NiCoMnTi-based strain glass alloy as well as preparation method and application thereof

Abstract

The invention relates to the technical field of magnetic materials, and provides a NiCoMnTi-based strained glass alloy and a preparation method and application thereof, the chemical formula of the alloy is Ni (50-x) CoxMn (50-y) Tiy, x is more than or equal to 10 and less than or equal to 40, y is more than or equal to 10 and less than or equal to 40, and x + ygt is greater than or equal to 10 and less than or equal to 40; x and y respectively represent atomic percentages of Co and Ti, the alloy is austenite with a B2 structure at room temperature, the microscopic phase composition is a single Heusler phase, and nano martensite domains of 1-900nm are dispersed and distributed below the room temperature. The alloy system is free of martensite phase transformation and has the frequency dependence characteristic of a glassy state; in a wide temperature range from a liquid nitrogen temperature zone to the room temperature, the super-elasticity alloy shows near-linear super-elasticity and low hysteresis loss, and has the advantages of high strength, corrosion resistance, good machinability and the like; the method has excellent application prospects in the fields of low-temperature wide-temperature-range magnetic driving materials, magnetostrictive strain / stress, intelligent application, solid-state refrigeration, thermal management and the like.

Description

Technical Field

[0001] The present invention relates to the technical field of magnetic materials, and in particular to a NiCoMnTi-based strained glass alloy and a preparation method and application thereof. Background Art

[0002] Ferromagnetic shape memory alloys (FMIs) are an important class of smart materials. Their crystal structure phase transitions and magnetic transitions impart physical properties such as superelasticity, shape memory, magnetoinduced strain / stress, and phase transition thermal effects. These materials are widely used in aerospace, mechanics, electronics, chemicals, energy, and construction, among other engineering fields. However, these materials struggle to undergo first-order phase transitions at low temperatures, and their intrinsic brittleness severely limits their application in cryogenic environments. Recently discovered NiTi strain glass alloys exhibit a strain glass transition accompanied by phase transition extinction, typically occurring at low temperatures. Unlike the martensitic phase transition, which involves shearing of the entire lattice, strain glass transitions occur through the action of an external field on short-range, ordered nanoscale strain domains, potentially enabling low-temperature applications. This non-martensitic shape memory mechanism opens new avenues for the development of novel smart materials, particularly in applications where conventional shape memory alloys struggle due to limited phase transition temperatures or insufficient cycling stability.

[0003] Following the discovery of the strain glass transition in nickel-titanium alloys, strain glass transitions were subsequently reported in other systems, such as the nickel-manganese-based Heusler alloys NiCoMnGa and NiCoMnIn. These strain glass alloys possess many of the properties of strain glass and are also responsive to magnetic fields, offering broad application prospects. However, the intrinsic brittleness of traditional Heusler alloys due to strong pd covalent hybridization still needs to be overcome. In 2015, Liu Enke, Wei Zhiyang, and others discovered highly tough, fully transitional Heusler alloys based on dd covalent hybridization, exemplified by NiMnTi and NiCoMnTi. This weak bonding leads to weak atomic ordering within the alloys, making them susceptible to localized distortions, dislocations, and other defects, creating a natural environment favorable for the formation of strain glass. This is also supported by the discovery of multiple modulated martensitic structures during the phase transition in previous studies. This suggests that fully transitional Heusler alloys may be ideal systems for realizing strain glass alloys for low-temperature applications.

[0004] Strain glass has been reported in the Ni2MnTi system, but Ni2MnTi alloys lack ferromagnetism, and strain glass in the ferromagnetic NiCoMnTi system has not yet been reported. Therefore, the ability to stably produce strain glass alloys in the fully transitional Heusler alloy NiCoMnTi system through a simple process has far-reaching application value. Summary of the Invention

[0005] The technical problem to be solved by the present invention is that the currently reported full transition Heusler alloys do not have ferromagnetism and cannot meet the requirements of highly adjustable physical properties and high toughness of strain glass alloys. To overcome the above defects of the existing technology, the present invention provides a NiCoMnTi-based strain glass alloy and its preparation method and application.

[0006] The first object of the present invention is to provide a NiCoMnTi based strain glass alloy, the chemical formula of the alloy is Ni 50-x Co x Mn 50-y Ti y , where 10≤ x ≤40, 10≤ y ≤40, x + y >30, x 、 y represent the atomic percentages of Co and Ti respectively. The alloy is austenite with B2 structure at room temperature, and its microphase composition is a single Heusler phase.

[0007] Compared with the prior art, the present invention has the following advantages: the alloy composed of transition elements and a single Heusler phase has no macroscopic martensitic phase transformation, has a strain glass transition, and has ferromagnetism, which ultimately leads to highly adjustable physical properties and superelasticity of the alloy and high toughness.

[0008] In a possible implementation manner, the strain glass transition temperature of the alloy is in the range of 80-300K.

[0009] In a possible implementation, the strain glass transition temperature of the alloy is in the range of 170-280K.

[0010] In a possible embodiment, the alloy can recover a strain greater than 1.5% in a temperature range from liquid nitrogen temperature to above room temperature.

[0011] In one possible implementation, the alloy can withstand a stress greater than 800 MPa.

[0012] A second object of the present invention is to provide a method for preparing a NiCoMnTi-based strained glass alloy, comprising the following steps: weighing Ni, Co, Mn, and Ti metal elements as raw materials according to a chemical formula, preparing the raw materials into a polycrystalline bulk ingot by high-temperature melting combined with isotropic cooling, then placing the ingot in an inert gas for heat treatment, and then quenching to obtain the alloy.

[0013] In one possible embodiment, the purity of the Ni, Co, Mn, and Ti metal elements is greater than 99.95%.

[0014] In one possible embodiment, the high-temperature smelting is arc melting, solid-phase reaction, induction melting or cold / hot rolling deformation, and the isotropic cooling method includes immediately placing the sample obtained by high-temperature smelting in a low thermal conductivity medium to maintain isotropic slow cooling.

[0015] In a possible implementation, the low thermal conductivity medium is a copper wire ball or an asbestos mesh.

[0016] In a possible implementation manner, the heat treatment is high-purity argon sealed tube annealing, the annealing temperature is 600-1100° C., and the annealing time is 2-72 hours.

[0017] In a possible embodiment, the quenching is to quickly quench the heat-treated sample in an ice-water mixture.

[0018] The third object of the present invention is to provide a NiCoMnTi-based strain glass alloy for use in low-temperature and wide-temperature range magnetic drive materials, magneto-induced strain / stress, intelligent applications, solid-state refrigeration, thermal management and other fields.

[0019] The beneficial effects of the present invention are: 1. Ni prepared by the present invention 50-x Co x Mn 50-y Ti y The alloy, through the specific ratio of each element and supplemented by special solidification cooling means, can simply and efficiently prepare strain glass alloys in the full transition family Heusler alloy NiCoMnTi system.

[0020] 2. Ni prepared by the present invention 50-x Co x Mn 50-y Ti y Strain glass alloys have no macroscopic martensitic phase transformation, but have strain glass transition, and the dynamic mechanical test curves show obvious frequency dependence and other behaviors unique to the glass state.

[0021] 3. Ni prepared by the present invention 50-x Co x Mn 50-y Ti y The strained glass alloy exhibits near-linear superelasticity and low hysteresis loss in a wide temperature range from liquid nitrogen temperature to above room temperature, and can recover strain exceeding 1.5%.

[0022] 4. Ni prepared by the present invention 50-x Co x Mn 50-y Ti yStrain glass alloy is based on the combined effect of weak dd covalent hybridization and strain glass state. Compared with NiCoMnTi alloy without strain glass state, the mechanical properties of this alloy are improved and it can withstand stress exceeding 800MPa. BRIEF DESCRIPTION OF THE DRAWINGS

[0023] In order to more clearly illustrate the embodiments of the present invention or the technical solutions in the prior art, the following briefly introduces the drawings required for use in the embodiments or the description of the prior art. Obviously, the drawings described below are some embodiments of the present invention. For ordinary technicians in this field, other drawings can be obtained based on these drawings without paying any creative work.

[0024] Figure 1 Ni in Example 1 34 Co 16 Mn 33 Ti 17 Room temperature XRD curve of the alloy; Figure 2 Ni in Example 1 34 Co 16 Mn 33 Ti 17 Schematic diagram of the austenite crystal structure of the alloy; Figure 3 Ni in Example 1 34 Co 16 Mn 33 Ti 17 SEM images of the alloy; Figure 4 Ni in Example 1 34 Co 16 Mn 33 Ti 17 Heat flow-temperature curve of the alloy; Figure 5 Ni in Example 1 34 Co 16 Mn 33 Ti 17 Magnetization-temperature curve of the alloy; Figure 6 Ni in Example 1 34 Co 16 Mn 33 Ti 17 Storage modulus-temperature curve of the alloy; Figure 7 Ni in Example 1 34 Co 16 Mn 33 Ti 17 TEM selected area electron diffraction pattern of the alloy at 298K; Figure 8 Ni in Example 1 34 Co 16 Mn 33 Ti 17 TEM selected area electron diffraction pattern of the alloy at 119K; Figure 9 Ni in Example 1 34 Co 16 Mn 33 Ti 17 Stress-strain curve of the alloy; Figure 10 Ni in Comparative Example 1 34 Co 16 Mn 33 Ti 17 Storage modulus-temperature curve of the alloy; Figure 11 Ni in Comparative Example 2 34 Co 16 Mn 33 Ti 17 Storage modulus-temperature curve of the alloy; Figure 12 Ni in Example 2 34 Co 16 Mn 33 Ti 17 Storage modulus-temperature curve of the alloy; Figure 13 Ni in Example 3 34 Co 16 Mn 33 Ti 17 Storage modulus-temperature curve of the alloy; Figure 14 Ni in Example 3 34 Co 16 Mn 33 Ti 17 Stress-strain curve of the alloy; Figure 15 Ni in Example 3 34 Co 16 Mn 33 Ti 17 Stress-strain curve of the alloy; Figure 16 Ni in Comparative Example 3 34 Co 16 Mn 33 Ti 17 Storage modulus-temperature curve of the alloy; Figure 17 Ni in Comparative Example 4 35 Co15 Mn 35 Ti 15 Alloy, Ni in Examples 1 and 3 34 Co 16 Mn 33 Ti 17 Resistance-temperature curve of the alloy; Figure 18 Ni in Comparative Example 5 33 Co 17 Mn 35 Ti 15 Stress-strain curve of the alloy. DETAILED DESCRIPTION

[0025] To make the above-mentioned objects, features, and advantages of the present invention more clearly understood, specific embodiments of the present invention are described in detail below. It should be noted that the following embodiments are only intended to illustrate the implementation methods and typical parameters of the present invention, and are not intended to limit the parameter ranges described in the present invention. Reasonable variations derived therefrom are still within the scope of protection of the claims of the present invention.

[0026] It should be noted that the endpoints of the ranges and any values ​​disclosed herein are not limited to the precise ranges or values, and these ranges or values ​​should be understood to include values ​​close to these ranges or values. For numerical ranges, the endpoints of each range, the endpoints of each range and individual point values, and the individual point values ​​can be combined with each other to obtain one or more new numerical ranges, and these numerical ranges should be considered to be specifically disclosed herein.

[0027] Unless otherwise defined, all terms, symbols and other scientific terms used herein are intended to have the same meaning as commonly understood by those skilled in the art to which the present invention belongs. In some cases, terms with conventional meanings are defined herein for the purpose of clarification or ease of reference, and such definitions herein should not be construed as indicating significant differences from conventional understandings in the art. The technical methods described or cited herein are generally well understood by those skilled in the art and are adopted by conventional methods. Unless otherwise stated, the use of commercially available kits, reagents and instruments was carried out in accordance with the protocols and parameters given by the manufacturers.

[0028] Example 1 The preparation method of the strained glass alloy of this embodiment is as follows: Step 1: According to the stoichiometric ratio of Ni 34 Co 16 Mn 33 Ti 17Weigh 30g of Ni, Co, Mn, and Ti with a purity exceeding 99.95% respectively. Since Mn is a volatile element, an additional 1% of its mass is added during batching to compensate for losses during the smelting process to ensure that the sample composition meets expectations. All oxide scales on the surface of the raw materials must be polished off before batching. Taking the purification of Mn as an example, the specific steps are as follows: (1) Place 30-50 g of Mn metal with a purity higher than 99.5% into an electric arc furnace; (2) Repeated smelting for more than 3 times using a current exceeding 200 A. In particular, the Mn ingot needs to be turned over after each smelting to ensure uniform smelting; (3) The oxide scale on the surface of the smelted Mn ingot was polished clean and smashed. The inside showed a silvery-white metallic luster and there were no oxide impurities of other colors, indicating that the Mn had been successfully purified.

[0029] Step 2: Use electric arc furnace to prepare alloy ingots. First, place the prepared raw materials in the center of the copper crucible, then use a mechanical pump to evacuate the furnace chamber and purge the air 3 to 4 times. After the purge is completed, wait until the vacuum degree is below 5 Pa and then turn on the molecular pump to pump the air pressure to 10 -3 The furnace is then backfilled with high-purity Ar gas to a high vacuum of 0.05 MPa.

[0030] During melting, place the arc tip 2-3 cm from the raw material and strike the arc with a low current. After striking the arc, slowly increase the current while raising the arc tip to avoid spattering due to uneven heating of the sample. Electromagnetic stirring is used during the melting process to ensure uniform melting of the sample, and the ingot is repeatedly melted 4-6 times. For samples containing volatile components, such as Mn, the melting current and duration must be strictly controlled, depending on the equipment status. After melting, slowly raise the arc tip and adjust the current to zero. Turn off the power to end the melting.

[0031] In particular, during the cooling process after the sample solidifies after the smelting is completed, it is necessary to ensure that the alloy ingot is cooled nearly isotropically and the cooling rate of the sample is reduced as much as possible. In this embodiment, the sample is flipped quickly and continuously on the copper mold to prevent excessive contact heat transfer between the sample and the copper mold, so as to achieve isotropic slow cooling to room temperature as much as possible and maintain the disorder, defects and internal stress inside the alloy.

[0032] Step 3: Use a grinding wheel to clean the oxide on the surface of the arc-melted sample ingot, and use electric spark wire cutting to cut the sample into the size required for the test. In this invention, 3×1.5×12mm 3 Strip samples are used for DMA, DSC, MT, ρ-T and other physical property tests; 4×4×8mm 3 The cube was used for elastic-thermal testing, and the surface of the sample was polished clean of wire-cut ablation marks and then ultrasonically cleaned with anhydrous ethanol.

[0033] Step 4: Place the cleaned sample into a quartz tube and pump the vacuum inside the tube to 8×10 -4 Pa, and then backfilled with high-purity Ar gas to 0.05MPa to seal the tube. The sealed quartz tube was placed in a tube furnace and annealed at 1173K for 24h. When taken out, the quartz tube was broken and quenched in ice water to ensure a sufficiently fast cooling rate for the sample.

[0034] The measured Ni 34 Co 16 Mn 33 Ti 17 Microstructure, physical properties, and superelasticity of strained glass alloy samples, and collection and analysis of test results.

[0035] Among them, the annealed sample is austenite with B2 structure at room temperature, and the room temperature XRD curve is as follows: Figure 1 As shown, the crystal structure model of B2 austenite is as follows Figure 2 As shown. Figure 3 In the SEM image of the sample, it can be seen that the sample microstructure is a single Heusler phase.

[0036] Figure 4 Ni in Example 1 34 Co 16 Mn 33 Ti 17 Heat flow-temperature curve of the alloy; Figure 5 Ni in Example 1 34 Co 16 Mn 33 Ti 17 The magnetization-temperature curve of the alloy; Figure 4 and Figure 5 It can be seen that Ni 34 Co 16 Mn 33 Ti 17 No martensitic transformation occurs in the alloy during the entire cooling process.

[0037] Figure 6 Ni in Example 1 34 Co 16 Mn 33 Ti 17 The storage modulus-temperature curve of the alloy shows that the frequency dependence of the storage modulus in the range of 205-260K is a sign of the strain glass transition. As can be seen from the figure, the strain glass transition temperature of the alloy prepared in this example is about 226K. Figure 7 、 8 Ni in Example 1 34 Co 16 Mn 33 Ti17 TEM selected area electron diffraction patterns of the

[110] zone axis of the alloy at 298K and 119K. It can be seen from the figure that the alloy prepared in this embodiment at room temperature is a cubic B2 austenite phase. After cooling to 119K (lower than the glass transition temperature of 226K), the halos of different sizes around the original diffraction band are the diffraction signals generated by the nano-martensite domains.

[0038] Figure 9 Ni in Example 1 34 Co 16 Mn 33 Ti 17 The stress-strain curves of the alloy at different temperatures show that the sample exhibits near-linear superelasticity in a wide temperature range of 166~323K. The irrecoverability of the sample in the range of 209~253K is caused by the strain glass transition. When the temperature is lowered below the strain glass freezing temperature, the sample still exhibits near-linear superelasticity. Example 2

[0039] This embodiment is an improvement of the process of Example 1. The difference from Example 1 is that in the cooling process of step 2 just after the sample solidifies, the high-temperature sample is placed on a copper wire ball and slowly cooled to room temperature. The other processes are exactly the same as those of Example 1 and will not be repeated here.

[0040] The measured Ni 34 Co 16 Mn 33 Ti 17 Physical properties and superelasticity of alloys, collecting and analyzing test results.

[0041] Figure 12 Ni in Example 2 34 Co 16 Mn 33 Ti 17 The storage modulus-temperature curve of the alloy shows that the use of copper wire balls for thermal insulation cooling reduces Ni 34 Co 16 Mn 33 Ti 17 During the alloy cooling process, the contact point between the sample ingot and the outside world is reduced, and the temperature gradient distribution and the overall cooling rate are reduced, so that a strain glass alloy can be obtained, and its strain glass transition temperature is about 286K. Example 3

[0042] This embodiment is an improvement of the process of Example 1. The difference from Example 1 is that in the cooling process of step 2 just after the sample solidifies, the high-temperature sample is placed on an asbestos net and slowly cooled to room temperature. The other processes are exactly the same as those of Example 1 and will not be repeated here.

[0043] The measured Ni 34 Co 16 Mn 33 Ti 17 Physical properties and superelasticity of alloys, collecting and analyzing test results.

[0044] Figure 13 Ni in Example 3 34 Co 16 Mn 33 Ti 17 The storage modulus-temperature curve of the alloy shows that the use of asbestos mesh for thermal insulation cooling reduces Ni 34 Co 16 Mn 33 Ti 17 During the alloy cooling process, the contact point between the sample ingot and the outside world is reduced, and the temperature gradient distribution and the overall cooling rate are reduced, so that a strain glass alloy can be obtained, and its strain glass transition temperature is about 286K.

[0045] Figure 14 、 15 In this embodiment, Ni 34 Co 16 Mn 33 Ti 17 The stress-strain curve of the alloy, Figure 12 From the stress-strain curve at 333K shown, it can be concluded that the sample can withstand a pressure of 800 MPa without failure, and in subsequent tests, it still exhibits nearly linear superelasticity in a wide temperature range of 253~333K, as shown in Figure 15 The residual strain of the sample during the initial compression in the range of 283~53K is caused by the temperature locking of the glass, which can be eliminated after multiple cycles at the same temperature.

[0046] Comparative Example 1 This comparative example has the same ingredients as Example 1, but slightly different preparation processes, the difference being: Ni in Comparative Example 1 34 Co 16 Mn 33 Ti 17 Alloy, in step 2 of Example 1, the sample ingot is cooled in a copper crucible of an electric arc furnace. The other processes are exactly the same as those in Example 1 and will not be repeated here.

[0047] The physical properties of the obtained samples were characterized, and the test results were collected and analyzed as a comparison with Example 1.

[0048] Figure 10 Ni in Comparative Example 1 34 Co 16 Mn 33 Ti 17The storage modulus-temperature curve of the alloy shows that a too fast cooling rate during the melting process is not conducive to the formation of strain glass.

[0049] Comparative Example 2 This comparative example has the same ingredients as Example 1, but slightly different preparation processes, the difference being: Ni in Comparative Example 2 34 Co 16 Mn 33 Ti 17 The alloy, in step 4 of Example 1, adopts the heat treatment condition of annealing at 1173K for 96h. The other processes are exactly the same as those in Example 1 and are not repeated here.

[0050] Figure 11 Ni in Comparative Example 2 34 Co 16 Mn 33 Ti 17 From the storage modulus-temperature curve of the alloy, it can be seen that a too long annealing time leads to an increase in the degree of atomic ordering inside the alloy, and the reduction of defects and internal stress is also not conducive to the formation of strain glass.

[0051] Comparative Example 3 This comparative example has the same ingredients as Example 1, but slightly different preparation processes, the difference being: Ni in Comparative Example 3 34 Co 16 Mn 33 Ti 17 The alloy ingot did not undergo any heat treatment, and the other processes were the same as those in Example 1, so the specific process will not be repeated here.

[0052] The physical properties of the obtained samples were characterized, and the test results were collected and analyzed as a comparison with Example 1.

[0053] Figure 16 Ni in Comparative Example 3 34 Co 16 Mn 33 Ti 17 From the storage modulus-temperature curve of the alloy, it can be seen that the cast alloy cannot exhibit strain glass state without any heat treatment.

[0054] Comparative Example 4 The difference between this comparative example and Example 1 is that the alloy composition is different. The alloy chemical formula of this comparative example is Ni 35 Co 15 Mn 35 Ti 15 The other processes are exactly the same as those in Example 1 and will not be described in detail here.

[0055] Figure 17Ni in Comparative Example 4 35 Co 15 Mn 35 Ti 15 Alloy, Example 1, 3Ni 34 Co 16 Mn 33 Ti 17 The common resistance-temperature curve of the alloy shows that the martensitic phase transition occurs and the strain glass state disappears after the composition changes.

[0056] Comparative Example 5 The difference between this comparative example and Example 3 is that: Ni 50-x Co x Mn 50-y Ti y Alloy composition is Ni 33 Co 17 Mn 35 Ti 15 The cooling process is carried out in a copper crucible of an arc melting furnace, and the heat treatment condition is annealing at 1173 K for 96 h. The other processes are exactly the same as those in Example 3 and will not be repeated here.

[0057] Figure 18 Ni in Comparative Example 5 37 Co 16 Mn 34 Ti 17 From the stress-strain curve of the alloy, it can be seen that the mechanical properties of the sample without strain glass are poor. It yields and produces irreversible deformation after only two low stress loadings of 150 MPa at room temperature.

[0058] The above description is merely a specific embodiment of the present application, but the scope of protection of the present application is not limited thereto. Any changes or substitutions that can be easily conceived by a person skilled in the art within the technical scope disclosed in the present application should be included in the scope of protection of the present application. Therefore, the scope of protection of the present application should be based on the scope of protection of the claims.

Claims

1. A NiCoMnTi-based strain glass alloy, characterized in that: The chemical formula of the alloy is Ni 50-x Co x Mn 50-y Ti y , where 10≤ x ≤40, 10≤ y ≤40, x + y >30, x 、 y represent the atomic percentages of Co and Ti, respectively. The alloy is austenite with a B2 structure at room temperature, and its microphase composition is a single Heusler phase. Below room temperature, nano-martensite domains with a size of 1 to 900 nm are dispersed.

2. The NiCoMnTi based strained glass alloy according to claim 1, characterized in that: The strain glass transition temperature of the alloy is in the range of 80-300K; Preferably, the temperature range is 170~280K.

3. The NiCoMnTi based strained glass alloy according to claim 1, characterized in that: The alloy can recover a strain greater than 1.5% in a temperature range from a liquid nitrogen temperature zone to above room temperature.

4. The NiCoMnTi-based strain glass alloy according to claim 1, characterized in that: The alloy can withstand stress greater than 800 MPa.

5. A method for preparing a NiCoMnTi-based strain glass alloy according to any one of claims 1 to 4, characterized in that: The method comprises the following steps: weighing Ni, Co, Mn and Ti metal elements as raw materials according to a chemical formula, preparing the raw materials into a polycrystalline bulk ingot by adopting a high-temperature smelting method combined with isotropic cooling, then placing the ingot in an inert gas for heat treatment, and then quenching to obtain the alloy.

6. The preparation method according to claim 5, characterized in that The purity of the Ni, Co, Mn and Ti metal elements is greater than 99.95%.

7. The preparation method according to claim 5, characterized in that The high-temperature melting is arc melting, solid-phase reaction, induction melting or cold / hot rolling deformation, and the isotropic cooling method includes immediately placing the sample obtained by high-temperature melting in a low thermal conductivity medium to maintain isotropic slow cooling; Preferably, the low thermal conductivity medium is copper wire balls or asbestos mesh.

8. The preparation method according to claim 5, characterized in that The heat treatment is high-purity argon sealed tube annealing, the annealing temperature is 600-1100° C., and the annealing time is 2-72 hours.

9. The preparation method according to claim 5, characterized in that The quenching is to quickly quench the heat-treated sample in an ice-water mixture.

10. Application of the NiCoMnTi-based strain glass alloy according to any one of claims 1 to 4 in the fields of low-temperature and wide-temperature range magnetic drive materials, magneto-induced strain / stress, intelligent applications, solid-state refrigeration, and thermal management.

Images