JPH01212728A - Manufacture of shape memory alloy - Google Patents
Manufacture of shape memory alloyInfo
- Publication number
- JPH01212728A JPH01212728A JP3740688A JP3740688A JPH01212728A JP H01212728 A JPH01212728 A JP H01212728A JP 3740688 A JP3740688 A JP 3740688A JP 3740688 A JP3740688 A JP 3740688A JP H01212728 A JPH01212728 A JP H01212728A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- shape memory
- memory alloy
- atomic percent
- tinicu
- 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 23
- 238000004519 manufacturing process Methods 0.000 title claims description 19
- 239000000956 alloy Substances 0.000 claims abstract description 27
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 26
- 238000000034 method Methods 0.000 claims abstract description 19
- 238000010791 quenching Methods 0.000 claims abstract description 9
- 230000000171 quenching effect Effects 0.000 claims abstract description 9
- 229910010165 TiCu Inorganic materials 0.000 claims abstract description 6
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 5
- 238000002844 melting Methods 0.000 claims abstract description 5
- 230000008018 melting Effects 0.000 claims abstract description 5
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 4
- 238000001556 precipitation Methods 0.000 claims description 7
- 239000011159 matrix material Substances 0.000 claims description 3
- 238000001816 cooling Methods 0.000 claims 2
- 238000010309 melting process Methods 0.000 claims 1
- 229910052742 iron Inorganic materials 0.000 abstract description 5
- 229910052802 copper Inorganic materials 0.000 abstract description 2
- 229910018054 Ni-Cu Inorganic materials 0.000 abstract 3
- 229910018481 Ni—Cu Inorganic materials 0.000 abstract 3
- 230000008021 deposition Effects 0.000 abstract 2
- 229910052759 nickel Inorganic materials 0.000 abstract 1
- 238000005507 spraying Methods 0.000 abstract 1
- 239000010949 copper Substances 0.000 description 16
- 229910000881 Cu alloy Inorganic materials 0.000 description 12
- 230000009466 transformation Effects 0.000 description 11
- 229910000734 martensite Inorganic materials 0.000 description 6
- 239000002184 metal Substances 0.000 description 6
- 229910052751 metal Inorganic materials 0.000 description 6
- 239000000203 mixture Substances 0.000 description 6
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 5
- 229910002804 graphite Inorganic materials 0.000 description 5
- 239000010439 graphite Substances 0.000 description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- 238000005452 bending Methods 0.000 description 4
- 238000010586 diagram Methods 0.000 description 4
- 238000007796 conventional method Methods 0.000 description 3
- 238000012545 processing Methods 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 229910010380 TiNi Inorganic materials 0.000 description 2
- WCERXPKXJMFQNQ-UHFFFAOYSA-N [Ti].[Ni].[Cu] Chemical compound [Ti].[Ni].[Cu] WCERXPKXJMFQNQ-UHFFFAOYSA-N 0.000 description 2
- 239000012300 argon atmosphere Substances 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 230000003446 memory effect Effects 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- 238000000137 annealing Methods 0.000 description 1
- 238000013459 approach Methods 0.000 description 1
- 239000012298 atmosphere Substances 0.000 description 1
- 229910002056 binary alloy Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 238000002347 injection Methods 0.000 description 1
- 239000007924 injection Substances 0.000 description 1
- 238000000399 optical microscopy Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000003672 processing method Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 229910001220 stainless steel Inorganic materials 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
Abstract
Description
【発明の詳細な説明】
［産業上の利用分野］
本発明は、チタン・ニッケル・銅基形状記憶合金の製造
に関するもので、特にしステリシスの小さい、且つ、低
温時と高温時の荷重差の大きい形状記憶合金の製造方法
に関するものである。[Detailed Description of the Invention] [Industrial Application Field] The present invention relates to the production of titanium-nickel-copper-based shape memory alloys, and in particular, the invention relates to the production of titanium-nickel-copper-based shape memory alloys, which have a small steresis and a load difference between low and high temperatures. The present invention relates to a method for manufacturing large shape memory alloys.
［従来の技術］
一般にＴ１Ｎｉ合金が熱弾性型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よく知
られている。[Prior Art] It is generally well known that T1Ni alloy exhibits a remarkable shape memory effect accompanying the reverse transformation of thermoelastic martensitic transformation.
また、特公昭６１−５４８５０号公報のようにＮｉの一
部をＣｕで置換したＴ ｉ Ｎ ｉ Ｃｕ合金が前記同
様の形状記憶効果を示し、かつ、組成に対し変態温度が
殆んど無関係であることはＲ１１ｅｌｅｏｎらによって
見出されている。Furthermore, as disclosed in Japanese Patent Publication No. 61-54850, a TiNiCu alloy in which part of Ni is replaced with Cu exhibits the same shape memory effect as described above, and the transformation temperature is almost unrelated to the composition. Something has been discovered by R11eleon et al.
更に、このＴ ｉ Ｎ ｉ Ｃｕ合金は、Ｃｕの添加量
が増えるにつれ、マルテンサイト変態温度と逆変態温度
が近接し、マルテンサイト相は、Ｔ ｉ Ｎ ｉ２元合
金については、単斜晶であるのに対して、Ｃｕ１Ｏ原子
パ一セント以上のＴ ｉ Ｎ ｉ Ｃｕ合金では斜方晶
となることが重量らによって見出されている。（東北大
選研索報３７ （１９８１） ７９ ）重量らによって
見出された特徴は、応力−温度しステリシスの小さなバ
ネ製作を可能にし、これまで自動車用バネ等に実用化さ
れている。Furthermore, in this TiNiCu alloy, as the amount of Cu added increases, the martensitic transformation temperature and the reverse transformation temperature approach each other, and the martensitic phase is monoclinic for the TiNi binary alloy. On the other hand, Weight et al. found that a T i N i Cu alloy containing more than 1 atomic percent of Cu becomes orthorhombic. (Tohoku University Research Report 37 (1981) 79) The characteristics discovered by Weight et al. enable the production of springs with small stress-temperature steresis, and have been put to practical use in automobile springs and the like.
［発明が解決しようとする課題］
Ｔ ｉ Ｎ ｉ Ｃｕ合金は、Ｃｕ添加量を１０原子パ
ーセントから増加されるに従ってマルテンサイト相の結
晶楕遠の変化に仔いＴ ｉ Ｃｕが析出し始め、その結
晶構造の変化１の増加と伴に、Ｔ ｉ Ｃｕの析出量は
多くなる。このＴ ｉ ＣｕはＴ ｉ Ｎ ｉ Ｃｕ合
金を脆くさせるので、Ｔ ｉ Ｎ ｉ Ｃｕ合金の製造
を困難にさせている。このため、しステリシスの小さな
バネを得るためには、Ｃｕを多く添加した方が良いが、
前記Ｔ１Ｃｕの析出の増大によってＴ ｉ Ｎ ｉ Ｃ
ｕ合金の製造は困難になり、これまでのＴ ｉ Ｎ ｉ
Ｃｕ合金の製造方法ではＴ ｉ Ｎ ｉ合金の１０原
子パーセントのＣｕ添加が限度であった。[Problems to be Solved by the Invention] In a TiNiCu alloy, as the amount of Cu added is increased from 10 atomic percent, TiCu begins to precipitate due to changes in the crystal ellipse of the martensitic phase. As the change 1 in the crystal structure increases, the amount of T i Cu precipitated increases. This T i Cu makes the T i N i Cu alloy brittle, making it difficult to manufacture the T i N i Cu alloy. Therefore, in order to obtain a spring with small steresis, it is better to add a large amount of Cu, but
Due to the increased precipitation of T1Cu, T i N i C
It has become difficult to manufacture u-alloys, and the conventional T i N i
In the manufacturing method of Cu alloy, the limit is 10 atomic percent Cu addition to TiNi alloy.
ここで云うこれまでの方法では、前記特公昭６１−５４
８５０号公報に記載されているものであって、黒鉛ルツ
ボ内でアルゴン雰囲気の誘導炉によって溶解し、黒鉛鋳
型に鋳遺し、９００℃で焼鈍を繰り返しながら、約１０
％ごとの加工を行う方法である。この加工方法によれば
、鋳造時の溶湯凝固過程でのＴ ｉ Ｃｕ析出は避けら
れず、得′られたＴ ｉ Ｎ ｉ Ｃｕ合金材料は脆＜
、Ｃｕ添加量が原子パーセント以上のＴ ｉ Ｎ ｉ
Ｃｕ合金のｆＪｊｉ造後の加工工程すなわち、熱間およ
び冷間加工では素材にしビ・クラックが入り、所要の寸
法素材は得られないという欠点を有した。In the conventional method mentioned here, the above-mentioned
It is described in Japanese Patent No. 850, and is melted in a graphite crucible in an induction furnace in an argon atmosphere, cast in a graphite mold, and repeatedly annealed at 900°C for about 10 minutes.
This is a method of processing by percentage. According to this processing method, TiCu precipitation during the molten metal solidification process during casting is unavoidable, and the obtained TiNiCu alloy material is brittle.
, T i N i in which the amount of Cu added is atomic percent or more
The processing steps after fJji fabrication of Cu alloys, that is, hot and cold working, have the drawback that cracks occur in the material, making it impossible to obtain a material with the required dimensions.
本発明は上記欠点に鑑みて行われており、バネ材料とし
てしステリシスの小さく、靭性のすぐれた形状記憶合金
１！！３ｍ方法を提供することを目的とする。The present invention has been made in view of the above-mentioned drawbacks, and it is a shape memory alloy that can be used as a spring material with small steresis and excellent toughness! ! The purpose is to provide a 3m method.
［課題を解決するための手段］
本発明によればＴ ｉ Ｎ ｉ Ｃｕ合金インゴットか
ら溶融する溶融工程と、溶融状態の上記Ｔ ｉ Ｎ ｉ
Ｃｕ合金を急冷凝固する急冷工程とを有し、上記急冷工
程は上記Ｔ ｉ Ｎ ｉ Ｃｕ合金母相からＴ１Ｃｕ相
析出を抑制することを特徴とする形状記憶合金の製造方
法が得られる。[Means for Solving the Problems] According to the present invention, a melting step of melting a T i N i Cu alloy ingot, and the above-mentioned T i N i in a molten state are performed.
A method for manufacturing a shape memory alloy is obtained, which comprises a quenching step of rapidly solidifying a Cu alloy, and the quenching step suppresses precipitation of a T1Cu phase from the T i N i Cu alloy matrix.
ここで、本発明においては、Ｔ ｉ Ｎ ｉ Ｃｕ合金
とはＴ１５０原子パーセント、Ｎ１を最低で１５原子パ
ーセント、およびＣｕを１０〜３０原子パーセント、な
らびにＣｒ、Ｆｅおよび■から選択した少なくとも１種
の元素を０．０１〜５原子パーセントを含むＴ ｉ Ｎ
ｉ Ｃｕ基形状記憶合金をいう、また、急冷工程は、
Ｔ ｉ Ｎ ｉ Ｃｕ合金母相からのＴ ｉ Ｃｕの析
出を抑え、このことにより所要寸法製作可能にし、さら
に溶融状態条または線状に急冷凝固させることが可能と
なる。Here, in the present invention, the TiNiCu alloy is T150 atomic percent, N1 at least 15 atomic percent, Cu 10 to 30 atomic percent, and at least one selected from Cr, Fe, and ■. T i N containing 0.01 to 5 atomic percent of the element
i Cu-based shape memory alloy, and the quenching process is
Precipitation of T i Cu from the T i N i Cu alloy parent phase is suppressed, thereby making it possible to manufacture the desired dimensions and further making it possible to rapidly solidify into a molten state strip or linear shape.
本発明においては、形状記憶合金は一般的に次式によっ
て表わされる。In the present invention, the shape memory alloy is generally represented by the following formula.
Ｔｉ Ｎｉ Ｃｕ 、およびＴ ｉ 、、０−
、−。Ti Ni Cu , and T i , 0-
,-.
５０ ５０−ｘ Ｘ
Ｃｕ Ｙ
ｙ
ｙはＣｒ、Ｆｅ、Ｖのうち少くとも１種で入は入；１０
〜３５の範囲内、ｙは０．５〜５．０の範囲内である。50 50-x X Cu Y y y is at least one of Cr, Fe, and V; 10
~35, and y is within the range of 0.5 to 5.0.
ここで、本発明においてはＣｕ添加量１０原子パーセン
ト未満では、従来法によっても容易に合金は加工され、
かつ、本発明の目的であるしステリシスの小さい合金素
子を得ることはできない。Here, in the present invention, when the amount of Cu added is less than 10 atomic percent, the alloy can be easily processed even by conventional methods.
Moreover, it is not possible to obtain an alloy element with small steresis, which is the object of the present invention.
また、Ｃｕ添加量が３０原子パーセントを越えると、Ｔ
ｉ Ｃｕ析出は顕著に認めらないが、曲げ特性が悪く
なる。Moreover, when the amount of Cu added exceeds 30 atomic percent, T
Although no significant Cu precipitation was observed, the bending properties deteriorated.
更に、本発明においては、Ｃｒ、Ｆｅ、およびＶ添加は
いずれも変態温度を低下される効果を有するが、５原子
パーセントを越えると、曲げ特性の劣化と同時に変態温
度が一１００℃以下となり、バネ材料としては実用的で
はない。Furthermore, in the present invention, the addition of Cr, Fe, and V all have the effect of lowering the transformation temperature, but when the addition exceeds 5 atomic percent, the transformation temperature decreases to 1100°C or less at the same time as the bending properties deteriorate. It is not practical as a spring material.
［実施例］ 以下、本発明の実施例を図面を参照して説明する。[Example] Embodiments of the present invention will be described below with reference to the drawings.
第１図は本発明の実施例に係る形状記憶合金の３！！遠
方法を示す。FIG. 1 shows shape memory alloy 3 according to an embodiment of the present invention. ! Show the distance method.
図のような片ロール装置で、アルゴン雰囲気中にて黒鉛
ノズル１中で表−１の化学組成の合金インゴット小片を
再溶解し、１．Ｏ気圧の噴出圧で、１０００ ｒ ｐ
ｍの速度で回転するステンレス製ロール３の表面に噴出
させ巾５閣厚さ０．０２ｍの薄帯を製造した。Using a single roll device as shown in the figure, a small piece of alloy ingot having the chemical composition shown in Table 1 was remelted in a graphite nozzle 1 in an argon atmosphere.1. 1000 r p with an injection pressure of O atmosphere
A thin strip having a width of 5 m and a thickness of 0.02 m was produced by jetting the mixture onto the surface of a stainless steel roll 3 rotating at a speed of 5 m.
以下余白
表−１
表２はこのように合金インゴット１〜１９より得られた
薄帯１０を室温で７字型に曲げ、■曲げ破断の有無を調
べた結果で、表２の薄帯試料番号は表１のインゴット番
号にそれぞれ対応している。Margin table below - 1 Table 2 shows the results of bending the ribbon 10 obtained from alloy ingots 1 to 19 into a figure 7 shape at room temperature and examining the presence or absence of bending breakage. correspond to the ingot numbers in Table 1, respectively.
以下余白
表−２
臥下余日
表−２にように本発明の実施例の方法より得られた薄帯
番号１〜６１番号８〜１０．番号１２〜１３、番号１６
〜１８はいずれも破断は認められなかった。As shown in Margin Table-2 Table-2 below, the ribbon numbers 1 to 61 and the numbers 8 to 10 obtained by the method of the embodiment of the present invention are shown in Table 2. Number 12-13, number 16
No breakage was observed in any of samples 1 to 18.
次に本発明の実施例の方法により得られた薄帯を示差走
査熱量計（ＤＳＣ）によってマルテンサイト変態温度（
ＭＳ）、および逆変態温度（Ａｓ）を測定した。その結
果を表−２に示す。Next, the ribbon obtained by the method of the example of the present invention was measured using a differential scanning calorimeter (DSC) at the martensitic transformation temperature (
MS) and reverse transformation temperature (As) were measured. The results are shown in Table-2.
本発明により得られた合金は、薄帯試料１〜６゜薄帯試
料８〜１０．薄帯１２〜１３．薄帯１６〜１８はいずれ
もマルテンサイト変態温度と逆変態温度の近接が認めら
れた。従って本発明の実施例による方法により得られた
形状記憶合金を感温素子として使用する場合、しステリ
シスの小さい素子の提供が可能である。また、Ｔ ｉ
Ｃｕ析出物の有無を調べるために、光学顕微鏡およびＸ
線マイクロアナライザーで形状記憶合金薄帯を調べたが
、いずれも顕著なＴ ｉ Ｃｕの析出は認められなかっ
た６表−２は、試料番号は表−１の合金の化学組成を示
す試料番号と同じでこの合金の試料は次のようにｉ遺さ
れた。The alloy obtained according to the present invention was used for ribbon samples 1 to 6 degrees and ribbon samples 8 to 10 degrees. Thin strips 12-13. In all ribbons 16 to 18, it was observed that the martensitic transformation temperature and the reverse transformation temperature were close to each other. Therefore, when the shape memory alloy obtained by the method according to the embodiment of the present invention is used as a temperature-sensitive element, it is possible to provide an element with small steresis. Also, T i
To examine the presence or absence of Cu precipitates, optical microscopy and
The shape memory alloy ribbons were examined using a wire microanalyzer, but no significant TiCu precipitation was observed in any of them.6 In Table 2, the sample number is the same as the sample number indicating the chemical composition of the alloy in Table 1. A sample of this alloy was also prepared as follows.
高周波真空溶解によって溶融され、鉄板上に鋳込まれた
Ｔ ｉ Ｎ ｉ Ｃｕ合金インゴットを２分割した。一
方は本発明のための供試材とされた０表−１に実施に用
いられた合金インゴットの組成を示している。比較の為
に同様な方法により得られたＴ ｉ Ｎ ｉ Ｃｕ合金
インゴットの他方を従来法によって熱間加工および冷間
加工（９００℃での焼なまし、および１０％の冷間加工
率）し、加工性の良否判定した。A T i N i Cu alloy ingot that was melted by high frequency vacuum melting and cast on an iron plate was divided into two parts. On the other hand, Table 0-1 shows the composition of the alloy ingot used as a test material for the present invention. For comparison, the other T i N i Cu alloy ingot obtained by the same method was hot worked and cold worked (annealed at 900 ° C. and cold working rate of 10%) by the conventional method. , the workability was judged.
すなわち、表−１に示される化学組成の合金インゴット
試料１〜１９を９００℃で２時間の均−化処理分、９０
０℃の温度で熱間加工を行った。That is, alloy ingot samples 1 to 19 having the chemical compositions shown in Table 1 were equalized at 900°C for 2 hours, and 90%
Hot working was carried out at a temperature of 0°C.
その結果、試料１．２は容易に加工された。試料３は耳
割れを生じたがかろうじて加工された。また試料４〜１
９は全く加工されなかった。As a result, sample 1.2 was easily processed. Sample 3 developed edge cracking, but was barely processed. Also, samples 4 to 1
9 was not processed at all.
次に加工率１０％毎に９００°Ｃで３０分間の焼なまし
を繰り返しながら０．０２＋ｍ＋の板厚まで加工された
。試料１，２は容易に加工されたが、試料３はかろうじ
て加工された。Next, the plate was processed to a thickness of 0.02+m+ while repeating annealing at 900°C for 30 minutes at every 10% processing rate. Samples 1 and 2 were easily processed, but sample 3 was barely processed.
それらの結果を表２に示している。The results are shown in Table 2.
第２図は本発明の他の実施例に係る急冷凝固薄帯を得る
方法の説明図である。FIG. 2 is an explanatory diagram of a method for obtaining a rapidly solidified ribbon according to another embodiment of the present invention.
この図において、黒鉛ノズル１１中から実施例に係る形
状記憶合金の溶湯１２を噴出させて、噴出した溶湯は、
１対のロール１３及び１３′間に挾まれて急冷凝固薄帯
となる。In this figure, the molten metal 12 of the shape memory alloy according to the example is ejected from the graphite nozzle 11, and the ejected molten metal is as follows.
It is sandwiched between a pair of rolls 13 and 13' to form a rapidly solidified ribbon.
第３図は本発明のもう１つの実施例に係る急冷凝固薄帯
を得る方法の説明図である。FIG. 3 is an explanatory diagram of a method for obtaining a rapidly solidified ribbon according to another embodiment of the present invention.
この図において、黒鉛ノズル１中から、本発明の実施例
に係る形状記憶合金の溶湯２２を噴出させて、噴出した
溶湯は、回転するカップ状の内壁に反射して薄帯となる
。In this figure, a molten metal 22 of a shape memory alloy according to an embodiment of the present invention is ejected from a graphite nozzle 1, and the ejected molten metal is reflected on the inner wall of a rotating cup shape to form a thin ribbon.
以上、本発明の実施例に係る形状記憶合金の製造方法は
、第１図〜第３図のようであるが、これらに限定されな
い。As described above, the method for manufacturing a shape memory alloy according to an embodiment of the present invention is shown in FIGS. 1 to 3, but is not limited thereto.
［発明の効果］
以上説明したように、本発明によれば、ＴｉＮｉＣｕ合
金の溶融状態からの急冷工程によって、Ｔ ｉ Ｎ ｉ
Ｃｕ合金母相がらしステリシスの小さな形状記憶バネ
を容易に製造でさるとともに、安価なアクチュエータ等
の靭性のすぐれた形状記憶合金の製造方法の提供が可能
である。[Effects of the Invention] As explained above, according to the present invention, T i Ni
It is possible to easily manufacture a shape memory spring with a small steresis using a Cu alloy matrix, and also to provide a method for manufacturing a shape memory alloy with excellent toughness such as an inexpensive actuator.
第１図は本発明の一実施例に係る形状記憶合金の急冷凝
固薄帯を製造する方法を示す説明図、第２図および第３
図は本発明の他の実施例に係る形状記憶合金の急冷凝固
薄帯を製造する方法を示す説明図である。
１・・・ノズル、２・・・溶湯、３．３′・・・ロール
、１０．２０．３０・・・薄帯。FIG. 1 is an explanatory diagram showing a method for producing a rapidly solidified ribbon of a shape memory alloy according to an embodiment of the present invention, and FIGS.
The figure is an explanatory diagram showing a method for producing a rapidly solidified ribbon of a shape memory alloy according to another embodiment of the present invention. 1... Nozzle, 2... Molten metal, 3.3'... Roll, 10.20.30... Thin ribbon.
Claims (1)
、溶融状態の上記ＴｉＮｉＣｕ合金を急冷凝固する急冷
工程とを有し、上記急冷工程は上記ＴｉＮｉＣｕ合金母
相からのＴｉＣｕの析出を抑制することを特徴とする形
状記憶合金の製造方法。 ２、上記急冷工程は、溶融状態の上記ＴｉＮｉＣｕ合金
を、回転する円筒面に噴出して急冷凝固して条又は線状
に成形する急冷工程とを有することを特徴とする第１の
請求項記載の形状記憶合金の製造方法。 ３、上記ＴｉＮｉＣｕ合金インゴットは、４９〜５１原
子パーセントの範囲内のＴｉ、１０〜３０原子パーセン
トの範囲内のＣｕ、及び ０．０１〜５．０原子パーセントの範囲内のＶ、Ｃｒ、
Ｆｅの少くとも１種、残部Ｎｉを有することを特徴とす
る第１又は第２の項記載の形状記憶合金の製造方法。[Claims] 1. A melting process for melting a TiNiCu alloy ingot, and a rapid cooling process for rapidly solidifying the TiNiCu alloy in a molten state, and the rapid cooling process prevents precipitation of TiCu from the TiNiCu alloy matrix. A method for manufacturing a shape memory alloy characterized by suppressing the shape. 2. The quenching step includes a quenching step in which the molten TiNiCu alloy is injected onto a rotating cylindrical surface and rapidly solidified to form a strip or line. A method for producing shape memory alloys. 3. The TiNiCu alloy ingot contains Ti within the range of 49 to 51 atomic percent, Cu within the range of 10 to 30 atomic percent, and V, Cr within the range of 0.01 to 5.0 atomic percent,
2. The method for producing a shape memory alloy according to the first or second item, characterized in that the shape memory alloy contains at least one type of Fe and the remainder is Ni.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63037406A JP2589125B2 (en) | 1988-02-22 | 1988-02-22 | Manufacturing method of shape memory alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63037406A JP2589125B2 (en) | 1988-02-22 | 1988-02-22 | Manufacturing method of shape memory alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH01212728A true JPH01212728A (en) | 1989-08-25 |
| JP2589125B2 JP2589125B2 (en) | 1997-03-12 |
Family
ID=12496644
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP63037406A Expired - Fee Related JP2589125B2 (en) | 1988-02-22 | 1988-02-22 | Manufacturing method of shape memory alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2589125B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US8092616B2 (en) | 2004-03-11 | 2012-01-10 | Japan Science And Technology Agency | Method for producing a giant magnetostrictive alloy |
| CN116005035A (en) * | 2022-12-30 | 2023-04-25 | 西安理工大学 | Shape memory alloy and preparation method thereof |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS59104459A (en) * | 1982-12-07 | 1984-06-16 | Sumitomo Electric Ind Ltd | Preparation of shape memory alloy material |
-
1988
- 1988-02-22 JP JP63037406A patent/JP2589125B2/en not_active Expired - Fee Related
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS59104459A (en) * | 1982-12-07 | 1984-06-16 | Sumitomo Electric Ind Ltd | Preparation of shape memory alloy material |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US8092616B2 (en) | 2004-03-11 | 2012-01-10 | Japan Science And Technology Agency | Method for producing a giant magnetostrictive alloy |
| CN116005035A (en) * | 2022-12-30 | 2023-04-25 | 西安理工大学 | Shape memory alloy and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2589125B2 (en) | 1997-03-12 |
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