An amorphous alloy strip with high resistivity and a preparation method thereof

Abstract

The present invention discloses an amorphous alloy strip with high resistivity, and the chemical formula of the amorphous alloy strip is Fe a P b Cr c B d Si e Cu h Ni f Mo g , where a, b, c, d, e, f, g, h are atomic percentages, 65 ≤ a ≤ 77, 8 ≤ b ≤ 13, 5 ≤ c ≤ 10, 3 ≤ d ≤ 6, 0 < e ≤ 2, 0 < f ≤ 5, 1 ≤ g ≤ 5, 0 < h ≤ 2, and a + b + c + d + e + f + g + h = 100. Here, Fe represents iron element, P represents phosphorus element, Cr represents chromium element, B represents boron element, Si represents silicon element, Ni represents nickel element, Mo represents molybdenum element, and Cu represents copper element. The amorphous alloy strip provided by the present invention has a relatively high glass transition temperature, ensuring the application of the amorphous alloy strip in the field of low-temperature heating, and has high resistivity, high strength and high hardness, and can meet the usage requirements in different environments.

Description

Technical Field

[0001] The present invention relates to the technical field of materials, and particularly relates to an amorphous alloy strip with high resistivity and a preparation method thereof. Background Art

[0002] Amorphous alloys are usually prepared by rapid solidification of liquid metals. Because under extremely cold conditions, atoms do not have time to rearrange, grow, and nucleate, there are no structural defects unique to crystalline alloys such as grain boundaries and dislocations. Moreover, on the macroscopic scale, they show long-range disorder and short-range order. Also, because the internal atomic arrangement and distribution are very similar to those of glass, they are also called metallic glasses and belong to metastable phases. They will transform into crystalline states under external stimuli (factors such as pressure and temperature). Therefore, amorphous alloys have excellent performances in soft magnetic properties, strength, hardness, and corrosion resistance.

[0003] With the rapid development of electric heating devices, the performance requirements for electric heating materials are also getting higher and higher. In the prior art, some people have studied using low-iron amorphous alloy strips as electric heating materials (the atomic percentage of Fe is less than 60%). On the one hand, iron-based amorphous alloys have relatively high resistivity and higher electrothermal conversion efficiency, which is beneficial for heating elements to quickly heat up and improve the electrothermal conversion rate. On the other hand, the thickness of iron-based amorphous strips is extremely thin, only between 20 - 30 μm, and the width can be correspondingly sized according to actual applications. They occupy a small space, have a large heating area, and high heating efficiency, which is also beneficial for improving the electrothermal conversion efficiency. However, iron-based amorphous alloys are very brittle, which hinders their wide application. Therefore, amorphous alloy strips are required to have good processing flexibility. On the one hand, amorphous alloy strips with a thickness range of 20 μm - 30 μm can be obtained, and on the other hand, the amorphous alloy strips are not easily broken and can also be applicable to equipment in different low-temperature electric heating fields. Since the amorphous alloy strips are electrically heated in different environments, the requirements for the amorphous strips are different in different application environments. For example, when the amorphous alloy strip is used as a heating element of an outdoor heating strip for snow melting and ice thawing on outdoor roads, on the one hand, the outdoor impact is relatively large, which may cause cracks or fractures and reduce the service life. On the other hand, the outdoor environment is relatively harsh, which may cause corrosion of the strip and thus affect its use performance. Therefore, the amorphous strip still requires good strength, hardness, and corrosion resistance.

[0004] Although the use of amorphous alloy tapes has better performance than traditional electric heating materials such as tungsten wires and nickel-chromium wires, there are still technical problems. First, the resistivity of amorphous alloy tapes is low, which is not conducive to the electrothermal conversion rate. Second, how to balance the relationship between the processing flexibility, hardness, and strength of amorphous alloy tapes. When the processing flexibility of the prepared amorphous alloy tape is better, it will lead to a decrease in the hardness and strength of the amorphous alloy tape, and it is easy to break during use. When the hardness and strength of the prepared amorphous alloy tape are better, it will lead to a decrease in the processing flexibility of the amorphous alloy tape, and it may also cause the amorphous alloy tape to break. Third, the corrosion resistance of the amorphous alloy tape can be improved, which is beneficial to the application of the amorphous alloy tape in different environments. Fourth, the temperature range of use of the amorphous alloy tape can be increased. The glass transition temperature of the low-iron amorphous alloy tape in the prior art is relatively low, so the low-iron amorphous alloy tape is suitable for low-temperature heating fields below 200°C. Summary of the Invention

[0005] In view of the problems in the prior art, the present invention discloses a high-resistivity amorphous alloy tape and a preparation method thereof. The amorphous alloy tape of the present invention has good processing flexibility, good strength and hardness, is applicable to a wider low-temperature heating field of 50°C - 300°C, and has higher resistivity and electrothermal conversion rate.

[0006] The present invention is achieved by the following technical solutions:

[0007] A high-resistivity amorphous alloy tape provided by the present invention, the chemical formula of the amorphous alloy tape is Fe a P b Cr c B d Si e Cu h Ni f Mo g , where a, b, c, d, e, f, g, h are atomic percentages, 65 ≤ a ≤ 77, 8 ≤ b ≤ 13, 5 ≤ c ≤ 10, 3 ≤ d ≤ 6, 0 < e ≤ 2, 0 < f ≤ 5, 1 ≤ g ≤ 5, 0 < h ≤ 2 and a + b + c + d + e + f + g + h = 100. Here, Fe represents iron element, P represents phosphorus element, Cr represents chromium element, B represents boron element, Si represents silicon element, Ni represents nickel element, Mo represents molybdenum element, and Cu represents copper element.

[0008] In the above design of the present invention, the amorphous alloy strip in the present invention is used as an electric heating material. In order to increase the resistivity of the amorphous alloy strip and reduce the cost at the same time, the atomic percentage of Fe in the amorphous alloy strip is increased to 65%-77%. On this basis, in order to obtain a higher resistance and further improve the amorphous forming ability and processing flexibility of the amorphous alloy strip, a P-B-Si-Cu system is further incorporated into the amorphous alloy strip system to enhance the amorphous forming ability and processing flexibility of the amorphous alloy strip. At the same time, a Mo-Ni co-doping system is also incorporated into the amorphous alloy strip, which can stabilize the high resistivity of the amorphous alloy strip after doping with the P-B-Si-Cu system, reduce the occurrence of element segregation, further stabilize and improve the amorphous forming ability of the amorphous alloy strip, and balance the processing flexibility of the amorphous strip with the strength and hardness of the amorphous strip. Finally, Cr is also doped in the non-alloy strip of the present invention to improve the corrosion resistance of the amorphous alloy strip.

[0009] As a further solution, the chemical formula of the amorphous alloy strip is Fe a P b Cr c B d Si e Cu h Ni f Mo g , where a, b, c, d, e, f, g, h are atomic percentages, 68≤a≤88, 10≤b≤13, 5≤c≤10, 3≤d≤6, 0<e≤2, 4.5<f + g<8, 0<h≤2 and a + b + c + d + e + f + g + h = 100. Within this range, while obtaining a good resistivity for the amorphous alloy strip, the amorphous alloy strip also has good strength and hardness.

[0010] As a further solution, the chemical formula of the amorphous alloy strip is Fe a P b Cr c B d Si e Cu h Ni f Mo g , where a, b, c, d, e, f, g, h are atomic percentages, 68≤a≤88, 10≤b≤13, 5≤c≤10, 3≤d≤6, 0<e≤2, 4.5<f + g<8, 0<h≤2, 1≤f / g≤2 and a + b + c + d + e + f + g + h = 100. Within this range, while obtaining a better resistivity for the amorphous alloy strip, the strength and hardness of the amorphous alloy strip are further improved.

[0011] As a further solution, the Fe is derived from industrial pure iron, the P is derived from ferrophosphorus, the Cr is derived from chromium, the B is derived from ferroboron, the Si is derived from polysilicon, the Ni is derived from nickel, the Mo is derived from molybdenum, and the Cu is derived from copper.

[0012] As a further solution, the glass transition temperature of the amorphous alloy strip is 440°C - 500°C.

[0013] The present invention also provides a method for preparing the amorphous alloy strip, and the preparation method includes:

[0014] S1: According to the atomic percentages of the amorphous alloy strip, weigh the raw materials, and the raw materials include one or more of industrial pure iron, ferrophosphorus, chromium, ferroboron, polysilicon, nickel, molybdenum, and copper;

[0015] S2: Clean the raw materials obtained in S1;

[0016] S3: Melting the raw materials cleaned in S2 multiple times in a vacuum environment to obtain a master alloy ingot;

[0017] S4: Melt the master alloy ingot and then rapidly cool it to obtain the non-alloy strip of the present invention.

[0018] As a further solution, the best way to clean in S2 is: Treat pure iron, molybdenum, and nickel with 5% dilute hydrochloric acid until the surface is bright, then soak in absolute ethanol and clean in an ultrasonic cleaner; Clean copper with 2% sulfuric acid and then put it into absolute ethanol for ultrasonic cleaning; Clean ferrophosphorus, chromium, ferroboron, and polysilicon with absolute ethanol in ultrasonic cleaning. Use acid pickling to remove the oxide layer on the metal surface.

[0019] As a further solution, add 0.04 Mpa - 0.06 Mpa argon in the vacuum environment in S3.

[0020] As a further solution, the specific melting in S3 is that when melting for the first time, add in the order of decreasing melting point, ensuring that the low-melting-point raw materials are on the upper layer.

[0021] As a further solution, the best number of melting times in S3 is 4 - 5 times. Ensure that the components in the non-alloy strip can be evenly distributed.

[0022] The present invention also provides the application of the amorphous alloy strip, and the amorphous alloy strip can be used in the low-temperature heating field below 300°C.

[0023] As a further solution, the amorphous alloy strip can be used in the low-temperature heating field below 300°C and above 200°C.

[0024] As a further solution, the amorphous alloy strip can be used in the low-temperature heating field below 300 °C and above 250 °C.

[0025] The features and beneficial effects of the present invention are as follows:

[0026] (1) The amorphous alloy strip provided by the present invention has a relatively high glass transition temperature, which ensures the application of the amorphous alloy strip in the low-temperature heating field. In addition, the amorphous alloy strip of the present invention has high resistivity, high strength and high hardness, and can meet the usage requirements in different environments, and has good application prospects in low-temperature electric heating fields such as indoor and outdoor heating and pipe tracing.

[0027] (2) The amorphous alloy strip of the present invention has the ability of low cost and high corrosion resistance.

[0028] (3) On the basis of good processing flexibility, the amorphous alloy strip of the present invention is applicable to the low-temperature heating field of 200-300 °C, and has high resistivity, which improves the electro-thermal conversion rate.

[0029] (4) The glass transition temperature of the amorphous alloy strip of the present invention is 440 °C - 500 °C, the resistivity is 160 μΩ·cm - 175 μΩ·cm, the Vickers microhardness HV0.3 of the amorphous alloy is 650 - 750, and the tensile strength is 1600 MPa - 2400 MPa. Description of the Drawings

[0030] In order to more clearly illustrate the technical solutions in the embodiments of the present invention, the following will briefly introduce the drawings required for use in the embodiments or the description of the prior art. Obviously, the following drawings are only some embodiments of the present invention. For those of ordinary skill in the art, without creative efforts, other drawings can also be obtained based on these drawings.

[0031] Figure 1 It is the DSC diagram of Comparative Example 9 of the present invention.

[0032] Figure 2 It is the DSC diagram of Embodiment 1 of the present invention.

[0033] Figure 3 It is the corrosion resistance result of Embodiment 4 and Comparative Example 2 of the present invention, where Figure 3 a is Embodiment 4 and b is Comparative Example 2. Detailed Embodiments

[0034] In order to facilitate the understanding of a high-resistivity amorphous alloy strip of the present invention, the following will give a more comprehensive description of a high-resistivity amorphous alloy strip of the present invention, and embodiments of the present invention are given, but the scope of the present invention is not limited thereby.

[0035] We first prepared the non-eutectic strip of the present invention. The specific steps include:

[0036] Prepare an amorphous alloy strip with the molecular formula Fe a P b Cr c B d Si e Cu h Ni f Mo g , where a, b, c, d, e, f, g, h are atomic percentages, 65 ≤ a ≤ 77, 8 ≤ b ≤ 13, 5 ≤ c ≤ 10, 3 ≤ d ≤ 6, 0 < e ≤ 2, 0 < f ≤ 5, 1 ≤ g ≤ 5, 0 < h ≤ 2 and a + b + c + d + e + f + g + h = 100. The specific steps are as follows:

[0037] S1: Weigh iron with a purity of 99.9 wt%, silicon with a purity of 99.99 wt%, copper with a purity of 99.95 wt%, nickel with a purity of 99.95 wt%, chromium with a purity of 99.99 wt%, molybdenum with a purity of 99.95 wt%, ferroboron with a B content of 17.58 wt%, and ferrophosphorus with a P content of 25.10 wt% according to the atomic percentage content in the above alloy expression, and polish, pickling and cleaning the raw materials.

[0038] S2: Place the above cleaned raw materials in the crucible of a vacuum arc melting furnace, evacuate to below 5×10 -4 Pa, and then fill with 0.05 Mpa of argon gas, and melt in a high-purity argon atmosphere to prepare a master alloy ingot.

[0039] S3: After grinding and removing the oxide scale from the master alloy ingot obtained in the above step, place it in a quartz tube, melt the master alloy ingot into a metal melt by induction melting, spray the alloy melt onto a high-speed rotating copper roll with a copper roll speed of 35 m / s, and rapidly cool the molten alloy by the heat conduction of the copper roll to obtain the amorphous alloy strip of the present invention.

[0040] Comparative Example 1 - Comparative Example 4, Comparative Example 6: At 180 °C, test the crystal phase structure of the amorphous alloy strip.

[0041] Comparative Example 5: At 250 °C, test the crystal phase structure of the amorphous alloy strip.

[0042] We also used the obtained amorphous strip for various performance tests:

[0043] Test of resistivity: Measure the resistivity of the amorphous alloy strip at room temperature using a four-probe resistivity tester.

[0044] Test of hardness: Test the hardness of the strip using a Vickers hardness tester.

[0045] Test of strength: The strength of the strip is tested using a universal testing machine.

[0046] Test of structure: The crystal phase structure of the amorphous alloy strip is tested at 250 °C.

[0047] Test of glass-forming ability: The structure of the strip is characterized using an X-ray diffractometer.

[0048] Test of corrosion resistance: After 48 h salt spray test.

[0049] Analysis of verification results:

[0050] Table 1 Test results of the amorphous alloy strips of the embodiments and comparative examples of the present invention

[0051]

[0052]

[0053] Table 2 Test results of the embodiments and comparative examples of the present invention

[0054] Serial number Component ΔTx Trg γ Comparative Example 7 <![CDATA[Fe 74.8 P 13 Cr 5 B 2 Si 1 Cu 0.2 Ni 4 Mo 2 > 18 0.6028 0.3864 Comparative Example 8 <![CDATA[Fe 72.8 P 13 Cr 5 B 5 Si 0 Cu 0.2 Ni 4 Mo 2 > 42 0.6438 0.4214 Comparative Example 9 <![CDATA[Fe 82.8 P 2 Cr 5 B 5 Si 1 Cu 0.2 Ni 4 Mo 2 > 15 0.5896 0.3822 Example 8 <![CDATA[Fe 69.8 P 13 Cr 5 B 5 Si 1 Cu 0.2 Ni 4 Mo 2 > 55 0.6547 0.4514

[0055] We have successfully obtained the amorphous alloy strip of the present invention through the preparation method of the present invention. We tested the amorphous alloy strip obtained by the present invention and the amorphous alloy strips in the prior art, and the test results are shown in Table 1 - Table 2. From Table 1, we can see that by comparing Examples 1 - 15 with Comparative Examples 1 - 3, we found that the amorphous alloy strips obtained by the present invention all have better resistivity and amorphous forming ability, and can balance processing flexibility, hardness and strength. We mainly designed the obtained amorphous strip. Specifically, we used the amorphous alloy strip as an electrothermal material. On the one hand, we need to increase the resistivity of the amorphous alloy strip, and on the other hand, we can reduce the production cost of the material. Therefore, we need to design a higher atomic percentage of Fe in the amorphous alloy strip. We designed the atomic percentage of the amorphous alloy material between 65% - 77%. Although it promotes the increase of the resistance of the amorphous alloy material, the increase of Fe will, on the one hand, reduce the amorphous forming ability of the electro-amorphous alloy material, and on the other hand, it will also lead to the reduction of the toughness of the amorphous alloy strip, which can be verified by Comparative Example 1. We can find that in Comparative Example 1, due to the relatively high atomic percentage of Fe, the amorphous forming ability decreases; although the proportion of metalloid elements reaches 23 (at%), there are still precipitations of some crystalline phases, resulting in the reduction of its resistivity and the reduction of the electrothermal conversion rate, and it cannot heat up quickly, causing waste of energy resources. In order to further improve the amorphous forming ability of the amorphous alloy strip of the present invention, we also configured a P - B - Si - Cu doping system in the amorphous alloy material system to further enhance the ability and flexibility of the amorphous alloy. We can verify from the comparison between Comparative Example 1 and Comparative Examples 2 - 3 that in Comparative Examples 2 and 3, the P - B - Si - Cu doping system is configured. Therefore, the amorphous forming ability of the amorphous alloy strips prepared in Comparative Examples 2 and 3 increases. We found that for high - iron - based materials with more than 65% composition, in order to meet the heating use requirements above 200 °C, when the atomic percentage of P is higher than 8% and / or the atomic percentage of B is higher than 6%, the thermal stability and amorphous forming ability of the amorphous alloy strip can be improved. And as the Fe content increases, the addition amounts of P and B often need to increase accordingly. However, when the atomic percentage of P in the amorphous alloy strip is higher than 8% or the atomic percentage of B is lower than 6%, on the one hand, it may also affect the weakening of the amorphous forming ability of the amorphous alloy strip, and on the other hand, when the atomic percentage of P is higher than 8%, it is easy to cause element segregation in the amorphous alloy material, resulting in the reduction of the processing flexibility of the amorphous alloy strip, which can be verified by Comparative Example 4 and Table 2.In the present invention, in the doped system P-B-Cu-Si of the amorphous alloy strip, the atomic percentage of P is designed to be 8%-13% and the atomic percentage of B is 3%-6%. The amorphous alloy strip of the present invention still has good amorphous forming ability. We believe that, firstly, since the atomic percentage of Fe in the amorphous alloy strip of the present invention is higher, a higher atomic percentage of P or a lower atomic percentage of B is required to match the decrease in the amorphous forming ability caused by the high atomic percentage of Fe, which can be verified by comparing Examples 1-17 with Comparative Example 5; secondly, we doped the Mo-Ni system in the present invention, which can further improve the amorphous forming ability of the amorphous alloy strip and balance the flexibility, strength and hardness, which can be verified by comparing Examples 1-17 with Comparative Example 6. In addition, the increase in Fe content will lead to a decrease in its glass transition temperature, thereby affecting its usable temperature range, which can be verified by... Figure 1 and Figure 2 verified Figure 1 is the DSC curve of Comparative Example 9. It can be seen from the figure that its glass transition temperature is about 350 °C, and the Tg is relatively low, which affects its usable temperature range. The DSC curve of Example 1 is as Figure 2 shown. Its glass transition temperature is about 470 °C. In summary, through the design in the present invention, on the basis of obtaining an amorphous alloy strip with good resistivity, the processing flexibility, hardness and strength of the non-alloy strip are also balanced, and the amorphous alloy strip of the present invention can be applied to the low-temperature heating field not higher than 300 °C.

[0056] On this basis, we also carried out corrosion resistance tests on Example 4 of the present invention and Comparative Example 2, and the test results are as Figure 3 shown. We can find that corrosion occurred on the surface of the non-alloy strip in Comparative Example 2. It can be seen that Cr in the non-alloy strip can improve the corrosion resistance of the amorphous alloy strip.

[0057] We further studied the mutual cooperation between the atomic percentage of Fe in the amorphous alloy strip of the present invention and the doped Mo-Ni system. From the comparison of Examples 1 to 17 in Table 1, we found that with the change of the sum of the atomic percentages of Mo and Ni in the amorphous alloy strip, the improvement of the strength of the amorphous alloy strip is more significant. Since the amorphous alloy strip of the present invention needs to be applied to many environments, even in relatively special fields (such as aqueous solutions with fluidity), sufficient strength is required. Therefore, we need the strength of the amorphous alloy strip of the present invention to be higher than 1800 Mp. At this time, the sum of the atomic percentages of Mo and Ni in the amorphous alloy strip needs to be greater than 4.5%; adding more Mo and Ni in the amorphous alloy strip will inevitably affect the atomic percentage of Fe in the amorphous alloy strip, resulting in a decrease in the resistivity of the amorphous alloy strip. Therefore, in order to balance the strength and resistivity of the amorphous alloy strip, we further select the sum of the atomic percentages of Mo and Ni to be less than 8%, and the atomic percentage of Fe in the amorphous alloy strip to be higher than 68%. On this basis, we further compared Example 7 and Example 10 and found that Example 10 has better strength and hardness. We believe that when the sum of the atomic percentages of Ni and Mo in the amorphous alloy strip is equal, the difference in the atomic ratio between Ni and Mo will also improve the strength and hardness of the amorphous alloy strip to varying degrees. We found that when the atomic percentages of Ni and Mo in the amorphous alloy strip are 1-2, the amorphous alloy within this range has better resistivity while also having better strength and hardness. The atomic ratio of Ni and Mo in Example 7 of Table 1 is 2.5, and the atomic ratio of Ni and Mo in Example 10 is 1.3, which can also be verified by comparing Example 6 and Example 9. We further preferably select the atomic ratio of Ni and Mo in the amorphous alloy strip to be 1 ≤ f / g ≤ 2.

[0058] In summary, through the design of the present invention, an amorphous alloy strip that can be applied to the low-temperature electroheating field of 200°C - 300°C is obtained. On the basis that the amorphous alloy strip of the present invention has good processing flexibility, it also has higher resistivity, electrothermal conversion rate, corrosion resistance, and amorphous ability.

[0059] It should be noted that the above are only the preferred embodiments of the present invention and are not intended to limit the present invention. Any modifications, equivalent replacements, improvements, etc. made within the spirit and principles of the present invention shall be included in the protection scope of the present invention.

Claims

1. An amorphous alloy strip with high resistivity, characterized in that, The chemical formula of the amorphous alloy strip is Fe a P b Cr c B d Si e Cu h Ni f Mo g , where a, b, c, d, e, f, g, h are atomic percentages, 68 ≤ a ≤ 88, 10 ≤ b ≤ 13, 5 ≤ c ≤ 10, 3 ≤ d ≤ 6, 0 < e ≤ 2, 0 < f ≤ 5, 1 ≤ g ≤ 5, 4.5 < f + g < 8, 0 < h ≤ 2, and a + b + c + d + e + f + g + h = 100. Here, Fe represents the iron element, P represents the phosphorus element, Cr represents the chromium element, B represents the boron element, Si represents the silicon element, Ni represents the nickel element, Mo represents the molybdenum element, and Cu represents the copper element; the resistivity of the amorphous alloy strip is 160 μΩ·cm - 175 μΩ·cm, the Vickers microhardness HV0.3 of the amorphous alloy is 650 - 750, and the tensile strength is 1600 MPa - 2400 MPa.

2. The amorphous alloy strip with high resistivity according to claim 1, characterized in that, The chemical formula of the amorphous alloy strip is Fe a P b Cr c B d Si e Cu h Ni f Mo g , where a, b, c, d, e, f, g, h are atomic percentages, 68 ≤ a ≤ 88, 10 ≤ b ≤ 13, 5 ≤ c ≤ 10, 3 ≤ d ≤ 6, 0 < e ≤ 2, 4.5 < f + g < 8, 0 < h ≤ 2, 1 ≤ f / g ≤ 2, and a + b + c + d + e + f + g + h = 100.

3. The amorphous alloy strip with high resistivity according to claim 1, characterized in that, the Fe is derived from industrial pure iron, the P is derived from ferrophosphorus, the Cr is derived from chromium, the B is derived from ferroboron, the Si is derived from polysilicon, the Ni is derived from nickel, the Mo is derived from molybdenum, and the Cu is derived from copper.

4. The amorphous alloy strip with high resistivity according to claim 1, characterized in that, the glass transition temperature of the amorphous alloy strip is 440 °C - 500 °C.

5. The preparation method of the amorphous alloy strip according to any one of claims 1 - 4, characterized in that, the preparation method includes: S1: Weigh the raw materials according to the atomic percentage of the amorphous alloy strip, and the raw materials are iron, ferrophosphorus, chromium, ferroboron, silicon, nickel, molybdenum, and copper; S2: Clean the raw materials obtained in S1; S3: Melting the raw materials cleaned in S2 multiple times in a vacuum environment to obtain a master alloy ingot; S4: Melting the master alloy ingot and then rapidly cooling it to obtain the amorphous alloy strip.

6. The preparation method according to claim 5, characterized in that, argon gas of 0.04 Mpa - 0.06 Mpa is added to the vacuum environment in S3; the melting in S3 is specifically: during the first melting, add in the order of increasing melting point, ensuring that the raw materials with high melting points are on the upper layer.

7. The application of the amorphous alloy strip according to any one of claims 1 - 4, characterized in that, the amorphous alloy strip can be used in the low - temperature heating field below 300 °C.

8. The application according to claim 7, characterized in that, the amorphous alloy strip can be used in the low - temperature heating field below 300 °C and above 200 °C.

9. The application according to claim 7, characterized in that, the amorphous alloy strip can be used in the low - temperature heating field below 300 °C and above 250 °C.

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