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US20090218013A1 - High temperature shape memory alloy, actuator and motor - Google Patents

High temperature shape memory alloy, actuator and motor Download PDF

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Publication number
US20090218013A1
US20090218013A1 US12/235,528 US23552808A US2009218013A1 US 20090218013 A1 US20090218013 A1 US 20090218013A1 US 23552808 A US23552808 A US 23552808A US 2009218013 A1 US2009218013 A1 US 2009218013A1
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Prior art keywords
mol
alloy
shape memory
concentration
alloys
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Abandoned
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US12/235,528
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English (en)
Inventor
Shuichi Miyazaki
Heeyoung Kim
Yoshinari Takeda
Masanari Tomozawa
Buenconsejo Pio
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University of Tsukuba NUC
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University of Tsukuba NUC
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Assigned to UNIVERSITY OF TSUKUBA reassignment UNIVERSITY OF TSUKUBA ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: KIM, HEEYOUNG, MIYAZAKI, SHUICHI, PIO, BUENCONSEJO, TAKEDA, YOSHINARI, TOMOZAWA, MASANARI
Publication of US20090218013A1 publication Critical patent/US20090218013A1/en
Abandoned legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C27/00—Alloys based on rhenium or a refractory metal not mentioned in groups C22C14/00 or C22C16/00
    • C22C27/02—Alloys based on vanadium, niobium, or tantalum
    • 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
    • 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
    • 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
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F02—COMBUSTION ENGINES; HOT-GAS OR COMBUSTION-PRODUCT ENGINE PLANTS
    • F02K—JET-PROPULSION PLANTS
    • F02K1/00—Plants characterised by the form or arrangement of the jet pipe or nozzle; Jet pipes or nozzles peculiar thereto
    • F02K1/54—Nozzles having means for reversing jet thrust
    • F02K1/76—Control or regulation of thrust reversers
    • F02K1/763—Control or regulation of thrust reversers with actuating systems or actuating devices; Arrangement of actuators for thrust reversers
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F03—MACHINES OR ENGINES FOR LIQUIDS; WIND, SPRING, OR WEIGHT MOTORS; PRODUCING MECHANICAL POWER OR A REACTIVE PROPULSIVE THRUST, NOT OTHERWISE PROVIDED FOR
    • F03G—SPRING, WEIGHT, INERTIA OR LIKE MOTORS; MECHANICAL-POWER PRODUCING DEVICES OR MECHANISMS, NOT OTHERWISE PROVIDED FOR OR USING ENERGY SOURCES NOT OTHERWISE PROVIDED FOR
    • F03G7/00—Mechanical-power-producing mechanisms, not otherwise provided for or using energy sources not otherwise provided for
    • F03G7/06—Mechanical-power-producing mechanisms, not otherwise provided for or using energy sources not otherwise provided for using expansion or contraction of bodies due to heating, cooling, moistening, drying or the like
    • F03G7/061—Mechanical-power-producing mechanisms, not otherwise provided for or using energy sources not otherwise provided for using expansion or contraction of bodies due to heating, cooling, moistening, drying or the like characterised by the actuating element
    • F03G7/0614—Mechanical-power-producing mechanisms, not otherwise provided for or using energy sources not otherwise provided for using expansion or contraction of bodies due to heating, cooling, moistening, drying or the like characterised by the actuating element using shape memory elements
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F03—MACHINES OR ENGINES FOR LIQUIDS; WIND, SPRING, OR WEIGHT MOTORS; PRODUCING MECHANICAL POWER OR A REACTIVE PROPULSIVE THRUST, NOT OTHERWISE PROVIDED FOR
    • F03G—SPRING, WEIGHT, INERTIA OR LIKE MOTORS; MECHANICAL-POWER PRODUCING DEVICES OR MECHANISMS, NOT OTHERWISE PROVIDED FOR OR USING ENERGY SOURCES NOT OTHERWISE PROVIDED FOR
    • F03G7/00—Mechanical-power-producing mechanisms, not otherwise provided for or using energy sources not otherwise provided for
    • F03G7/06—Mechanical-power-producing mechanisms, not otherwise provided for or using energy sources not otherwise provided for using expansion or contraction of bodies due to heating, cooling, moistening, drying or the like
    • F03G7/061—Mechanical-power-producing mechanisms, not otherwise provided for or using energy sources not otherwise provided for using expansion or contraction of bodies due to heating, cooling, moistening, drying or the like characterised by the actuating element
    • F03G7/0616—Mechanical-power-producing mechanisms, not otherwise provided for or using energy sources not otherwise provided for using expansion or contraction of bodies due to heating, cooling, moistening, drying or the like characterised by the actuating element characterised by the material or the manufacturing process, e.g. the assembly
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
    • F05C—INDEXING SCHEME RELATING TO MATERIALS, MATERIAL PROPERTIES OR MATERIAL CHARACTERISTICS FOR MACHINES, ENGINES OR PUMPS OTHER THAN NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES
    • F05C2201/00—Metals
    • F05C2201/04—Heavy metals
    • F05C2201/0433—Iron group; Ferrous alloys, e.g. steel
    • F05C2201/0466—Nickel
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
    • F05C—INDEXING SCHEME RELATING TO MATERIALS, MATERIAL PROPERTIES OR MATERIAL CHARACTERISTICS FOR MACHINES, ENGINES OR PUMPS OTHER THAN NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES
    • F05C2201/00—Metals
    • F05C2201/90—Alloys not otherwise provided for
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
    • F05D—INDEXING SCHEME FOR ASPECTS RELATING TO NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES, GAS-TURBINES OR JET-PROPULSION PLANTS
    • F05D2300/00—Materials; Properties thereof
    • F05D2300/50—Intrinsic material properties or characteristics
    • F05D2300/505—Shape memory behaviour

Definitions

  • the present inventions relate to high temperature shape memory alloys which can be used at temperatures in excess of 100° C., as well as actuators and a motors using the shape memory alloys. More particularly, the present inventions relate to high temperature shape memory alloys with peak and reverse martensite transformation temperatures higher than 100° C., as well as actuators and motors using the shape memory alloys.
  • Ti—Ni base alloys are widely known shape memory alloys consisting of Titanium (Ti) and Nickel(Ni) which revert back to their original configuration upon application of heat up to their prescribed operating temperature, remembering their original shape.
  • Ti—Ni—Cu alloys are generally known to exhibit shape memory effects at temperature in the range of 200K to 360K Kokai publication Tokukai No. 2002-294371).
  • Ti—Ni—Nb alloys with martensite start temperatures (M s ) below 50° C. have also been disclosed (Patent publication No. 2539786).
  • the below mentioned alloys are generally well known as high temperature shape memory alloys obtained by adding additive elements to Ti—Ni base alloys for operation at high temperature exceeding 100° C.
  • Titanium is substituted by 0-20 mol % (atomic percent) Zirconium (Zr) to obtain a corresponding martensite start temperature (M s ) in the range of 373(K) to 550(K).
  • Titanium is substituted by 0-20 mol % Hafnium (Hf) to obtain a corresponding martensite start temperature (M s ) in the range of 373(K) to 560(K).
  • Nickel is substituted by 0-50 mol % Palladium (Pd) to obtain a corresponding martensite start temperature (M s ) from 280(K) to 800(K).
  • Nickel(Ni) is substituted by 0-50 mol % Gold(Au) to obtain a corresponding martensite start temperature (M s ) from 300(K) to 850(K).
  • Nickel is substituted by 0-50 mol % Platinum (Pt) to obtain a corresponding martensite start temperature (M s ) from 280(K) to 1300(K).
  • Ni—Al base alloys comprising 30-36 mol % Aluminum (Al) and a balance of Nickel (Ni)
  • M s martensite start temperature
  • the conventional high temperature shape memory alloys No. 1 and 2 described above are brittle and thus break easily, which results in poor machinability and lead to failure in cold working.
  • shape memory alloy No. 6 in addition to poor machinability, precipitation of Ni5Al3 weakens the structural stability of the alloy and embrittles the alloy. Therefore, repeated operation of the alloy at temperatures over 200° C. is impossible. That is to say, the alloy does not exhibit shape memory effects.
  • embodiments of the present disclosure address the problems of the prior art and provide a high temperature shape memory alloys which have good machinability and, in the meanwhile, are suitable for repeated high temperature operation.
  • a high temperature shape memory alloy is provided in Embodiment 1 to solve these technical problems, where the alloy consists of 34.7 mol %-48.5 mol % Nickel, at least one of Zirconium or Hafnium as transformation temperature increasing additive element, with a total content of 6.8 mol %-22.5 mol %; at least one of Niobium or Tantalum as machinability improving additive element, with a total content of 1 mol %-30 mol %, Boron below 2 mol %, and the balance Titanium; and impurities.
  • Embodiment 1 With respect to high temperature shape memory alloys having the components of Embodiment 1, since the alloys consist of 34.7 mol %-48.5 mol % Nickel at least one of Zirconium or Hafnium as transformation temperature increasing additive element, with a total content of 6.8 mol %-22.5 mol %, at least one of Niobium or Tantalum as machinability improving additive elements, with a total content of 1 mol %-30 mol %, Boron below 2 mol % and the balance Titanium, high transformation temperatures (peak transformation temperature (M*) or peak reverse transformation temperatures (A*)) in excess of 100° C. are obtained, and cold ductility is also improved. Consequently, Embodiment 1 provides a high temperature shape memory alloy for repeated high temperature operation with improved cold working machinability.
  • M* peak transformation temperature
  • A* peak reverse transformation temperatures
  • High temperature shape memory alloys of form 1 in Embodiment 1 consists of 6.8 mol %-22.5 mol % Zirconium as transformation temperature increasing additive elements and 3 mol %-30 mol % Niobium as machinability improving additives.
  • High temperature shape memory alloys of form 2 in Embodiment 1 consist of 6.8 mol %-18 mol % Hafnium as transformation temperature increasing additive elements and 3 mol %-20 mol % Niobium as machinability improving additive elements.
  • High temperature shape memory alloys of form 3 in Embodiment 1 consists of 6.8 mol %-20 mol % of transformation temperature increasing additive elements and 3 mol %-30 mol % Tantalum as said machinability improving additive elements.
  • Embodiment 2 An actuator is provided in Embodiment 2 to solve the above-mentioned technical problems, where the actuator is made of the high temperature shape memory alloys described in either the Embodiment 1 or forms 1 through 4 of Embodiment 1.
  • the actuator since the actuator is made of the high temperature shape memory alloy of either the Embodiment 1 or forms 1 through 4 of Embodiment 1, it is capable to perform cold working. In addition, high temperature applications are possible with the help of its high transformation temperatures and shape memory effects.
  • a motor is provided in Embodiment 3 to solve the above-mentioned technical problems, where the motor possesses a flux adjustment valve made of the high temperature shape memory alloys described in either Embodiment 1 or forms 1 through 4 of Embodiment 1.
  • the present embodiments provide shape memory alloys capable of repeated high temperature operation with high machinability.
  • FIG. 1 shows a scanning electron microscope image of alloy No. 7 in an embodiment of the present disclosure.
  • FIG. 2 shows a scanning electron microscope image of alloy No. 8 in an embodiment of the present disclosure.
  • each metallic element is measured by mol %, and then molten by means of arc melting method to make alloy ingots.
  • alloy No. 2 Ti—Ni 49.5 —Zr 10
  • alloy No. 2 has a composition expressed as 49.5 mol % Ni, 10 mol % Zr and the balance Ti (40.5 mol %).
  • step 2 the resultant alloy ingots are subjected to homogenization heat treatment for 2 hours (7.2 ks) at 950° C.
  • step 3 billets (test pieces) 15 mm long, 10 mm wide, and 1 mm thick are cut off by electric discharge machining.
  • Machinability evaluation tests were carried out to evaluate the machinability of the alloys manufactured by the above mentioned methods. Machinability evaluation tests were carried out through cold rolling at deformations up to 60%. The break rolling ratio of test pieces, with test pieces breaking down at deformations up to 60%, was measured to evaluate machinability.
  • composition of ternary Ti—Ni—Zr alloys Nos. 1 to 4 along with the mol ratio of Ti plus Zr to Ni, break rolling ratio (%), martensite peak transformation temperature (M*, ° C.) and peak reverse transformation temperature (A*, ° C.) are provided in Table 1.
  • composition of quaternary Ti—Ni—Zr—Nb alloys Nos. 5 to 7, along with the mol ratio of Ti plus Zr to Ni, break rolling ratio (%), martensite peak transformation temperature (M*, ° C.), and peak reverse transformation temperature (A*, ° C.) are shown respectively in Table 2.
  • alloys No. 5-7 are derived by fixing Ti and Zr content (mol %) of alloy No. 3, and then substituting Ni content by Nb.
  • the composition of quaternary Ti—Ni—Zr—Nb alloys Nos. 8 to 12, along with the mol ratio of Ti plus Zr to Ni, break rolling ratio (%), martensite peak transformation temperature (M*, ° C.), and peak reverse transformation temperature (A*, ° C.) are shown respectively in Table 3.
  • alloys No. 8-12 are derived by fixing the mol ratio of Ti, Ni and Zr to 35.5 mol %, 49.5%, and 15 mol % respectively, and then substituting Ti, Ni, and Zr as a whole by Nb.
  • composition of quaternary Ti—Ni—Zr—Nb alloys Nos. 13 to 17, along with the mol ratio of Ti plus Zr to Ni, break rolling ratio (%), martensite peak transformation temperature (M*, ° C.), and peak reverse transformation temperature (A*, ° C.) are shown respectively in Table 4.
  • composition of quaternary Ti—Ni—Zr—Nb alloys Nos. 18 to 26, as well as the mol ratio of Ti plus Zr to Ni, break rolling ratio (%), martensite peak transformation temperature (M*, ° C.), and peak reverse transformation temperature (A*, ° C.) are shown respectively in Table 5.
  • the composition of quaternary Ti—Ni—Hf—Nb alloys and quinary Ti—Ni—Zr—Hf—Nb Nos. 27 to 37, along with the mol ratio of Ti plus Zr and Hf to Ni, break rolling ratio (%), martensite peak transformation temperature (M*, ° C.) and peak reverse transformation temperature (A*, ° C.), are given respectively in Table 6.
  • alloys No. 28 and 29 correspond to alloys 9 and 10, respectively, in which Zr is substituted by Hf and alloy No. 30 corresponds to alloy 20 in which Zr, is substituted by Hf.
  • alloy No. 31 corresponds to alloy No. 7 in which Zr is substituted by Hf
  • alloy No. 32 corresponds to alloy No. 19, in which half of Zr content (10 mol %) is substituted by Hf.
  • the total content of Zr and Hf transformation temperature increasing additive elements
  • composition of quaternary Ti—Ni—Zr—Ta alloys Nos. 38 to 42, along with the mol ratio of Ti plus Zr to Ni, break rolling ratio (%), martensite peak transformation temperature (M*, ° C.), and peak reverse transformation temperature (A*, ° C.) are shown respectively in Table 7.
  • alloys 38-42 are derived by fixing the mol ratio of Ti, Ni and Zr to 40.5 mol %, 49.5% and 10 mol % respectively, and then substituting Ti, Ni, and Zr as a whole by Ta.
  • the composition of quaternary Ti—Ni—Zr—Ta alloys and quinary Ti—Ni—Zr—Nb—Ta, Nos. 43 to 48, along with the mol ratio of Ti plus Zr to Ni, break rolling ratio (%), martensite peak transformation temperature (M*, ° C.), and peak reverse transformation temperature (A*, ° C.) are shown respectively in Table 8.
  • the total content of Nb and Ta (machinability improving additive elements) is 10 mol % in alloy No. 48.
  • the composition of quinary Ti—Ni—Zr—Nb—B alloys Nos. 49 to 52, along with the mol ratio of Ti plus Zr to Ni, break rolling ratio (%), martensite peak transformation temperature (M*, ° C.), and peak reverse transformation temperature (A*, ° C.) are shown respectively in Table 9.
  • alloys No. 49 to 52 are derived by adding element B (Boron) into Ti—Ni—Zr—Nb based alloys.
  • the composition of Ti—Ni—Zr—Hf—Nb—Ta—B based multi-component alloys No. 53 to 55, along with the mol ratio of Ti plus Zr and Hf to Ni, break rolling ratio (%), martensite peak transformation temperature (M*, ° C.), and peak reverse transformation temperature (A*, ° C.), are shown in Table 10.
  • FIG. 1 shows a scanning electron microscope image of alloy No. 7 in an embodiment of the present disclosure.
  • alloys No. 5 to 7 are suitable for high temperature operation as high temperature shape memory alloys. Furthermore, even with improved break rolling ratio, existence of a large amount of fine cracks are observed in alloys No. 5 to 7. As shown in FIG. 1 of the SEM image by Scanning Electric Microscope, together with the hard brittle Laves phase that forms in alloy No. 7 after rolling, the soft ⁇ phase liable to plastic deformation precipitates, which hinders the development of cracks, appeared on the interfaces of said Laves phase. As a result, machinability is improved.
  • FIG. 2 shows a scanning electron microscope image of alloy No. 8 in embodiment of the present disclosure.
  • alloys Nos. 38 and 39 possess higher transformation temperature; besides, as we compare alloys Nos. 43, 44 and 46 with alloys Nos. 8, 9, 10 and 3, even though adding Ta to alloys No. 43, 44, and 46 exhibits little effect to improve rolling ratio compared with adding Nb to alloys Nos. 8 to 10, better rolling ratio and higher transformation temperature were obtained compared respectively with alloy No. 3 and alloys Nos. 8 to 10 with added Nb.
  • alloy No. 48 was compared with alloys Nos. 44, 9, and 3, in the case of alloy 48 with combined addition of Ta and Nb, the rolling ratio is improved compared with alloy No. 44 with only Ta added, and yet the transformation temperature is increased compared with alloy No. 9 while only Nb is added.
  • the afore-described shape memory alloys do not lose their shape memory effect during repeated use at high temperature, they can be used as valves inside gas channels of motors (engines of automobiles, aircrafts, or gas turbine) for high temperature operation, when heated, channel area is regulated with the help of the shape memory effect; when cooled, channel area is reversed back by a spring used for deforming the valve. Besides, they can also be used as lubricant supplying valves of high speed rotating shafts. In addition, these alloys can be used as safety devices for power supply of household electric appliance at high temperature operation. Furthermore, they can also be used as actuators for high temperature operation. In the case of actuators, they also exhibit improved responsiveness resulting from increased cooling speed.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Combustion & Propulsion (AREA)
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  • Heat Treatment Of Steel (AREA)
  • Temperature-Responsive Valves (AREA)
US12/235,528 2006-03-20 2008-09-22 High temperature shape memory alloy, actuator and motor Abandoned US20090218013A1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP2006-076560 2006-03-20
JP2006076560 2006-03-20
PCT/JP2006/324206 WO2007108180A1 (fr) 2006-03-20 2006-12-05 Alliage a memoire de forme haute temperature, actionneur et moteur associes

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EP (1) EP1997922B1 (fr)
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WO2007108180A1 (fr) 2007-09-27
EP1997922A4 (fr) 2011-04-20

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