US20090071577A1 - Process for making ti-ni based functionally graded alloys and ti-ni based functionally graded alloys produced thereby - Google Patents

Process for making ti-ni based functionally graded alloys and ti-ni based functionally graded alloys produced thereby Download PDF

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US20090071577A1
US20090071577A1 US12/299,113 US29911306A US2009071577A1 US 20090071577 A1 US20090071577 A1 US 20090071577A1 US 29911306 A US29911306 A US 29911306A US 2009071577 A1 US2009071577 A1 US 2009071577A1
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alloys
functionally graded
deformation
temperature
temperature gradient
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Tae-Hyun Nam
Ki-Won Kim
Hyo-Jun Ahn
Kwon-Koo Cho
Jou-Hyeon Ahn
Gyu-Bong Cho
Yinong Liu
Jung-Moo Lee
Yun-jung Lee
Cheol-Am Yu
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Industry Academic Cooperation Foundation of GNU
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Assigned to INDUSTRY-ACADEMIC COOPERATION FOUNDATION GYEONGSANG NATIONAL UNIVERSITY reassignment INDUSTRY-ACADEMIC COOPERATION FOUNDATION GYEONGSANG NATIONAL UNIVERSITY ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: AHN, HYO-JUN, AHN, JOU-HYEON, CHO, GYU-BONG, CHO, KWON-KOO, KIM, KI-WON, LEE, JUNG-MOO, LEE, YUN-JUNG, LIU, YINONG, NAM, TAE-HYUN, YU, CHEOL-AM
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    • 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
    • C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
    • 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
    • C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
    • C22F1/18—High-melting or refractory metals or alloys based thereon
    • C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C14/00—Alloys based on titanium
    • 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

Definitions

  • the present invention relates to Ti—Ni based functionally graded alloys, and more particularly, to a process for making Ti—Ni based functionally graded alloys and Ti—Ni based functionally graded alloys produced thereby, in which Ti—Ni based alloys are cold worked, annealed under a predetermined temperature gradient, and functionally graded.
  • Ti—Ni based shape memory alloys are rapidly deformed at a Martensite transformation start temperature (Ms) if being cold worked, annealed at a predetermined temperature, and cooled with being given a load. After that, if a temperature elevates, a recovery of rapid deformation occurs at an austenite deformation start temperature (As) (Referring to FIG. 1 ).
  • Ms Martensite transformation start temperature
  • As austenite deformation start temperature
  • shape memory alloys are being applied to various on-off switching actuators using a phenomenon in which a rapid deformation is generated at a specific temperature and recovered.
  • the Ti—Ni based shape memory alloys are applied as an actuator element for robot, they have to enable a position control by proportional control.
  • the conventional Ti—Ni based shape memory alloys are rapidly deformed at a specific temperature, they were appropriate for an on-off switching actuator, but were inappropriate for a proportional control actuator.
  • the present invention is a result of making efforts to fix the defects in which the shape memory alloys are rapidly deformed at a specific temperature.
  • the present invention is directed to a process for making Ti—Ni based functionally graded alloys and Ti—Ni based functionally graded alloys produced thereby that substantially obviate one or more of the problems due to limitations and disadvantages of the related art.
  • An object of the present invention is to provide a process for making Ti—Ni based functionally graded alloys, for facilitating a proportional control by consecutively varying a transformation temperature (Ms and As) within the same Ti—Ni based alloys and generating gradual deformation over a wide range of temperature (Referring to FIG. 2 ).
  • Ms and As transformation temperature
  • Cold working may be performed by 25% to 65% and annealing may be performed under a temperature gradient of 823 K to 466 K.
  • Ti—Ni based functionally graded alloys enabling a proportional control, made according to the process.
  • a deformation-rate recovery speed of the alloys may be reduced to 1/30 to 1/100.
  • Ti—Ni based alloys processed according to the present invention has a shape memory effect and an ultra elasticity and at the same time, a deformation-rate recovery speed gets smaller 1/30 to 1/100 compared to that of conventional alloys.
  • the Ti—Ni based alloys having a low deformation-rate recovery speed is easy in position control through proportional control.
  • FIG. 1 is a graph illustrating a deformation-temperature curve for shape memory alloys heat-treated at a predetermined time
  • FIG. 2 is a graph illustrating a deformation-temperature curve for functionally graded shape memory alloys
  • FIG. 3 shows differential scanning thermal analysis curves for Ti-50.0Ni (at %) alloys processed by solution heat treatment and Ti-50.0 (at %) alloys processed by a temperature gradient heat treatment;
  • FIG. 4 is a result of arrangement of Ms-by-positions of a wire obtained by 25% cold working and annealing Ti-50.0Ni (at %) alloys under a temperature gradient of 658 K to 466 K according to the present invention
  • FIG. 5 is a result of arrangement of Ms-by-positions of a wire obtained by 25% cold working and annealing Ti-50.0Ni (at %) alloys under a temperature gradient of 823 K to 658 K according to the present invention
  • FIG. 6 is a result of arrangement of Ms-by-positions of a wire obtained by 65% cold working and annealing Ti-50.0Ni (at %) alloys under a temperature gradient of 823 K to 658 K according to the present invention
  • FIG. 7 is a graph illustrating a deformation (e)-temperature (T) curve of Ti-50.0Ni (at %) alloys processed by solution heat treatment according to the present invention.
  • FIG. 8 is a graph illustrating a deformation (e)-temperature (T) curve of a wire obtained by 25% cold working and annealing Ti-50.2 (at %) alloys under a temperature gradient of 658 K to 466 K according to the present invention.
  • FIG. 9 is a graph illustrating a deformation (e)-temperature (T) curve of a wire obtained by 65% cold working and annealing Ti-50.2 (at %) alloys under a temperature gradient of 658 K to 466 K according to the present invention.
  • FIG. 3( a ) shows a differential scanning thermal analysis curve of Ti-50.0Ni (at %) alloys processed by solution heat treatment.
  • a peak appears one by one during cooling and heating. This is caused by B2 (Cubic)-B19′ (Monoclinic) Martensite transformation.
  • FIGS. 3( b ), 3 ( c ), 3 ( d ), and 3 ( e ) show results of differential scanning thermal analysis of samples taken at positions shown in FIG. 3( f ) from Ti-50.0Ni alloys that are 25% cold worked and annealed under a temperature gradient of 658 K to 466 K. Wide peaks were observed at the time of cooling and heating. Particularly, it can be appreciated that a peak of a sample taken in a low annealing temperature region is wider.
  • Ti-50.0Ni (at %) alloys were cold worked within a range of 25% to 65% before being heat-treated under a temperature gradient. This is because if cold working is performed at less than 25%, a characteristic of functionally grading cannot be obtained due to a small variation of temperature after heat treatment and cold working of more than 65% is impossible.
  • the temperature gradient heat treatment was performed using a heat treatment furnace having a temperature gradient of 823 K to 466 K. However, in the case of 65% cold working, a heat treatment was performed at a temperature gradient of 823 K to 658 K. This is because if a heat treatment is performed at a temperature gradient of 658 K to 466 K, a deformation ratio is small less than 1% and thus is inappropriate for an actuator element.
  • Ti-50.0Ni (at %) alloys were used as Ti—Ni based alloys.
  • other Ti—Ni based alloys can be also used and even in such a case, a similar result can be obtained.
  • Ti-50.0Ni (at %) alloy wire having a length of 150 mm is 25% cold worked and annealed under a temperature gradient of 658 K to 466 K.
  • a sample was taken at an interval of 5 mm and processed by differential scanning thermal analysis.
  • a result of arrangement of measured Ms was shown in FIG. 4 . It can be appreciated that Ms consecutively varies as a position varies. In case where a wire having a length of 150 mm is 25% cold worked and annealed under the temperature gradient of 658 K to 466 K, a variation of Ms is equal to about 19 K.
  • Ti-50.0Ni (at %) alloy wire having a length of 150 mm is 25% cold worked and annealed under a temperature gradient of 823 K to 658 K.
  • a sample was taken at an interval of 5 mm and processed by differential scanning thermal analysis.
  • a result of arrangement of measured Ms was shown in FIG. 5 . It can be appreciated that Ms consecutively varies as a position varies. In case where a wire having a length of 150 mm is 25% cold worked and annealed under the temperature gradient of 823 K to 658 K, a variation of Ms is equal to about 14 K.
  • Ti-50.0Ni (at %) alloy wire having a length of 150 mm is 65% cold worked and annealed under a temperature gradient of 823 K to 658 K.
  • a sample was taken at an interval of 5 mm and processed by differential scanning thermal analysis.
  • a result of arrangement of measured Ms was shown in FIG. 6 . It can be appreciated that Ms consecutively varies as a position varies. In case where a wire having a length of 150 mm is 65% cold worked and annealed under the temperature gradient of 823 K to 658 K, a variation of Ms is equal to about 60 K.
  • a deformation (e)-temperature (T) curve for Ti-50.0Ni (at %) alloys processed by solution heat treatment was shown in FIG. 7 . If alloys are cooled under a load strain of 80 MPa, there occurs deformation at a temperature expressed by Ms. This is caused by B2 (Cubic)-B19′ (Monoclinic) Martensite deformation. Meantime, if alloys are heated, deformation is recovered at a temperature expressed by As. This is caused by B19′-B2 austenite deformation. A deformation-rate recovery speed (d ⁇ /dT) at the time of heating is equal to about 1%/K.
  • Ti-50.0 (at %) alloy wire was 25% cold worked and annealed under a temperature gradient of 658 K to 466 K.
  • a deformation ( ⁇ )-temperature (T) curve of the processed wire was shown in FIG. 8 . If alloys are cooled under a load strain of 80 MPa, there occurs deformation at a temperature expressed by Ms. This is caused by B2 (Cubic)-B19′ (Monoclinic) Martensite deformation. Meantime, if alloys are heated, deformation is recovered at a temperature expressed by As. This is caused by B19′-B2 austenite deformation. A deformation-rate recovery speed (d ⁇ /dT) at the time of heating is equal to about 0.03%/K.
  • Ti-50.0 (at %) alloy wire was 65% cold worked and annealed under a temperature gradient of 658 K to 466 K.
  • a deformation ( ⁇ )-temperature (T) curve of the processed wire was shown in FIG. 9 . If alloys are cooled under a load strain of 80 MPa, there occurs deformation at a temperature expressed by Ms. This is caused by B2 (Cubic)-B19′ (Monoclinic) Martensite deformation. Meantime, if alloys are heated, deformation is recovered at a temperature expressed by As. This is caused by B19′-B2 austenite deformation. A deformation-rate recovery speed (d ⁇ /dT) at the time of heating is equal to about 0.01%/K. If the 65% cold worked alloys had been heated within a range of temperature of 658 K to 466 K, they were inappropriate for an actuator element because a deformation rate is so small less than 1%.
  • a deformation-rate recovery speed is equal to 0.03%/K to 0.01%/K and gets smaller about 1/30 to 1/100 compared to a recovery speed of 1%/K when being annealed at a predetermined temperature. Accordingly, it can be appreciated that Ti—Ni based alloys for proportional control can be made in a method of annealing under a temperature gradient after cold-working.
  • Ti—Ni based alloys processed according to the present invention has a shape memory effect and an ultra elasticity and at the same time, a deformation-rate recovery speed gets smaller 1/30 to 1/100 compared to that of conventional alloys.
  • the Ti—Ni based alloys having a low deformation-rate recovery speed is easy in position control through proportional control and therefore, is useful for an industrial field requiring a precise position control such as an actuator for robot.

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  • Metallurgy (AREA)
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  • Physics & Mathematics (AREA)
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US12/299,113 2006-06-05 2006-07-25 Process for making ti-ni based functionally graded alloys and ti-ni based functionally graded alloys produced thereby Abandoned US20090071577A1 (en)

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KR1020060050410A KR100807393B1 (ko) 2006-06-05 2006-06-05 Ｔｉ－Ｎｉ계 경사기능 합금의 제조방법 및 그로부터제조된 Ｔｉ－Ｎｉ계 경사기능 합금
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Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN102828066A (zh) * 2012-09-07 2012-12-19 哈尔滨工程大学 功能连续梯度TiNi形状记忆合金的制备方法
US20130239565A1 (en) * 2012-03-16 2013-09-19 GM Global Technology Operations LLC Spatially graded sma actuators
CN104399750A (zh) * 2014-10-23 2015-03-11 哈尔滨工程大学 一种TiNi记忆合金板材的制备方法
CN110157952A (zh) * 2019-07-01 2019-08-23 中国工程物理研究院机械制造工艺研究所 梯度功能NiTiHf高温记忆合金及其制备方法
US10532996B2 (en) 2011-05-12 2020-01-14 Proteostasis Therapeutics, Inc. Proteostasis regulators
CN110842022A (zh) * 2019-12-06 2020-02-28 东北大学 一种记忆合金纳米叠层Ni/Ti预制坯的制备方法
CN111041421A (zh) * 2019-12-30 2020-04-21 哈尔滨工业大学 一种形状记忆合金径向梯度薄膜及其制备方法

Families Citing this family (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN107030111B (zh) * 2017-04-17 2019-07-02 东北大学 一种等厚度超细晶tc4钛合金板材的制备方法
CN110193934B (zh) * 2019-05-08 2021-12-28 西安交通大学 激光选区烧结中在线退火调控聚合物性能的方法与设备

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US4637846A (en) * 1982-06-29 1987-01-20 Sumitomo Electric Industries, Ltd. Nickel-titanium-beryllium alloy wire
US4896955A (en) * 1983-12-06 1990-01-30 Cvi/Beta Ventures, Inc. Eyeglass frame including shape-memory elements
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JPH07107184B2 (ja) * 1989-08-24 1995-11-15 裕一 中里 アクチュエータ用Ｔｉ―Ｎｉ形状記憶合金からなる物品とその製造方法
JPH0796036A (ja) * 1993-09-28 1995-04-11 Tokin Corp カテーテル
JP2895824B1 (ja) 1998-01-21 1999-05-24 株式会社古河テクノマテリアル ＮｉＴｉ系形状記憶合金製釣り糸とその製造方法
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US4637846A (en) * 1982-06-29 1987-01-20 Sumitomo Electric Industries, Ltd. Nickel-titanium-beryllium alloy wire
US4896955A (en) * 1983-12-06 1990-01-30 Cvi/Beta Ventures, Inc. Eyeglass frame including shape-memory elements
US4896955B1 (en) * 1983-12-06 1991-05-21 Eyeglass frame including shape-memory elements
US6149742A (en) * 1998-05-26 2000-11-21 Lockheed Martin Corporation Process for conditioning shape memory alloys

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US10532996B2 (en) 2011-05-12 2020-01-14 Proteostasis Therapeutics, Inc. Proteostasis regulators
US20130239565A1 (en) * 2012-03-16 2013-09-19 GM Global Technology Operations LLC Spatially graded sma actuators
CN102828066A (zh) * 2012-09-07 2012-12-19 哈尔滨工程大学 功能连续梯度TiNi形状记忆合金的制备方法
CN104399750A (zh) * 2014-10-23 2015-03-11 哈尔滨工程大学 一种TiNi记忆合金板材的制备方法
CN110157952A (zh) * 2019-07-01 2019-08-23 中国工程物理研究院机械制造工艺研究所 梯度功能NiTiHf高温记忆合金及其制备方法
CN110842022A (zh) * 2019-12-06 2020-02-28 东北大学 一种记忆合金纳米叠层Ni/Ti预制坯的制备方法
CN111041421A (zh) * 2019-12-30 2020-04-21 哈尔滨工业大学 一种形状记忆合金径向梯度薄膜及其制备方法
CN111041421B (zh) * 2019-12-30 2022-04-22 哈尔滨工业大学 一种形状记忆合金径向梯度薄膜及其制备方法

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KR100807393B1 (ko) 2008-02-28
JP2009536265A (ja) 2009-10-08
WO2007142380A1 (en) 2007-12-13

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