shape memory properties after solution treatment were measured, and the results are also listed in Table 1. Each alloy is melted in a vacuum high-frequency melting furnace using a graphite crucible using a conventional method, and the ingot is cast into a water-cooled mold and subjected to hot forging and hot rolling, followed by repeated intermediate annealing and cold wire drawing. Finished with a 1.0mm line. However, since it was difficult to wire-draw the invention alloy No. 5, it was rolled to a thickness of 1 mm.
Finished to a board with a width of 3 by cutting with a whetstone.
mm, and the length was cut to 150 mm to obtain a plate-shaped sample. After removing scale on the surface of these wire rods and plate materials, they were solution-treated at a temperature of 1000℃ for 1 hour in an argon atmosphere, quenched in ice water, placed in a quartz tube, and heated at a temperature of 500℃ for 1 hour. Time-aged. Shape memory is defined by winding a wire or plate material around a 10mm diameter iron rod at a temperature 20℃ or more below the transformation temperature, removing it from the rod in that state, heating it in hot water, and forming a straight line when the temperature reaches the transformation temperature or higher. The degree of recovery is measured by angle, and if the angle is 175° or more, ◎
If the angle is 135° or more and less than 175°, mark ○, 135
Those less than ° are marked with △. In addition, for those whose transformation temperature was below room temperature, winding was performed in a mixed solution of dry ice and alcohol. In addition, superelasticity is measured by winding a wire or plate material around a 10 mm diameter iron rod at a temperature higher than the transformation temperature, removing the winding force, and measuring the angle after recovery due to spring back. It was shown as follows.
【表】
〓〓〓〓〓
[Table] 〓〓〓〓〓
このように本発明によればNi―Ti基合金を溶
体化処理後に時効処理することにより、冷間加工
を必要とせずに、高性能の超弾性、非可逆形状記
憶性が得られるもので、工業上顕著な効果を奏す
るものである。
〓〓〓〓〓
As described above, according to the present invention, by subjecting the Ni-Ti base alloy to solution treatment and then aging treatment, high-performance superelasticity and irreversible shape memory can be obtained without the need for cold working. This has a remarkable industrial effect. 〓〓〓〓〓
Claims (1)
相中に微細なNi3Ti相を分散析出させ、かつ内部
応力が均一であることを特徴とする超弾性、非可
逆形状記憶性Ni―Ti基合金材。 ２ Ni50.0〜52.0at％、残部Tiからなる合金のNi
又はTi含有量の1.0at％以下をＶ、Cr、Mn、
Fe、Co、Cu、Zr、Nb、Mo、Ta及び貴金族から
選ばれる元素の１種又は２種以上で置換した合金
の母相中に微細なNi3Ti相を分散析出させかつ内
部応力が均一であることを特徴とする超弾性、非
可逆形状記憶性Ni―Ti基合金材。 ３ Ni50.0〜52.0at％、残部Tiからなる合金を
700〜1100℃の温度で溶体化処理した後、300〜
600℃の温度で時効処理することを特徴とする超
弾性、非可逆形状記憶性Ni―Ti基合金材の製造
方法。 ４ 溶体化処理後の冷却を水焼入する特許請求の
範囲第３項記載の超弾性、非可逆形状記憶性Ni
―Ti基合金材の製造方法。 ５ Ni50.0〜52.0at％、残部Tiからなる合金のNi
又はTi含有量の1.0at％以下をＶ、Cr、Mn、
Fe、Co、Cu、Zr、Nb、Mo、Ta及び貴金族から
選ばれる元素の１種又は２種以上で置換した合金
を700〜1100℃の温度で溶体化処理した後、300〜
600℃の温度で時効処理することを特徴とする超
弾性、非可逆形状記憶性Ni−Ti基合金材の製造
方法。 ６ 溶体化処理後の冷却を水焼入する特許請求の
範囲第５項記載の超弾性、非可逆形状記憶性Ni
―Ti基合金材の製造方法。[Claims] 1. Superelasticity characterized by having a fine Ni 3 Ti phase dispersed and precipitated in the matrix of an alloy consisting of 50.0 to 52.0 at% Ni and the balance Ti, and having uniform internal stress. , Ni-Ti base alloy material with irreversible shape memory. 2 Ni in an alloy consisting of 50.0 to 52.0 at% Ni and the balance Ti
Or 1.0at% or less of Ti content is replaced by V, Cr, Mn,
Fine Ni 3 Ti phase is dispersed and precipitated in the matrix of the alloy substituted with one or more elements selected from Fe, Co, Cu, Zr, Nb, Mo, Ta, and noble metals, and internal stress is reduced. A superelastic, irreversible shape-memory Ni-Ti-based alloy material characterized by uniformity. 3 An alloy consisting of 50.0 to 52.0at% Ni and the balance Ti
After solution treatment at a temperature of 700~1100℃, 300~
A method for producing a superelastic, irreversible shape memory Ni-Ti base alloy material, which is characterized by aging treatment at a temperature of 600°C. 4. Superelastic, irreversible shape memory Ni according to claim 3, in which cooling after solution treatment is water quenching.
-Production method for Ti-based alloy materials. 5 Ni in an alloy consisting of 50.0 to 52.0 at% Ni and the balance Ti
Or 1.0at% or less of Ti content is replaced by V, Cr, Mn,
After solution treatment of an alloy substituted with one or more elements selected from Fe, Co, Cu, Zr, Nb, Mo, Ta, and noble metals at a temperature of 700 to 1100℃,
A method for producing a superelastic, irreversible shape memory Ni-Ti base alloy material, which is characterized by aging treatment at a temperature of 600°C. 6. Superelastic, irreversible shape memory Ni according to claim 5, in which cooling after solution treatment is water quenching.
-Production method for Ti-based alloy materials.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP13706682A JPS5928548A (en) | 1982-08-06 | 1982-08-06 | Superelastic shape-memory ni-ti base alloy and manufacture thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP13706682A JPS5928548A (en) | 1982-08-06 | 1982-08-06 | Superelastic shape-memory ni-ti base alloy and manufacture thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS5928548A JPS5928548A (en) | 1984-02-15 |
| JPS6159390B2 true JPS6159390B2 (en) | 1986-12-16 |
Family
ID=15190094
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP13706682A Granted JPS5928548A (en) | 1982-08-06 | 1982-08-06 | Superelastic shape-memory ni-ti base alloy and manufacture thereof |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS5928548A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0534303U (en) * | 1991-10-14 | 1993-05-07 | 河村電器産業株式会社 | Equipment storage box mounting structure |
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|---|---|---|---|---|
| JPS60155657A (en) * | 1984-01-12 | 1985-08-15 | Hitachi Metals Ltd | Production of ti-ni superelastic alloy |
| JPS60155656A (en) * | 1984-01-12 | 1985-08-15 | Hitachi Metals Ltd | Production of ti-ni superelastic alloy |
| JPS60169552A (en) * | 1984-01-30 | 1985-09-03 | Hitachi Metals Ltd | Manufacture of shape memory alloy |
| JPS60248856A (en) * | 1984-05-23 | 1985-12-09 | Daido Steel Co Ltd | Ni-ti alloy |
| US4770725A (en) * | 1984-11-06 | 1988-09-13 | Raychem Corporation | Nickel/titanium/niobium shape memory alloy & article |
| JPS61235528A (en) * | 1985-04-09 | 1986-10-20 | Keijiyou Kioku Gokin Gijutsu Kenkyu Kumiai | Superelastic ni-ti-cr alloy |
| JPS6210233A (en) * | 1985-07-09 | 1987-01-19 | Tohoku Metal Ind Ltd | Shape memory alloy |
| JPH0686639B2 (en) * | 1985-07-09 | 1994-11-02 | 株式会社トーキン | Shape memory alloy |
| JPS6247445A (en) * | 1985-08-24 | 1987-03-02 | Tohoku Metal Ind Ltd | Pseudoelastic alloy |
| CA1279210C (en) * | 1985-12-23 | 1991-01-22 | Mitsubishi Kinzoku Kabushiki Kaisha | Wear-resistant intermetallic compound alloy having improved machineability |
| JPH0639648B2 (en) * | 1986-01-23 | 1994-05-25 | 大同特殊鋼株式会社 | Shape memory alloy material and manufacturing method thereof |
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| JP2541802B2 (en) * | 1986-07-07 | 1996-10-09 | 株式会社トーキン | Shape memory TiNiV alloy and manufacturing method thereof |
| JPS6383252A (en) * | 1986-09-26 | 1988-04-13 | Furukawa Electric Co Ltd:The | Method and device for heat treating superelastic shape memory material |
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| JPH07300638A (en) * | 1995-05-29 | 1995-11-14 | Daido Steel Co Ltd | Shape memory alloy material and its production |
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| WO2011053737A2 (en) * | 2009-11-02 | 2011-05-05 | Saes Smart Materials | Ni-Ti SEMI-FINISHED PRODUCTS AND RELATED METHODS |
| CN104099544A (en) * | 2013-04-07 | 2014-10-15 | 北京有色金属研究总院 | Whole course memory effect acquisition method for shape memory alloy |
| CN104946956A (en) * | 2015-06-09 | 2015-09-30 | 哈尔滨工程大学 | TiNiCuNb shape memory alloy and preparation method thereof |
| CN105033252B (en) * | 2015-07-23 | 2016-05-25 | 南京航空航天大学 | Laser in combination process technology based on automatic power spreading is prepared the method for marmem intravascular stent |
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-
1982
- 1982-08-06 JP JP13706682A patent/JPS5928548A/en active Granted
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0534303U (en) * | 1991-10-14 | 1993-05-07 | 河村電器産業株式会社 | Equipment storage box mounting structure |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS5928548A (en) | 1984-02-15 |
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