Near room temperature transition metal-based amorphous alloy with high magnetic entropy change peak and preparation method thereof

Abstract

The application discloses a near-room-temperature transition metal-based amorphous alloy with a high magnetic entropy change peak value and a preparation method thereof, and comprises the following steps: S1, weighing and mixing metal raw materials; S2, repeatedly melting the uniformly mixed metal raw materials in a titanium-adsorbed argon environment by using an electric arc furnace to obtain a uniform alloy mother ingot; S3, clamping the alloy mother ingot and placing it in a quartz tube, fully melting the alloy mother ingot by induction melting, and then spraying the alloy melt onto a rotating copper roller to solidify the alloy melt into an alloy strip. The near-room-temperature transition metal-based amorphous alloy with a high magnetic entropy change peak value and the preparation method thereof can overcome the shortcomings of a small magnetic entropy change temperature zone, a low magnetic refrigeration capacity and a high cost of the existing near-room-temperature magnetic heat materials.

Description

Technical Field

[0001] This invention relates to the field of amorphous magnetocaloric alloy technology, and in particular to near-room temperature transition metal-based amorphous alloys with high magnetic entropy change peaks and their preparation methods. Background Technology

[0002] Compared to traditional refrigeration technologies, magnetic refrigeration (MR) has attracted widespread attention due to its high efficiency, low energy consumption, compact structure, and environmental friendliness. Firstly, magnetic refrigeration boasts higher refrigeration efficiency, reaching up to 60% of the theoretical limit. Secondly, because it does not contain ozone-depleting chemicals or emit greenhouse gases, magnetic refrigeration is more environmentally friendly. Finally, it uses solid materials as refrigerants, making magnetic refrigerators more compact and safer.

[0003] Since the efficiency of magnetic refrigeration technology, based on the magneto-caloric effect (MCE) of magnetic materials, mainly depends on the magnetic entropy change performance of the refrigerant, developing materials with excellent room-temperature magnetic entropy change performance has become a major challenge in the field of magnetic refrigeration and a bottleneck for the practical application of magnetic refrigeration technology. The magneto-caloric performance of magnetic materials can be measured by the magnetic entropy change (-ΔS). m Or adiabatic temperature rise (ΔT) ad ) is used to measure. -ΔS at different temperatures m (-ΔS m The -T curve can usually be obtained from the isothermal magnetization curve according to Maxwell's equations. Based on the -ΔS of the magnetic material... m Based on the shape of the -T curve, magnetocaloric materials can generally be divided into two categories: those with a sharp -ΔS curve. m First-order magnetic phase transition materials with peaks and flat -ΔS m Second-order magnetic phase transition materials with hump-shaped lattice structures. The sharp -ΔS of first-order magnetic phase transition materials. m The peaks limit their usability to a very narrow temperature range, so even though first-order magnetic phase transition materials exhibit very high magnetic entropy change peaks (-ΔS), they are still usable only within a very narrow temperature range. m peak However, these materials are still unsuitable for use as magnetic refrigerants because they cannot meet the wide operating temperature range requirements of conventional refrigerators. Conversely, second-order magnetic phase change materials possess a wide -ΔS... m The distribution and the resulting greater magnetic refrigeration capacity (RC, which is derived by multiplying the peak magnetic entropy change by the temperature width at half the peak value, and is a more effective measure of magnetic refrigeration efficiency) make them more suitable as magnetic refrigerants in room temperature magnetic refrigerators.

[0004] As an important class of second-order magnetic phase change materials, amorphous alloys have advantages over general second-order magnetic phase change materials, such as the ability to form over a wider compositional range and adjustable Curie temperatures (Ti). c It possesses magnetocaloric properties, soft magnetic properties and low hysteresis loss, high resistance and low eddy current loss, as well as excellent electrical and mechanical properties.

[0005] Generally speaking, amorphous magnetocaloric alloys can be divided into rare earth (RE)-based and transition metal (TM)-based amorphous alloys. RE-based amorphous alloys typically exhibit excellent forming ability and high -ΔS at low temperatures. m peak However, as their Curie temperatures are tuned to near room temperature, the forming ability and -ΔS of RE-based amorphous alloys decrease. m peak In contrast, TM-based amorphous alloys exhibit good formability near room temperature and are easily manufactured over a wide compositional range, allowing their Curie temperatures to be tuned to the operating temperature range of room temperature refrigeration equipment. This provides a prerequisite for using TM-based amorphous alloys as refrigerants in room temperature magnetic refrigerators. Furthermore, the manufacturing cost of TM-based amorphous alloys is significantly lower than that of RE-based amorphous alloys, making them more suitable for large-scale industrial applications in room temperature magnetic refrigeration.

[0006] However, the current peak values ​​of magnetic entropy change of TM-based amorphous alloys are still not high, making it difficult to meet the requirements for efficient industrial applications of room-temperature magnetic refrigerators. Therefore, it is essential to explore and develop a series of TM-based amorphous magnetocaloric materials with higher near-room-temperature magnetic entropy change peak values, thereby constructing efficient magnetic refrigerants with a magnetic entropy change platform within the operating temperature range of household refrigerators.

[0007] Therefore, the purpose of this invention is to provide a series of TM-based amorphous magnetocaloric alloys and their preparation methods that have higher magnetic entropy change peak values ​​within the operating temperature range of household refrigerators, lower costs, and are more suitable for industrial applications, overcoming the shortcomings of existing near-room temperature magnetocaloric materials such as small magnetic entropy change temperature range, low magnetic cooling capacity, and high cost. Summary of the Invention

[0008] The purpose of this invention is to provide a near-room temperature transition metal-based amorphous alloy with a high magnetic entropy change peak value and its preparation method, which can overcome the shortcomings of existing near-room temperature magnetocaloric materials, such as small magnetic entropy change temperature range, low magnetic cooling capacity and high cost.

[0009] To achieve the above objectives, this invention provides a near-room-temperature transition metal-based amorphous alloy with a high magnetic entropy change peak value and a method for its preparation, comprising the following steps:

[0010] S1. Weigh and mix the metal raw materials;

[0011] S2. The uniformly mixed metal raw materials are repeatedly melted in an electric arc furnace in an argon atmosphere adsorbed by titanium to obtain a uniform alloy master ingot.

[0012] S3. After crushing the alloy master ingot, place it in a quartz tube and melt it fully through induction melting. Then, spray the alloy melt onto a rotating copper roller to solidify and form an alloy strip.

[0013] Preferably, in step S1, the metal raw materials are weighed according to the following atomic ratio.

[0014] TM x%

[0015] Zr,RE (100-xy)%

[0016] B,Si,Al y%.

[0017] Preferably, in step S1, 85≤x≤95, 1≤y≤7.

[0018] Preferably, in step S1, TM is one of the transition metals Fe, Co, or Ni; RE is one of the rare earth metals Ce, Pr, Nd, Sm, Gd, Tb, Dy, Ho, or Er.

[0019] Preferably, in step S3, the alloy strip is solidified on the rotating copper roller by using a cooling roller to spin the strip, and the tangential linear velocity of the copper roller surface is 55 m / s.

[0020] A method for preparing near-room temperature transition metal-based amorphous alloys with high magnetic entropy change peak values.

[0021] Preferably, the transition metal-based amorphous alloy includes Fe. 87 Pr 10 B3, Fe 87 Pr 11 B2, Fe 87 Pr9Ce2B2, Fe 88 Pr 10 Ce1B1 and Fe 87 Pr 10 Al3 five amorphous alloy strips.

[0022] Therefore, the present invention employs the above-mentioned near-room temperature transition metal-based amorphous alloy with high magnetic entropy change peak value and its preparation method, and its technical effects are as follows:

[0023] (1) The transition metal-based amorphous magnetocaloric alloy of the present invention has a higher magnetic entropy change peak value, a wider magnetic entropy change distribution and a large magnetic refrigeration capacity, which makes it easier to construct a magnetic entropy change platform suitable for the Eriksen cycle. Its magnetic entropy change temperature range can be easily adjusted according to the working temperature range of the magnetic refrigeration machine.

[0024] (2) The transition metal-based amorphous magnetocaloric alloy of the present invention can be formed in a relatively wide range of compositions, and by adjusting its composition, a continuously changing Curie temperature and magnetic entropy change performance can be obtained, thereby obtaining a series of amorphous alloys with high magnetic entropy change peaks in the operating temperature range of household air conditioners, which is superior to general crystalline alloys.

[0025] (3) The transition metal-based amorphous magnetocaloric alloy of the present invention has a Curie temperature between 279K and 337K and a magnetic entropy change peak value of 4.5J / kgK at 5T, which is higher than other amorphous magnetocaloric alloys reported in the literature.

[0026] (4) The transition metal-based amorphous magnetocaloric alloy of the present invention has the advantages of small coercivity, small magnetic hysteresis and thermal hysteresis, high strength, good corrosion resistance and easy processing and forming.

[0027] (5) The preparation process used in this invention is relatively simple and has low preparation cost, making it suitable for large-scale industrial applications.

[0028] The technical solution of the present invention will be further described in detail below with reference to the accompanying drawings and embodiments. Attached Figure Description

[0029] Figure 1 It is Fe 87 Pr 10 B3, Fe 87 Pr 11 B2, Fe 87 Pr9Ce2B2, Fe 88 Pr 10 Ce1B1 and Fe 87 Pr 10 X-ray diffraction images of five iron-based alloy stripes of Al3;

[0030] Figure 2 It is Fe 87 Pr 10 B3, Fe 87 Pr 11 B2, Fe 87 Pr9Ce2B2, Fe 88 Pr 10 Ce1B1 and Fe 87 Pr 10 Magnetization intensity of five iron-based amorphous stripes of Al3 as a function of temperature under a magnetic field of 0.03T;

[0031] Figure 3 It is Fe 87 Pr 10 Arrott curves of B3 amorphous stripes at different temperatures;

[0032] Figure 4 It is Fe 87 Pr 11 Arrott curves of B2 amorphous stripes at different temperatures;

[0033] Figure 5 It is Fe 87 Arrott curves of Pr9Ce2B2 amorphous stripes at different temperatures;

[0034] Figure 6 It is Fe 88 Pr 10 Arrott curves of Ce1B1 amorphous stripes at different temperatures;

[0035] Figure 7 It is Fe 87 Pr 10 Arrott curves of Al3 amorphous stripes at different temperatures;

[0036] Figure 8 It is Fe 87 Pr 10 B3, Fe 87 Pr 11 B2, Fe 87 Pr9Ce2B2, Fe 88 Pr 10 Ce1B1 and Fe 87 Pr 10 The magnetic entropy change of five iron-based amorphous strips of Al3 under a 5T magnetic field as a function of temperature. Detailed Implementation

[0037] The technical solution of the present invention will be further described below with reference to the accompanying drawings and embodiments.

[0038] Unless otherwise defined, the technical or scientific terms used in this invention shall have the ordinary meaning as understood by one of ordinary skill in the art to which this invention pertains.

[0039] It will be apparent to those skilled in the art that the present invention is not limited to the details of the exemplary embodiments described above, and that the invention can be implemented in other specific forms without departing from its spirit or essential characteristics. Therefore, the embodiments should be considered illustrative and non-limiting in all respects, and the scope of the invention is defined by the appended claims rather than the foregoing description. Thus, all variations falling within the meaning and scope of equivalents of the claims are intended to be included within the present invention, and no reference numerals in the claims should be construed as limiting the scope of the claims.

[0040] Furthermore, it should be understood that although this specification describes embodiments, not every embodiment contains only one independent technical solution. This narrative style is merely for clarity. Those skilled in the art should consider the specification as a whole, and the technical solutions in each embodiment can be appropriately combined to form other embodiments that can be understood by those skilled in the art. These other embodiments are also covered within the scope of protection of this invention.

[0041] It should also be understood that the specific embodiments described above are only used to explain the present invention, and the scope of protection of the present invention is not limited thereto. Any equivalent substitutions or modifications made by those skilled in the art within the scope of the technology disclosed in the present invention, based on the technical solution and inventive concept of the present invention, should be covered within the scope of protection of the present invention.

[0042] Techniques, methods, and apparatus known to those skilled in the art may not be discussed in detail, but where appropriate, they should be considered part of the specification.

[0043] All prior art documents cited in this specification are incorporated herein by reference and are therefore part of the disclosure of this invention.

[0044] Example 1

[0045] The near-room-temperature transition metal-based amorphous alloy with a high magnetic entropy change peak value provided by this invention is a TM-based amorphous magnetocaloric alloy, with the general chemical formula TM. x (Zr,RE) 100-x-y (B,Si,Al) yIn the general formula, 85≤x≤95, 1≤y≤7; TM is a transition metal Fe, Co, or Ni; RE is a rare earth metal Ce, Pr, Nd, Sm, Gd, Tb, Dy, Ho, or Er, etc.; the Curie temperature of pure TM metals is generally very high. Adding metalloids B, Si, and metal Al can lower their Curie temperature, but the magnetic entropy change performance is not improved; the addition of metal Zr is beneficial to improving the peak value of magnetic entropy change of TM-based amorphous alloys and adjusting their Curie temperature to the room temperature range; RE metals generally have excellent magnetocaloric effects, but they are expensive; the combination of TM metals and a small amount of RE metals is beneficial to improving the peak value of magnetic entropy change of TM-based amorphous alloys, while avoiding the disadvantage of high cost of RE-based magnetocaloric materials, which meets the requirements of low cost and high performance for industrial applications.

[0046] In this embodiment, the TM x (Zr,RE) 100-x-y (B,Si,Al) y The alloy is an amorphous stripe; amorphous alloys exhibit disordered atomic arrangement at the microscopic level, have high strength and hardness, lack grain boundaries, crystals and dislocations, have better corrosion resistance, and possess excellent soft magnetic properties and high magnetic permeability.

[0047] In this embodiment, the TM-based amorphous magnetocaloric material includes Fe. 87 Pr 10 B3, Fe 87 Pr 11 B2, Fe 87 Pr9Ce2B2, Fe 88 Pr 10 Ce1B1 and Fe 87 Pr 10 Five Al3 amorphous alloy strips with Curie temperatures (ranging from 279 K to 337 K) spanning both room temperature cold end and hot end temperatures; the peak values ​​of the magnetic entropy changes of these five alloy strips are all above 4.5 J / kgK.

[0048] A method for preparing near-room-temperature transition metal-based amorphous alloys with high magnetic entropy change peaks includes the following steps:

[0049] S1. Weigh and mix the metal raw materials according to the atomic percentage of each element in the above general formula;

[0050] S2. The uniformly mixed metal raw materials are repeatedly melted in an electric arc furnace in an argon atmosphere adsorbed by titanium to obtain a uniform alloy master ingot.

[0051] S3. After crushing the alloy master ingot, place it in a quartz tube and melt it fully through induction melting. Then, spray the alloy melt onto a rotating copper roller to solidify and form an alloy strip.

[0052] In step S3, a cooling roller is used to spin the strip, and the tangential linear velocity of the copper roller surface is 55 m / s. At this speed, the alloy strip is well formed, and an amorphous strip with a thickness of 30 to 40 μm can be formed without droplet splashing.

[0053] Example 2

[0054] Fe was prepared using the preparation method described in Example 1. 87 Pr 10 B3 alloy, the steps are as follows:

[0055] S1. The Fe-B alloy is pre-melted into an alloy ingot, and then mixed with pure metals Fe and Pr with a purity of not less than 99.9 at.% according to Fe... 87 Pr 10 The atomic percentages of each element in B3 were weighed and mixed, with the mass error controlled within 0.1 mg;

[0056] S2. Place the prepared raw materials into a high vacuum electric arc melting furnace and repeatedly melt them more than 5 times in a high-purity argon atmosphere adsorbed by sponge titanium to ensure that the alloy composition is homogeneous. After cooling, a uniform alloy master ingot is obtained.

[0057] S3. After crushing the alloy master ingot, place it in a quartz tube and melt it into a molten liquid state through an induction coil in a high-purity argon atmosphere. Then, use a pneumatic injection device to spray the molten alloy onto the surface of a high-speed rotating copper roller, thereby rapidly solidifying to form a 30-40 μm thick Fe layer. 87 Pr 10 The B3 amorphous alloy strip has a tangential linear velocity of 55 m / s for the rotating copper roller and a pressure difference of 0.06 MPa between the inside and outside of the pneumatic injection device.

[0058] Replacing Pr or / and B in the alloy of this embodiment with Zr, Ce, Nd, Sm, Gd, Tb, Dy, Ho, Er or / and Si, Al according to equal atomic percentages can achieve the purpose of this invention.

[0059] The purpose of this invention can be achieved by replacing a small amount of Fe in the alloy of this embodiment with Co or Ni.

[0060] Example 3

[0061] Fe was prepared using the preparation method described in Example 2. 87 Pr 11 B2 alloy, yielding Fe alloy with a thickness of 30–40 μm. 87 Pr 11 B2 amorphous alloy strip.

[0062] Replacing Pr or / and B in the alloy of this embodiment with Zr, Ce, Nd, Sm, Gd, Tb, Dy, Ho, Er or / and Si, Al according to equal atomic percentages can achieve the purpose of this invention.

[0063] The purpose of this invention can be achieved by replacing a small amount of Fe in the alloy of this embodiment with Co or Ni.

[0064] Example 4

[0065] Fe was prepared using the preparation method described in Example 1. 87 The steps for producing Pr9Ce2B2 alloy are as follows:

[0066] S1. The Fe-B alloy is pre-melted into an alloy ingot, and then mixed with pure metals Fe, Pr, and Ce with a purity of not less than 99.9 at.% according to Fe... 87 The atomic percentages of each element in Pr9Ce2B2 were weighed and mixed, with the mass error controlled within 0.1 mg.

[0067] Steps S2 and S3 are the same as steps S2 and S3 in Example 1; a Fe layer with a thickness of 30–40 μm is obtained. 87 Pr9Ce2B2 amorphous alloy strip.

[0068] Replacing Pr and / or Ce and / or B in the alloy of this embodiment with Zr, Nd, Sm, Gd, Tb, Dy, Ho, Er and / or Si, Al according to equal atomic percentages can achieve the purpose of this invention.

[0069] The purpose of this invention can be achieved by replacing a small amount of Fe in the alloy of this embodiment with Co or Ni.

[0070] Example 5

[0071] Fe 88 Pr 10 The preparation method of Ce1B1 alloy is the same as in Example 4, yielding Fe alloys with a thickness of 30–40 μm. 88 Pr 10 Ce1B1 amorphous alloy strips.

[0072] Replacing Pr and / or Ce and / or B in the alloy of this embodiment with Zr, Nd, Sm, Gd, Tb, Dy, Ho, Er and / or Si, Al according to equal atomic percentages can achieve the purpose of this invention.

[0073] The purpose of this invention can be achieved by replacing a small amount of Fe in the alloy of this embodiment with Co or Ni.

[0074] Example 6

[0075] Fe was prepared using the preparation method described in Example 1. 87 Pr 10 Al3 alloy, the steps are as follows:

[0076] S1. Pure metals Fe, Pr, and Al with a purity of not less than 99.9 at.% are mixed according to Fe... 87 Pr 10 The mass percentage of each element in Al3 was weighed and mixed, and the mass error was controlled within 0.1 mg.

[0077] Steps S2 and S3 are the same as steps S2 and S3 in Example 1; a Fe layer with a thickness of 30–40 μm is obtained. 87 Pr 10 Al3 amorphous alloy strips.

[0078] Replacing Pr or / and Al in the alloy of this embodiment with Zr, Ce, Nd, Sm, Gd, Tb, Dy, Ho, Er or / and Si, B according to equal atomic percentages can achieve the purpose of this invention.

[0079] The purpose of this invention can be achieved by replacing a small amount of Fe in the alloy of this embodiment with Co or Ni.

[0080] Figure 1 Fe from Examples 2 to 6 87 Pr 10 B3, Fe 87 Pr 11 B2, Fe 87 Pr9Ce2B2, Fe 88 Pr 10 Ce1B1 and Fe 87 Pr 10 X-ray diffraction images of Al3 alloy strips show typical amorphous diffuse scattering peaks and the absence of sharp crystallization peaks, indicating their amorphous structure.

[0081] Figure 2 This is a curve showing the magnetization of a strip sample under an applied magnetic field of 0.03T versus temperature, measured using Quantum Design's Comprehensive Physical Performance Measurement System (PPMS). The Curie temperature of the material is determined to be the temperature at which the derivative of magnetization with respect to temperature reaches its minimum, near which the material undergoes a ferromagnetic-paramagnetic transition. Figure 2 Derive Fe 87 Pr 10 B3, Fe 87 Pr 11 B2, Fe 87 Pr9Ce2B2, Fe 88 Pr 10 Ce1B1 and Fe 87 Pr10 The Curie temperatures of the amorphous Al3 stripes are 337 K, 326 K, 310 K, 290 K, and 279 K, respectively. Their Curie temperatures span both the cold and hot ends of room temperature, making them a potential candidate for room-temperature magnetic refrigerants.

[0082] According to Banerjee's principle and Landau's theory, if the slope of the Arrott curve of a sample is negative, i.e., a "C" or "S" shaped curve appears, then the sample has undergone a first-order magnetic phase transition; otherwise, it has undergone a second-order magnetic phase transition. The Arrott curve of a sample can be determined by using the isothermal magnetization curve at the corresponding temperature with H / M as the x-axis and M as the y-axis. 2 It was constructed for the y-axis. Figure 3 , Figure 4 , Figure 5 , Figure 6 and Figure 7 They are Fe 87 Pr 10 B3, Fe 87 Pr 11 B2, Fe 87 Pr9Ce2B2, Fe 88 Pr 10 Ce1B1 and Fe 87 Pr 10 Arrott curves of Al3 amorphous strips at different temperatures are shown in the figure. All curves exhibit positive slopes, and the Arrott curves of each sample at different temperatures are almost parallel to each other, indicating that the magnetic transitions of these samples are all second-order magnetic phase transitions. This ensures that these samples can undergo ferromagnetic-paramagnetic transitions over a wide temperature range, while maintaining low thermal and magnetic hysteresis near the phase transition point, which can effectively improve energy utilization.

[0083] According to Maxwell's equations, the magnetic entropy change of the alloy under different temperatures and magnetic fields can be calculated from the isothermal magnetization curves of the sample at different temperatures. Figure 8 It is Fe 87 Pr 10 B3, Fe 87 Pr 11 B2, Fe 87 Pr9Ce2B2, Fe 88 Pr 10 Ce1B1 and Fe 87 Pr 10 Al3 amorphous stripe under a 5T magnetic field -ΔS m -T curves. The graph shows the -ΔS curves of these alloys. m The -T curves all exhibit very wide full width at half maximum (FWHM), ensuring that these amorphous stripes can be used over a wide operating temperature range. Fe 87 Pr10 B3, Fe 87 Pr 11 B2, Fe 87 Pr9Ce2B2, Fe 88 Pr 10 Ce1B1 and Fe 87 Pr 10 The peak values ​​of the magnetic entropy change and peak temperatures of the Al3 amorphous strips under a 5T magnetic field are 4.66 J / kgK (337.5 K), 4.73 J / kgK (327.5 K), 4.65 J / kgK (307.5 K), 4.61 J / kgK (292.5 K), and 4.62 J / kgK (282.5 K), respectively. The peak values ​​of the magnetic entropy change of these amorphous strips all exceed 4.5 J / kgK, which is higher than the peak values ​​of the magnetic entropy change of current RE-based room-temperature magnetocaloric amorphous alloys. Combined with the low cost of these Fe-based amorphous alloy strips, the Fe-based amorphous strips of this invention have greater commercial application value. Furthermore, the peak temperatures of the magnetic entropy change of these amorphous strips are distributed between the cold end and hot end temperatures of room temperature, indicating that the peak temperatures of these Fe-based amorphous strips can be easily adjusted within the operating temperature range of room temperature refrigeration equipment while maintaining a high peak magnetic entropy change. Therefore, it is entirely feasible to use these Fe-based amorphous alloy strips as refrigerants for room temperature magnetic refrigerators.

[0084] Therefore, the present invention employs the above-mentioned near-room temperature transition metal-based amorphous alloy with high magnetic entropy change peak value and its preparation method, which can overcome the shortcomings of existing near-room temperature magnetocaloric materials, such as small magnetic entropy change temperature range, low magnetic cooling capacity and high cost.

[0085] Finally, it should be noted that the above embodiments are only used to illustrate the technical solutions of the present invention and not to limit them. Although the present invention has been described in detail with reference to preferred embodiments, those skilled in the art should understand that modifications or equivalent substitutions can still be made to the technical solutions of the present invention, and these modifications or equivalent substitutions cannot cause the modified technical solutions to deviate from the spirit and scope of the technical solutions of the present invention.

Claims

1. A method for preparing near-room temperature transition metal-based amorphous alloys with high magnetic entropy change peak values, characterized in that, Includes the following steps: S1. Weigh and mix the metal raw materials; Metal raw materials are weighed according to the following atomic ratios. TM x% Zr,RE (100-xy)% B,Si,Al y% 85≤x≤95,1≤y≤7; TM is one of the transition metals Fe, Co, or Ni; RE is one of the rare earth metals Ce, Pr, Nd, Sm, Gd, Tb, Dy, Ho, or Er. S2. The uniformly mixed metal raw materials are repeatedly melted in an electric arc furnace in an argon atmosphere adsorbed by titanium to obtain a uniform alloy master ingot. S3. After crushing the alloy master ingot, place it in a quartz tube and melt it fully through induction melting. Then, spray the alloy melt onto a rotating copper roller to solidify and form an alloy strip.

2. The method for preparing a near-room-temperature transition metal-based amorphous alloy with a high magnetic entropy change peak value according to claim 1, characterized in that, In step S3, the alloy strip is solidified by spraying onto a rotating copper roller and then spun onto a cooling roller. The tangential linear velocity of the copper roller surface is 55 m / s.

3. The near-room temperature transition metal-based amorphous alloy with a high magnetic entropy change peak obtained by the preparation method of the near-room temperature transition metal-based amorphous alloy with a high magnetic entropy change peak according to any one of claims 1-2.

4. The near-room temperature transition metal-based amorphous alloy with a high magnetic entropy change peak value according to claim 3, characterized in that: Transition metal-based amorphous alloys include Fe 87 Pr 10 B3, Fe 87 Pr 11 B2, Fe 87 Pr9Ce2B2, Fe 88 Pr 10 Ce1B1 and Fe 87 Pr 10 Al3 five amorphous alloy strips.

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