US20080289730A1 - Material having a high elastic deformation and process for producing the same - Google Patents

Material having a high elastic deformation and process for producing the same Download PDF

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US20080289730A1
US20080289730A1 US12/112,513 US11251308A US2008289730A1 US 20080289730 A1 US20080289730 A1 US 20080289730A1 US 11251308 A US11251308 A US 11251308A US 2008289730 A1 US2008289730 A1 US 2008289730A1
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based alloy
amount
elastic deformation
alloy
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Kiyohito Ishida
Ryosuke Kainuma
Katsunari Oikawa
Yuji SUTOU
Toshihiro OMORI
Keisuke Ando
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Japan Science and Technology Agency
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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
    • C22F1/10—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
    • C22C19/07—Alloys based on nickel or cobalt based on cobalt

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  • the present invention relates to a ferromagnetic material having a high elastic deformation composed of Co-based alloy which has a high elastic deformation capability and is capable of displacement control by applied magnetic field.
  • Titanium alloys have drawn attention as materials having a low Young's modulus and high elastic deformation capability and have been used in a dental implant, an artificial bone, and an eyeglass frame.
  • Patent documents 1 and 2 introduce a titanium alloy containing elements of Groups 4A and 5A, which exhibits a low Young's modulus and has a high elastic deformation capability.
  • a shape memory alloy is known for displacement control by temperature and a small percentage of change in dimension can be obtained.
  • Shape memory effect is a phenomenon in which an original shape is recovered by utilizing the martensite reverse transformation occurred when a deformed material is heated to a predetermined temperature or higher.
  • the shape memory effect allows the shape memory alloy to be used as a heat driven actuator.
  • temperature control is required and further changes in shape during the cooling-down period are rate-limited by thermal diffusion, and thus the responsiveness is bad.
  • Ferromagnetic shape memory alloys have also been attracting attention as actuator materials. In the ferromagnetic shape memory alloys, a small percentage of change in dimension which exceeds conventional magnetostriction materials can be obtained by application of an external magnetic field. Low responsiveness which is a defect of heat-driven shape memory alloy is also reduced.
  • a ferromagnetic shape memory alloy for example, Ni—Mn—Ga system is listed, and Patent document 3 introduces actuator materials which deform in response to an applied magnetic field.
  • Patent documents 4 and 5 introduce Co—Ni—Al system, and further Patent document 6 introduces Co system alloy.
  • Ni—Mn—Ga system is inferior inductility, and thus it is hard to be formed into a complicated and precise shape which is required for machine parts.
  • the ductility of Co—Ni—Al system alloy is improved by using a ⁇ -phase as a second phase, however, the intensity of magnetization is low.
  • the Co system alloy is relatively excellent in ductility and intensity of magnetization and heat driven shape memory effect is obtained, magnetostrictive characteristics are insufficient and super elastic characteristics cannot be obtained.
  • Patent document 1 Japanese Patent Application Laid-Open (JP-A) No. 2002-332531
  • Patent document 2 JP-A No. 2002-249836
  • Patent document 3 U.S. Pat. No. 5,958,154
  • Patent document 4 JP-A No. 2002-129273
  • Patent document 5 JP-A No. 2004-277865
  • Patent document 6 JP-A No. 2004-238720
  • the present inventors investigated and examined various materials which are ferromagnetic and can be driven by the magnetic field while maintaining high elastic deformation capability, and further have a good ductility in view of the defects of conventional titanium alloys and Ni—Mn—Ga system alloy. As a result, they found that a Co-based alloy having a high elastic deformation capability can be obtained by using cobalt as a basic material, properly selecting alloy content and composition, and forming an appropriate amount of an ⁇ -phase of h.c.p. structure.
  • An objective of the present invention is to provide Co-based alloy having a high elastic deformation capability and good ductility and workability which is obtained by controlling the level of production of the ⁇ -phase in the component system to which one or more members selected from Fe, Ni, and Mn are added, on the basis of the findings.
  • the Co-based alloy of the present invention includes, on the basis of mass percent, one or more members selected from 0.01 to 10% of Fe, 0.01 to 30% of Ni, and 0.01 to 25% of Mn.
  • the total content is set to the range of 0.02 to 50%.
  • the mass ratio is simply expressed as %.
  • the Co-based alloy of the present invention may include, in addition to Fe, Ni, and Mn, one or more members selected from 0.01 to 10% of Al, 0.01 to 35% of Cr, 0.01 to 20% of V, 0.01 to 15% of Ti, 0.01 to 30% of Mo, 0.01 to 10% of Nb, 0.01 to 3% of Zr, 0.01 to 30% of W, 0.01 to 10% of Ta, 0.01 to 5% of Hf, 0.01 to 8% of Si, 0.001 to 3% of C, 0.001 to 3% of B, 0.001 to 3% of P, and 0.001 to 3% of misch metal in a total of 0.001 to 50%.
  • one or more members selected from 0.01 to 10% of Al, 0.01 to 35% of Cr, 0.01 to 20% of V, 0.01 to 15% of Ti, 0.01 to 30% of Mo, 0.01 to 10% of Nb, 0.01 to 3% of Zr, 0.01 to 30% of W, 0.01 to 10% of Ta, 0.01 to 5% of Hf, 0.01 to 8% of Si
  • the proposed Co-based alloy is ferromagnetic at least ordinary temperature and the ⁇ -phase of h.c.p. structure induced by heat or stress is distributed in the alloy.
  • the proportion of the ⁇ -phase is 10% by volume or more and can be controlled by adjusting the components and production conditions.
  • a metallic structure in which the ⁇ -phase of h.c.p. structure is distributed is formed by solution-treating Co-based alloy with a predetermined composition at 900 to 1400° C. After the solution treatment, working may be performed at a working ratio of 10% or more, and further aging treatment may be performed at 300 to 800° C.
  • FIG. 1 is a graph showing effects of Fe content on the volume fraction of the ⁇ -phase in the metallic structure of the Co—Fe binary alloy, the amount of recovered strain, and the intensity of magnetization.
  • FIG. 3 is a graph showing effects of Mn content on the volume fraction of the ⁇ -phase in the metallic structure of the Co—Mn binary alloy, the amount of recovered strain, and the intensity of magnetization.
  • FIG. 4 is a microphotograph of the Co alloy containing 3.80% of Fe which has a metallic structure produced by the ⁇ -phase of h.c.p. structure.
  • FIG. 5 is a stress/strain diagram of the Co alloy containing 3.80% of Fe.
  • FIG. 6 is a graph showing effects of solution treatment conditions on the volume fraction of the ⁇ -phase in the metallic structure of the Co—Fe binary alloy, the amount of recovered strain, and the intensity of magnetization.
  • FIG. 7 is a graph showing effects of the rate of cold working on the volume fraction of the ⁇ -phase in the metallic structure of the Co—Fe binary alloy, the amount of recovered strain, and the intensity of magnetization.
  • FIG. 8 is a graph showing effects of aging treatment conditions on the volume fraction of the ⁇ -phase in the metallic structure of the Co—Fe binary alloy, the amount of recovered strain, and the intensity of magnetization.
  • FIG. 9 is a graph showing effects of solution treatment conditions on the volume fraction of the ⁇ -phase in the metallic structure of the Co—Ni binary alloy, the amount of recovered strain, and the intensity of magnetization.
  • FIG. 10 is a graph showing effects of the rate of cold working on the volume fraction of the ⁇ -phase in the metallic structure of the Co—Ni binary alloy, the amount of recovered strain, and the intensity of magnetization.
  • FIG. 11 is a graph showing effects of aging treatment conditions on the volume fraction of the ⁇ -phase in the metallic structure of the Co—Ni binary alloy, the amount of recovered strain, and the intensity of magnetization.
  • FIG. 12 is a graph showing effects of solution treatment conditions on the volume fraction of the ⁇ -phase in the metallic structure of the Co—Mn binary alloy, the amount of recovered strain, and the intensity of magnetization.
  • FIG. 13 is a graph showing effects of the rate of cold working on the volume fraction of the ⁇ -phase in the metallic structure of the Co—Mn binary alloy, the amount of recovered strain, and the intensity of magnetization.
  • FIG. 14 is a graph showing effects of aging treatment conditions on the volume fraction of the ⁇ -phase in the metallic structure of the Co—Mn binary alloy, the amount of recovered strain, and the intensity of magnetization.
  • FIG. 15 is a stress/strain diagram depending on the test temperature of the Co alloy containing 3.80% of Fe.
  • the present inventors added various alloy elements to cobalt which is a ferromagnetic element and then investigated and examined the relationship amongst the structure, the elastic deformation capability, and the magnetic properties in order to develop materials which have a high elastic deformation capability and are capable of displacement control by application or removal of magnetic field and workable. As a result, it is found out that when an appropriate amount of at least one member selected from Fe, Ni, and Mn is alloyed with cobalt, a ferromagnetic alloy having a high elastic deformation capability in which the workability is enhanced is produced.
  • the equation means that a force F obtained by a predetermined magnetic gradient dH/dx is proportional to an intensity of magnetization M.
  • the amount of strain to be obtained is larger as the force F applied to materials is larger. Therefore, a large intensity of magnetization M is better to increase the amount of strain.
  • the force required for deformation is high, the amount of strain due to the magnetic field becomes small, and thus it is desirable that the Young's modulus is small.
  • the elastic deformation capability is low, the strain is remained by removing the magnetic gradient. For that reason, a large elastic deformation capability is needed in order to obtain a large reversible strain by application or removal of the magnetic gradient.
  • Cobalt is a ferromagnetic element with a high Curie temperature, however, pure cobalt is lack of workability and has a low magnetic susceptibility.
  • the Cobalt has the ⁇ -phase of f.c.c. structure at high temperature and is transformed to a martensitic ⁇ -phase of h.c.p. structure at around 420° C. during cooling.
  • Various alloy elements are added to cobalt and then the phase stability of the ⁇ - and ⁇ -phases are investigated. As a result, the ⁇ -phase could be stabilized and various elements capable of improving workability could be identified.
  • the ⁇ -phase has a good workability because of f.c.c. of unordered structure. Although the ⁇ -phase has an effect of increasing the amount of elastic deformation, it is easily work-hardened and allows defects such as working cracks to be generated. Thus, when an element to be dissolved in the ⁇ -phase and stabilize is added, the ⁇ -phase remains even at an ordinary temperature. Therefore, the improvement in the workability of the Co-based alloy can be expected. Particularly, Fe, Ni, and Mn which have magnetic moments are effective for enhancement of magnetic characteristics of the Co-based alloy in addition to the improvement in workability.
  • the Co-based alloy has a diploid structure consisting of the ⁇ -phase of h.c.p. structure and the remainder being ⁇ -phase of f.c.c. structure.
  • the Co-based alloy permits a heterophase to be present as long as the phase does not have an adverse influence on the high elastic characteristics, magnetic properties, and workability.
  • the heterophase include an intermetallic compound produced by addition of a third component, a carbide, and an ⁇ -phase (b.c.c. structure).
  • the Co alloy to which Fe is added exhibits particularly excellent magnetic properties.
  • a large intensity of magnetization is obtained by a relatively low magnetic field.
  • the intensity of magnetization is 30 emu/g or more to an external magnetic field of 0.2T (Tesla). It can be said that the material is promising as the displacement control element.
  • Ni and Mn have effects which reduce the intensity of magnetization, the intensity of magnetization is still maintained at high level. Thus, demand characteristics as the displacement control elements are given.
  • the elastic limit strain of annealed metallic materials such as Fe and Co is normally about 0.3%.
  • the materials are work-hardened and sliding deformation is suppressed.
  • the hardness and tensile strength are increased, and further the yield stress and elastic limit are increased.
  • the Co-based alloy of the present invention based on, for example, 1% of bending deformation, 0.4% or more of strain that exceeds the normal amount of elastic strain is recovered.
  • a large temperature range from ⁇ 196° C. (liquid nitrogen temperature) to 400° C. is applicable.
  • the Young's modulus is a value of physical properties related to cohesive force between atoms. It is considered that it is hard to control by working or heat treatment. In this regard, a low Young's modulus is attained by lattice softening at the time of martensitic transformation or controlling the direction of the martensite variant in the present invention.
  • the lattice softening by the martensitic transformation is brought about in the vicinity of 420° C.
  • the transformation temperature is decreased by the addition of Fe, Ni, and Mn.
  • a low Young's modulus is obtained in the desired temperature range.
  • the martensitic transformation of Co—X (X: Fe, Ni, Mn) system is non-thermoelastic, and thus the hysteresis is about 150° C. Since the hysteresis further grows by the working, it is suitable to realize the low Young's modulus with a large temperature width.
  • the martensitic transformation of the Co-based alloy even if the Co-based alloy is sufficiently cooled to the Ms temperature or less in the same manner as that of the Fe alloy, the whole sample is not necessarily transformed into a martensitic phase and a certain amount of the mother phase remains.
  • the martensitic phase is stress-induced by working after the solution treatment.
  • the largest variant of Schmid factor to the stress is preferentially generated.
  • a part of the martensitic phase is rearranged in the variant preferential to the direction of the stress.
  • Such a preferential variant exhibits a low deforming stress against the direction of the stress, which is considered as one of the causes that the Co-based alloy exhibits a low Young's modulus.
  • the Co—Ni—Al system alloy (Patent documents 4 and 5) has a structure of the ⁇ -phase or ⁇ + ⁇ phase and the martensitic transformation and reverse transformation of the ⁇ -phase is used to impart a shape memory property.
  • the ⁇ -phase is not transformed to the ⁇ -phase.
  • the presence of the ⁇ -phase of B2 structure with a low ductility causes the reduction in workability, it can be said that the material is excellent in ductility from the viewpoint that the ⁇ -phase is not present in the Co-based alloy of the present invention.
  • the Co-based alloy of the present invention has an extremely high intensity of magnetization compared with the Co—Ni—Al system alloy being ferromagnetic and having a low intensity of magnetization.
  • the Co-based alloy of the present invention exhibits excellent capacity when performing displacement control by the magnetic gradient.
  • the Co-based alloy with a shape memory property described in Patent document 6 is excellent in shape memory effect.
  • superelasticity is not obtained and the displacement control by the magnetic field is also difficult because of extremely small magnetostriction.
  • the shape memory effect is a phenomenon where the deformation is given in the martensitic phase state and the shape is recovered by allowing the mother phase to be martensite reverse-transformed.
  • the superelasticity is a phenomenon where stress-induced martensitic transformation is exhibited when the stress is given in the state of the mother phase, and martensite reverse transformation to the mother phase occurs when the stress is unloaded, thereby recovering the shape.
  • a large magnetostriction in the ferromagnetic shape memory alloys is a phenomenon that is given by rearrangement of the martensite variant by a uniform magnetic field or magnetic-field-induced martensitic transformation.
  • the Co-based alloy of the present patent application a high elastic deformation capability is realized mainly by work hardening, which essentially differs from the superelasticity in the respect that martensitic reversible transformation or reverse transformation is not clearly detected by stress loading or unloading. While a martensitic phase ( ⁇ -phase) has a low Young's modulus, it only supports the elastic deformation capability. Further the workability is enhanced and the intensity of magnetization is also increased. Thus, the Co-based alloy exhibits an excellent function as a material in which displacement control can be performed by application or removal of the magnetic gradient.
  • the Co-based alloy of the present invention has a basic composition which includes one or more selected from 0.01 to 10% of Fe, 0.01 to 30% of Ni, and 0.01 to 25% of Mn.
  • Fe, Ni, and Mn reduce the martensitic transformation temperature, contribute to the improvement in ductility and workability, and are effective in increasing the magnetic susceptibility. Such effects become significant when 0.01% or more of Fe, Ni, or Mn is added. However, an excessive addition thereof reduces the martensite transformation temperature and magnetic transformation temperature to below room temperature, thereby inhibiting the production of the ⁇ -phase and reduction in magnetic properties.
  • the upper limits of Fe, Ni, and Mn are set to 10%, 30%, and 25%, respectively.
  • the total content is set to the range of 0.02 to 50%.
  • Each content of Fe, Ni, and Mn is set to preferably in the range of 1 to 8%, 1 to 25%, or 1 to 20%, more preferably in the range of 2 to 6%, 5 to 20%, or 5 to 15%.
  • One or more third components selected from Al, Cr, V, Ti, Mo, Nb, Zr, W, Ta, Hf, Si, C, B, P, and misch metal can be added to Co— (Fe, Mn, Ni) system if necessary.
  • the total content is selected in the range of 0.002 to 50% (preferably in the range of 0.005 to 30%).
  • Al, V, and Ti are components which reduce the martensitic transformation temperature. However, an excessive amount thereof allows the ⁇ -phase to be stabilized and reduces the volume fraction of the E-phase.
  • the content of Al, V, and Ti is selected in the range of 0.01 to 10%, in the range of 0.01 to 20%, and in the range of 0.01 to 15%, respectively.
  • Cr and Mo are components effective in improving corrosion resistance, however, the addition of an excessive amount thereof leads to a significant deterioration in ductility.
  • the Cr content is selected in the range of 0.01 to 35% and the Mo content is selected in the range of 0.01 to 30%.
  • Nb, Zr, W, Ta, and Hf are components effective in strengthening materials, however, the addition of an excessive amount thereof leads to a significant deterioration in ductility.
  • the content of Nb, Zr, W, Ta, and Hf is selected in the range of 0.01 to 10%, in the range of 0.01 to 3%, in the range of 0.01 to 30%, in the range of 0.01 to 10%, and in the range of 0.01 to 5%, respectively.
  • Si is a component which increases the martensitic transformation temperature, however, the addition of an excessive amount thereof leads to a significant deterioration in ductility.
  • the Si content is selected in the range of 0.01 to 8%.
  • C, B, P, and misch metal are components effective in allowing crystal grains to form a fine-grained structure, however, the addition of an excessive amount thereof leads to a significant deterioration in ductility.
  • the content of C, B, P, and misch metal is selected in the range of 0.001 to 3%, in the range of 0.001 to 3%, in the range of 0.001 to 3%, and in the range of 0.001 to 3%, respectively.
  • the Co-based alloy adjusted to a predetermined composition is dissolved, followed by casting, forging, and hot-rolling.
  • the resulting alloy is subjected to cold working, such as rolling, drawing, and forging so as to be formed into a plate member, a wire member, a pipe member, and the like, with a target size.
  • the solution-treatment temperature is sufficiently required to be the recrystallization temperature or higher. Therefore, it is set to 900° C. or higher and below melting point (specifically 1400° C. or less). Preferably, it is set to the range of 1000 to 1250° C.
  • the ⁇ -phase of f.c.c. structure is transformed to a martensitic ⁇ -phase of h.c.p. structure.
  • Ms temperature martensitic transformation point
  • the ⁇ -phase is stabilized by Fe, Ni, and Mn.
  • the structure after the cooling is not transformed to a single ⁇ -phase.
  • the Co-based alloy after the solution treatment may be subjected to rolling, forging, bending, and drawing.
  • the working temperature is usually set to an ordinary temperature. It can be set to 700° C. or less.
  • Examples of the martensitic transformation include stress induced transformation in addition to the heat induced transformation caused by cooling to the Ms temperature or less.
  • the working is an effective means for the increase of the volume fraction of the E-phase.
  • the stress induced transformation is caused when the stress is applied under the environment at the Ms temperature or more.
  • the hot working that concerns about dynamic recrystallization and precipitation accompanying the working is not preferable.
  • the hot working is usually defined as working at 0.6 T M (T M : melting point) or more
  • the working temperature is set to 0.6 T M or less, specifically 700° C. or less.
  • An inductive effect of the ⁇ -phase becomes remarkable due to the increase in the working ratio. Therefore, the working ratio at the time of cold working is set to 10% or more.
  • the upper limit of the working ratio is determined depending on the capability of the processing plant. However, an excessive working ratio makes the burdens involved in the processing plant greater. Therefore, it is preferable that the upper limit is set to 90%.
  • the upper limit of the ⁇ -phase is set to 99% by volume.
  • Solution treatment is performed at 900 to 1400° C. and working is performed at 700 or less.
  • aging temperature may be carried out at 300 to 800° C. (preferably at 400 to 700° C.).
  • the strength can be increased or decreased by the strain-aging effect or the recovery and recrystallization. The strength is increased in the case where the Cottrell effect or the Suzuki effect occurs, while the strength is decreased in the case where the recovery or recrystallization occurs.
  • At least short-range atomic diffusion is required for aging treatment, and thus the aging temperature is set to 300° C. or more. However, high-temperature heating at greater than 800° C. does not allow for a sufficient elastic strain.
  • Co-based alloys of Tables 1 to 3 were dissolved, followed by casting and hot-rolling. Then, each alloy was cold-rolled to a plate thickness of 0.5 mm and further subjected to solution-treatment at 1200° C. for 15 minutes.
  • F1 to F8 of Table 1 have alloy designs based on Co—Fe systems
  • N1 to N8 of Table 2 have alloy designs based on Co—Ni systems
  • M1 to M8 of Table 3 have alloy designs based on Co—Mn systems.
  • Volume fraction X ⁇ of the ⁇ -phase is calculated by substituting integrated intensities I(200) ⁇ and I(10 1 0) ⁇ of (200) ⁇ and (10 1 0) ⁇ based on X-ray diffraction into the following equation.
  • the amount of recovered strain is an amount of strain in the shape recovered when unloaded after applying an amount of bending strain (1%) in three-point bending test.
  • the intensity of magnetization was defined as the intensity of magnetization obtained when a magnetic field of 0.2 T was applied by using a vibrating sample magnetometer.
  • the intensity of magnetization is increased with a weighting amount of Fe.
  • the amount of Fe was 7.61% (No. F4), the maximum value of the intensity was shown, which was excellent magnetic properties.
  • the decrease in intensity of magnetization was observed depending on the weighting of Ni and Mn. However, a large intensity of magnetization of 43.9 emu/g or more was still maintained.
  • Comparative example C1 pure cobalt
  • the amount of recovered strain was lower than that of the material of the present invention.
  • Comparative example C2 pure iron
  • Comparative example C3 SUS316L
  • the intensity of magnetization was close to about 0 when a magnetic field of 0.2 T was applied.
  • the amount of recovered strain also showed a low value.
  • F2 of Table 1, N4 of Table 2, and M3 of Table 3 were selected as representatives of Co—Fe system alloy, Co—Ni system alloy, and Co—Mn system alloy, respectively, which were subjected to cold working and aging treatment after the solution treatment.
  • Test Nos. 4, 6, and 7 the cold working ratio and aging treatment conditions were fixed and the solution treatment temperature was changed. However, great changes in the volume fraction of the ⁇ -phase, amount of recovered strain, and intensity of magnetization were not observed. The relation was the same as that of Test Nos. 12 and 13 as well as Test Nos. 19 and 20. It can be understood from FIGS. 6 , 9 , and 12 .
  • Test Nos. 11, 12, 14, and 15 the solution treatment conditions and aging treatment conditions were fixed and the cold working ratio was changed.
  • the volume fraction of the ⁇ -phase was higher as the cold working ratio was higher, and the amount of recovered strain was also larger. Although the intensity of magnetization was reduced slightly, the reduction was not large.
  • the relation was observed in Test Nos. 4 and 5 as well as Test Nos. 19 and 21. It can be understood from FIGS. 7 , 10 , and 13 .
  • Test Nos. 16 to 19, 22, and 23 the solution treatment conditions and aging treatment conditions were fixed and the aging treatment conditions were changed.
  • the volume fraction of the ⁇ -phase and the amount of recovered strain tended to be reduced with the increase of the aging temperature.
  • the amount of recovered strain was small as compared with materials left after the cold working.
  • Test Nos. 17 to 19 and 22 the value was intermediate between the amount of recovered strain obtained by materials left after the solution treatment and the amount of recovered strain obtained by materials given by solution treatment and cold working. Remarkable changes in the intensity of magnetization were not observed.
  • the relation was the same as that of Test Nos. 1, 3, and 4 as well as Test Nos. 8, 10, and 12.
  • Co-alloy containing 2.05% of Fe, Co-alloy containing 10% of Ni, and Co-alloy containing 5% of Mn were basic compositions of Co—Fe system, Co—Ni system, and Co—Mn system, respectively.
  • the third component was added to prepare various Co-based alloys. Each alloy was dissolved, followed by casting and hot-rolling in the same manner as described in Example 1. Then, each alloy was cold-rolled to a plate thickness of 0.5 mm, which was subjected to solution treatment, cold rolling, and aging treatment.
  • F2 alloy of Table 1 was selected, followed by casting and hot-rolling. Then, the alloy was cold-rolled to a plate thickness of 0.33 mm, which was subjected to solution treatment at 1200° C. for 15 minutes and finally cold-rolled at a rolling reduction of 20%.
  • the volume fraction of the E-phase, the amount of recovered strain, and the intensity of magnetization (under conditions of ⁇ 50° C., 25° C., 100° C., and 200° C.) were determined.
  • the amount of recovered strain is an amount of strain in the shape recovered when unloaded after applying an amount of bending strain (1%) in tensile test at each temperature.
  • the volume fraction of the ⁇ -phase, the amount of recovered strain, and the intensity of magnetization were determined at each temperature in the same manner as described in Example 1.
  • the deforming stress varies largely with temperature.
  • the temperature dependence of the apparent yield stress in Ti—Ni system alloy is about 5 MPa/° C.
  • the temperature dependence of the stress in the Co—Fe system alloy of the present invention is as small as about 0.5 MPa/° C., which is about one-tenth of the Ti—Ni system alloy. Therefore, it is suitable to utilize over wide temperature ranges from below room temperature to high temperatures. Further, the intensity of magnetization was large even at 200° C. since the Curie temperature was very high.
  • the Co-based alloy with a high elastic deformation capability was given by adding an appropriate amount of one or more members selected from Fe, Ni, and Mn and controlling the level of production of the ⁇ -phase.
  • a functional material which is useful as a sensor or actuator capable of displacement control by an applied magnetic field is provided.

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Cited By (8)

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US9157136B2 (en) 2012-12-05 2015-10-13 Industrial Technology Research Institute Multi-element alloy material and method of manufacturing the same
US20160289800A1 (en) * 2012-08-28 2016-10-06 Questek Innovations Llc Cobalt alloys
WO2019099719A1 (fr) * 2017-11-16 2019-05-23 Arconic Inc. Alliages de cobalt-chrome-aluminium et leurs procédés de production
DE102018208737A1 (de) * 2018-06-04 2019-12-05 Siemens Aktiengesellschaft Y, Y` gehärtete Kobalt-Nickel-Basislegierung, Pulver, Komponente und Verfahren
DE102018208736A1 (de) * 2018-06-04 2019-12-05 Siemens Aktiengesellschaft Y, Y' gehärtete Kobalt-Nickel-Basislegierung, Pulver, Komponente und Verfahren
US10844465B2 (en) 2017-08-09 2020-11-24 Garrett Transportation I Inc. Stainless steel alloys and turbocharger kinematic components formed from stainless steel alloys
CN115679233A (zh) * 2022-09-21 2023-02-03 北京航空材料研究院股份有限公司 一种物理场固态处理铸造钛合金的方法及得到的钛合金

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KR102136455B1 (ko) * 2018-03-16 2020-07-21 서울대학교산학협력단 자가 치유 특성을 가지는 변태 유기 소성 초합금 및 그 제조 방법
CN110592432B (zh) * 2019-09-25 2020-09-04 北京北冶功能材料有限公司 一种钴基变形高温合金及其制备方法

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Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20140334968A1 (en) * 2011-11-18 2014-11-13 Tubitak Alloy for high temperature tooling applications
US20160289800A1 (en) * 2012-08-28 2016-10-06 Questek Innovations Llc Cobalt alloys
US9157136B2 (en) 2012-12-05 2015-10-13 Industrial Technology Research Institute Multi-element alloy material and method of manufacturing the same
US10844465B2 (en) 2017-08-09 2020-11-24 Garrett Transportation I Inc. Stainless steel alloys and turbocharger kinematic components formed from stainless steel alloys
WO2019099719A1 (fr) * 2017-11-16 2019-05-23 Arconic Inc. Alliages de cobalt-chrome-aluminium et leurs procédés de production
DE102018208737A1 (de) * 2018-06-04 2019-12-05 Siemens Aktiengesellschaft Y, Y` gehärtete Kobalt-Nickel-Basislegierung, Pulver, Komponente und Verfahren
DE102018208736A1 (de) * 2018-06-04 2019-12-05 Siemens Aktiengesellschaft Y, Y' gehärtete Kobalt-Nickel-Basislegierung, Pulver, Komponente und Verfahren
CN115679233A (zh) * 2022-09-21 2023-02-03 北京航空材料研究院股份有限公司 一种物理场固态处理铸造钛合金的方法及得到的钛合金

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