JPH0441639A - Ti-ni-c shape memory alloy and its manufacture - Google Patents
Ti-ni-c shape memory alloy and its manufactureInfo
- Publication number
- JPH0441639A JPH0441639A JP14732590A JP14732590A JPH0441639A JP H0441639 A JPH0441639 A JP H0441639A JP 14732590 A JP14732590 A JP 14732590A JP 14732590 A JP14732590 A JP 14732590A JP H0441639 A JPH0441639 A JP H0441639A
- Authority
- JP
- Japan
- Prior art keywords
- shape memory
- alloy
- memory alloy
- tinic
- tini
- 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
- 229910001285 shape-memory alloy Inorganic materials 0.000 title claims abstract description 18
- 238000004519 manufacturing process Methods 0.000 title claims description 7
- 230000032683 aging Effects 0.000 claims abstract description 12
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 3
- PVNIIMVLHYAWGP-UHFFFAOYSA-N Niacin Chemical compound OC(=O)C1=CC=CN=C1 PVNIIMVLHYAWGP-UHFFFAOYSA-N 0.000 claims description 14
- 239000011664 nicotinic acid Substances 0.000 claims description 14
- 235000001968 nicotinic acid Nutrition 0.000 claims description 14
- 238000000034 method Methods 0.000 claims description 8
- 239000000463 material Substances 0.000 abstract description 8
- 230000006870 function Effects 0.000 abstract description 6
- 229910018106 Ni—C Inorganic materials 0.000 abstract 1
- KHYBPSFKEHXSLX-UHFFFAOYSA-N iminotitanium Chemical class [Ti]=N KHYBPSFKEHXSLX-UHFFFAOYSA-N 0.000 abstract 1
- 230000001105 regulatory effect Effects 0.000 abstract 1
- 229910045601 alloy Inorganic materials 0.000 description 37
- 239000000956 alloy Substances 0.000 description 37
- 229910010380 TiNi Inorganic materials 0.000 description 15
- 230000009466 transformation Effects 0.000 description 9
- 230000000694 effects Effects 0.000 description 6
- 238000005482 strain hardening Methods 0.000 description 4
- 230000035882 stress Effects 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 3
- 229910052804 chromium Inorganic materials 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 230000001771 impaired effect Effects 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 238000011084 recovery Methods 0.000 description 2
- 230000002441 reversible effect Effects 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- 229910001020 Au alloy Inorganic materials 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 230000006399 behavior Effects 0.000 description 1
- 230000036760 body temperature Effects 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000003353 gold alloy Substances 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 230000003446 memory effect Effects 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 229910001220 stainless steel Inorganic materials 0.000 description 1
- 229910052715 tantalum Inorganic materials 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
- 230000000007 visual effect Effects 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/006—Resulting in heat recoverable alloys with a memory effect
Abstract
Description
【発明の詳細な説明】
［産業上の利用分野］
本発明は、超弾性機能を有する形状記憶合金に関し、詳
しくはバネ材等に用いられる形状記憶合金及びその製造
方法に関する。DETAILED DESCRIPTION OF THE INVENTION [Industrial Application Field] The present invention relates to a shape memory alloy having a superelastic function, and more particularly to a shape memory alloy used for spring materials and the like, and a method for manufacturing the same.
［従来の技術］
ＴｉＮｉ合金 ＴｉＮ１Ｘ合金（但し、Ｘ−Ｆｅ、Ｃｕ
、Ｃｒ、Ｖ・・・等）合金が、熱弾性マルテンサイト変
態の逆変態に付随して顕著な形状記憶効果を示すことは
良く知られている（「金属」１９６６年２月１３日号、
４４．ｒ日本金属学会会報」第１２巻、第３号（１９７
Ｂ）１５７゜「日本金属学会誌」第３０巻、第２号（１
９７５）１７５）。[Prior art] TiNi alloy TiN1X alloy (however, X-Fe, Cu
, Cr, V, etc.) It is well known that alloys (such as Cr, V, etc.) exhibit a remarkable shape memory effect accompanying the reverse transformation of thermoelastic martensitic transformation ("Metal", February 13, 1966 issue,
44. ``Bulletin of the Japan Institute of Metals'' Volume 12, No. 3 (197
B) 157゜ “Journal of the Japan Institute of Metals” Vol. 30, No. 2 (1
975) 175).
これと同時にＴｉＮｉ合金にゴムのようなしなやかさを
示す超弾性機能があることも良く知られている（ｒＪ、
Ａｐｐｌ、ｐｈｙｓ、、３４（１９６３）１４７５．東
北大学選研紮報２７（１，９７１）２４５） 。At the same time, it is well known that TiNi alloys have superelastic properties that exhibit rubber-like flexibility (rJ,
Appl, phys, 34 (1963) 1475. Tohoku University Senken Rhoho 27 (1,971) 245).
更１．：、ＴｉＮｉ合金にＣを添加したＴｉＮｉＣ合金
について１本発明者はＣ添加によって１本質的なＴｉＮ
ｉ合金のもつ形状記憶特性は損なわれないこと、及び形
状記憶、特に可逆形状記憶特性に役立つことを示してい
る（東北大学選研索報。Further 1. : Regarding the TiNiC alloy in which C is added to the TiNi alloy, the present inventor has discovered that by adding C, the essential TiN
It has been shown that the shape memory properties of the i-alloy are not impaired, and that it is useful for shape memory, especially reversible shape memory properties (Tohoku University Research Report).
昭和５７年６月、第３８巻、特開昭６３−１１６３６号
公報）
前述したＴｉＮｉ合金の超弾性機能は、約７％の伸び変
形を与えても、荷重を解放すると同時に殆ど元に戻る。(June 1980, Vol. 38, JP-A-63-11636) The above-mentioned superelastic function of the TiNi alloy returns to almost its original state as soon as the load is released, even if it is subjected to an elongation deformation of about 7%.
また、変形に必要な応力が殆ど一定で、且つ変形除荷の
回復応力もほぼ一定となるため、これまでにブラジャー
用芯金、歯列矯正器具、カテーテルガイドワイヤー等主
として人体に関するバネ材とに使用されている。In addition, the stress required for deformation is almost constant, and the recovery stress after deformation and unloading is also almost constant. It is used.
［発明が解決しようとする課８］
しかし、従来のステンレス、あるいはピアノ線等のバネ
材に比べ、バネの剛性に欠ける難点があった。[Problem 8 to be solved by the invention] However, compared to conventional spring materials such as stainless steel or piano wire, the spring has a disadvantage in that it lacks rigidity.
これに対し１通常ＴｉＮｉ合金の超弾性機能は。In contrast, the superelastic function of normal TiNi alloys is.
冷間加工後、４００〜５５０℃の時効処理によって付与
されるが、この方法では、優れた変形・回復挙動を示す
もののバネとしての剛性感に欠ける。After cold working, it is applied by aging treatment at 400 to 550°C, but this method shows excellent deformation and recovery behavior, but lacks the rigidity of a spring.
これを解決する手段として冷間加工状態でバネ材として
使用する方法が挙げられるが、剛性感の改善には若干の
効果は認められるものの１本来的に求められる超弾性機
能は損なわれる。One way to solve this problem is to use it as a spring material in a cold-worked state, but although it is somewhat effective in improving the stiffness, the originally required superelastic function is impaired.
このように、従来のバネ材の剛性を保持できなため１人
体に係るガイドワイヤー、ブラジャー芯金、歯列矯正器
具に形状記憶合金を用いる場合において、従来と同等の
機能を持たせるためには。In this way, when shape memory alloys are used in guide wires, brassiere cores, and orthodontic appliances related to the human body because they cannot maintain the rigidity of conventional spring materials, it is necessary to provide them with the same functionality as conventional spring materials. .
用いる線は太くなり、外見上、スペース上の問題を生じ
ていた。The lines used were thicker, creating visual and spacing problems.
そこで１本発明の技術的課題は、上記難点を解決し、断
面積が小なる場合においても１本質的な超弾性機能を損
なわず高い剛性を有するバネ材等に用いられるＴｉＮｉ
Ｃ形状記憶合金及びその製造方法を提供することにある
。Therefore, 1. the technical problem of the present invention is to solve the above-mentioned difficulties, and 1. to use TiNi for spring materials, etc., which has high rigidity without impairing the essential superelastic function even when the cross-sectional area is small.
An object of the present invention is to provide a C shape memory alloy and a method for manufacturing the same.
［課題を解決するための手段］
本発明によれば、ＴｉＮｉ系形状記憶合金において、Ｃ
を０．２０〜５．Ｏａｔ％含み、３７℃以下で超弾性特
性を有することを特徴とするＴｉＮｉＣ形状記憶合金が
得られる。[Means for Solving the Problems] According to the present invention, in a TiNi-based shape memory alloy, C
0.20 to 5. A TiNiC shape memory alloy containing Oat% and having superelastic properties at 37° C. or lower is obtained.
本発明によれば、前記ＴｉＮｉＣ形状記憶合金において
、Ｎｉ及びＣの含有量が総量で少なくとも５０ａ ｔ％
以上であることを特徴とするＴｉＮｉＣ形状記憶合金が
得られる。According to the present invention, in the TiNiC shape memory alloy, the total content of Ni and C is at least 50at%.
A TiNiC shape memory alloy characterized by the above is obtained.
本発明によれば、前記ＴｉＮｉＣ形状記憶合金を製造す
る方法であって、６００’Ｃ以下の時効処理を行うこと
を特徴とするＴｉＮｉＣ形状記憶合金の製造方法が得ら
れる。According to the present invention, there is obtained a method for manufacturing the TiNiC shape memory alloy, which is characterized in that an aging treatment at 600'C or less is performed.
本発明によれば、前記ＴｉＮｉＣ形状記憶合金の製造方
法であって、前記時効処理は４００〜５５０℃で行うこ
とを特徴とするＴｉＮｉＣ形状記憶合金の製造方法が得
られる。According to the present invention, there is obtained a method for manufacturing the TiNiC shape memory alloy, wherein the aging treatment is performed at 400 to 550°C.
ＴｉＮｉ合金で少なくとも３７℃における超弾性特性を
得るためには、６００”Ｃ以下の温度での時効処理によ
って中間相変態が現れる必要がある。In order to obtain superelastic properties at least at 37° C. in a TiNi alloy, an intermediate phase transformation must occur through aging treatment at a temperature below 600”C.
溶体化処理後の６００℃以下の温度で時効処理がおこな
われる場合は、中間相変態が現れるためには、Ｎｉ濃度
は少なくとも５０．５ａｔ％が必要である。When aging treatment is performed at a temperature of 600° C. or lower after solution treatment, the Ni concentration must be at least 50.5 at % in order for mesophase transformation to occur.
また、冷間加工後に６００’Ｃ以下の温度での時効処理
が行われる場合には１合金のＮｉ濃度は４９、Ｏａｔ％
以上である。In addition, when aging treatment is performed at a temperature of 600'C or less after cold working, the Ni concentration of one alloy is 49, Oat%.
That's all.
特に、超弾性の良好なカーブを得る最適熱処理温度の５
００℃前後の時効処理では１合金のＮｉ濃度は少なくと
も５０．２ａｔ％が必要とされる。In particular, the optimum heat treatment temperature for obtaining a good curve of superelasticity is 5.
In aging treatment at around 00°C, the Ni concentration of one alloy is required to be at least 50.2 at%.
本発明によるＴｉＮｉＣ合金についても少なくとも同様
の時効で中間相変態が出現されることが必要とされる。It is also necessary for the TiNiC alloy according to the present invention that an intermediate phase transformation appears with at least similar aging.
しかし、Ｃの添加により剛性アップの効果と同時に変態
温度低下の効果を奏するためには合金中のＮｉ４度は、
ＴｉＮｉ合金に比べ少ない領域で可能であり１具体的に
は、Ｎｉ十Ｃの含量が５０．０ａｔ％以上であれば良い
。However, in order for the addition of C to have the effect of increasing rigidity and lowering the transformation temperature, the Ni4 degree in the alloy must be
This is possible in a smaller area compared to TiNi alloys, and specifically, it is sufficient if the content of Ni+C is 50.0 at% or more.
本発明において、Ｃの添加効果の範囲を０．２０〜５．
Ｏａｔ％としたのは、０．２０ａｔ％未満では１変態温
度を低下させ剛性アップの効果が認め難いためであり、
５．Ｏａｔ％を越えると剛性の上昇効果は認められるも
のの、冷間加工性を極度に悪くするためである。In the present invention, the range of the effect of adding C is 0.20 to 5.
The reason why it is set as Oat% is that if it is less than 0.20at%, it is difficult to see the effect of lowering the first transformation temperature and increasing the rigidity.
5. This is because if it exceeds Oat%, although the effect of increasing rigidity is recognized, cold workability becomes extremely poor.
尚、以下に述べる実施例においては、ＴｉＮｉ合金につ
いて述べるでいるが１本発明はＴｉＮｉ合金の一部を第
３の元素Ｘ （Ｘｌ、ｔＣｒ、 Ｖ、 Ａ Ｉ 。In the examples described below, a TiNi alloy will be described; however, in the present invention, a part of the TiNi alloy is replaced by a third element X (Xl, tCr, V, A I ).
Ｎｂ、Ｔａ、Ｗ等の元素）で置換したＴｉＮ１Ｘ合金に
ついても、Ｃ添加効果は十分に認められるものである。The effect of C addition is also sufficiently recognized in the TiN1X alloy substituted with elements such as Nb, Ta, and W.
［実施例コ 次に１本発明の実施例を図面を参照して説明する。[Example code] Next, an embodiment of the present invention will be described with reference to the drawings.
溶解法によって得たＴｉＮｉ合金及びＴｉＮｉＣ合金及
びＴｉＮｉＣ合金を熱間加工、冷間加工によって、直径
１．３１１ｍφまで加工し、９５０℃×１０分の溶体化
処理後、直径１，０■φまで加工し、冷間加工率４０％
の試験片を得た。The TiNi alloy, TiNiC alloy, and TiNiC alloy obtained by the melting method were processed to a diameter of 1.311 mφ by hot working and cold working, and after solution treatment at 950°C for 10 minutes, processed to a diameter of 1.0 mmφ. and cold working rate 40%
A test piece was obtained.
その後、５００℃で３０分間の時効処理を行い。Thereafter, aging treatment was performed at 500°C for 30 minutes.
３７℃での引張り試験により、荷重及び除荷型サイクル
による超弾性特性の測定を行った。The superelastic properties were measured by tensile testing at 37°C with loading and unloading type cycles.
第１図（ａ）、（ｂ）は本発明の実施例による合金とし
て＋ Ｔ ｊ ５０−Ｘ／２Ｎ ｉ ５０−Ｘ／２ＣＸ
合金（但し、 Ｘ−１，２，３，） ＋ Ｔ ｉ
４９．７５−Ｘ／２ ・Ｎｉ５０、２５−Ｘ／２ Ｃ
Ｘ合金（但し、Ｘ−１，２，３，）の式で表わされるＴ
ｉＮｉ合金線の５％引張りによる荷重・除荷型サイクル
結果を示している。FIGS. 1(a) and 1(b) show + T j 50-X/2N i 50-X/2CX as an alloy according to an embodiment of the present invention.
Alloy (X-1, 2, 3,) + Ti
49.75-X/2 ・Ni50, 25-X/2 C
T expressed by the formula of X alloy (X-1, 2, 3,)
The results of loading/unloading type cycles of iNi alloy wire under 5% tension are shown.
また、比較例として、上記合金のＸ−０の場合の合金も
夫々併せて示した。In addition, as comparative examples, alloys in the case of X-0 of the above alloys are also shown.
第１図（ａ）、（ｂ）において、Ｃを添加しない（Ｘ−
０）の比較例に係るＴｉ、。Ｎｉ、。合金線は、３７℃
では超弾性を示さないが、ＣをＸ−１゜２．３の割合で
添加した実施例による合金はそれぞれ良好な超弾性特性
を示し、その応力レベルもほぼ直線的に高くなっている
。また、同様なことが（Ｔ ｉ ４９．５−Ｘ／２Ｎ
ｉ ５０．５−Ｘ／２ＣＸ （Ｘ＝ １ 、２゜３）合
金について言えることが判明した。In Figures 1(a) and (b), C is not added (X-
Ti according to the comparative example of 0). Ni,. Alloy wire is 37℃
However, the alloys according to the examples in which C was added at a ratio of X-1°2.3 each exhibited good superelastic properties, and their stress levels increased almost linearly. Also, the same thing happens (T i 49.5-X/2N
It has been found that the same can be said for the i50.5-X/2CX (X=1, 2°3) alloy.
−船釣に、ＴｉＮｉ合金にＣを添加すると。- When C is added to TiNi alloy for boat fishing.
ＴｉＮｉ合金がマトリックス中のＣと反応して。TiNi alloy reacts with C in the matrix.
主としてＴｉＣを生成させ、この合金の変態温度を低下
させることが知られている。しかし２本発明の実施例に
おいては単にＣが合金の変態温度を低下させるだけでは
なく、加工によって、ファイバー化されたＴｉＣが１０
の添加量に共に増加し。It is known to primarily produce TiC and lower the transformation temperature of this alloy. However, in the two embodiments of the present invention, C not only lowers the transformation temperature of the alloy, but also allows fiberized TiC to
The amount of addition increases as well.
合金の超弾性の応力アップを導き母相でのバネの剛性ア
ップをさせる効果を導くものであることが判明した。It was found that this increases the superelastic stress of the alloy and increases the rigidity of the spring in the matrix.
゛［発明の効果］
以上説明したように１本発明によれば、少なくとも体温
（３７℃）でバネ剛性の高い超弾性を得ることかできる
ため、従来のＴｉＮｉ合金で使われていた歯列矯正器具
、ブラジャー用芯金、カテーテルガイドワイヤー等人体
に供される断面の小さなバネ材等に幅広く使われること
が期待さねる。[Effects of the Invention] As explained above, according to the present invention, it is possible to obtain superelasticity with high spring stiffness at least at body temperature (37°C). It is expected that it will be widely used in spring materials with small cross sections used in the human body, such as instruments, brassiere cores, and catheter guide wires.
荷重サイクル結果を夫々示す図で、比較の為にＴ ｉ
５ＯＮ ｊ ｓｏ金合金即ち、Ｘ−０）、及びＴｉａ、
７ｓＮｉ５゜２９合金（即ち、Ｘ−０）の式で表される
ＴｉＮｉ合金線の特性も併せＣ示した。This figure shows the load cycle results, and for comparison, T i
5ON j so gold alloy i.e. X-0), and Tia,
The characteristics of the TiNi alloy wire represented by the formula of 7sNi5°29 alloy (ie, X-0) are also shown in C.
Claims (1)
特性を有することを特徴とするＴｉＮｉＣ形状記憶合金
。 ２、第１の請求項記載のＴｉＮｉＣ形状記憶合金におい
て、Ｎｉ及びＣの含有量が総量で少なくとも５０ａｔ％
以上であることを特徴とするＴｉＮｉＣ形状記憶合金。 ３、第１又は第２の請求項記載のＴｉＮｉＣ形状記憶合
金を製造する方法であって、６００℃以下の時効処理を
行うことを特徴とするＴｉＮｉＣ形状記憶合金の製造方
法。 ４、第３の請求項記載のＴｉＮｉＣ形状記憶合金の製造
方法において、前記時効処理は４００〜５５０℃で行う
ことを特徴とするＴｉＮｉＣ形状記憶合金の製造方法。[Claims] 1. A TiNiC shape memory alloy, which contains 0.20 to 5.0 at% of C and has superelastic properties at temperatures below 37°C. 2. In the TiNiC shape memory alloy according to the first claim, the total content of Ni and C is at least 50 at%
A TiNiC shape memory alloy characterized by the above. 3. A method for manufacturing a TiNiC shape memory alloy according to claim 1 or 2, which comprises performing an aging treatment at 600° C. or lower. 4. The method for manufacturing a TiNiC shape memory alloy according to claim 3, wherein the aging treatment is performed at 400 to 550°C.
Priority Applications (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP02147325A JP3141328B2 (en) | 1990-06-07 | 1990-06-07 | Manufacturing method of super elastic spring alloy |
| EP19910109349 EP0460695B1 (en) | 1990-06-07 | 1991-06-07 | Ti-Ni-C shape memory alloy with a pseudoelasticity and a wide elasticity range |
| DE1991623084 DE69123084T2 (en) | 1990-06-07 | 1991-06-07 | Pseudoelastic Ti-Ni-C shape memory alloy with a higher elastic limit |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP02147325A JP3141328B2 (en) | 1990-06-07 | 1990-06-07 | Manufacturing method of super elastic spring alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0441639A true JPH0441639A (en) | 1992-02-12 |
| JP3141328B2 JP3141328B2 (en) | 2001-03-05 |
Family
ID=15427633
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP02147325A Expired - Fee Related JP3141328B2 (en) | 1990-06-07 | 1990-06-07 | Manufacturing method of super elastic spring alloy |
Country Status (3)
| Country | Link |
|---|---|
| EP (1) | EP0460695B1 (en) |
| JP (1) | JP3141328B2 (en) |
| DE (1) | DE69123084T2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2007147549A (en) * | 2005-11-30 | 2007-06-14 | Hugle Electronics Inc | Method and device for displaying measured data |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP3782289B2 (en) * | 2000-07-06 | 2006-06-07 | トキコーポレーション株式会社 | Method of processing shape memory alloy and shape memory alloy |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4533411A (en) * | 1983-11-15 | 1985-08-06 | Raychem Corporation | Method of processing nickel-titanium-base shape-memory alloys and structure |
| JPH0665742B2 (en) * | 1987-01-08 | 1994-08-24 | 株式会社ト−キン | Shape memory TiNiV alloy manufacturing method |
-
1990
- 1990-06-07 JP JP02147325A patent/JP3141328B2/en not_active Expired - Fee Related
-
1991
- 1991-06-07 EP EP19910109349 patent/EP0460695B1/en not_active Expired - Lifetime
- 1991-06-07 DE DE1991623084 patent/DE69123084T2/en not_active Expired - Fee Related
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2007147549A (en) * | 2005-11-30 | 2007-06-14 | Hugle Electronics Inc | Method and device for displaying measured data |
Also Published As
| Publication number | Publication date |
|---|---|
| DE69123084D1 (en) | 1996-12-19 |
| EP0460695A1 (en) | 1991-12-11 |
| DE69123084T2 (en) | 1997-04-03 |
| JP3141328B2 (en) | 2001-03-05 |
| EP0460695B1 (en) | 1996-11-13 |
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