Zirconium-niobium alloy with high activity / high density for shaped charge liner and preparation method of zirconium-niobium alloy

Abstract

The invention belongs to the technical field of alloy preparation, and particularly relates to a high-activity / high-density zirconium-niobium alloy for a shaped charge liner and a preparation method of the high-activity / high-density zirconium-niobium alloy. The zirconium-niobium alloy is prepared from the following elements in percentage by mass: 16.0 to 18.5 percent of Nb, 3.5 to 7.0 percent of W and the balance of Zr, and the sum of all the elements is 100 percent. Comprising the following steps that Zr blocks, Nb blocks and W blocks are weighed according to the element mass percent of the zirconium-niobium alloy; melting a button ingot in a vacuum arc melting manner to obtain the button ingot, and crushing the button ingot to obtain a blank; the blank is remelted in a laser melting mode, and pellets are obtained; and the material balls are subjected to laser heating and deep supercooling circulation in an electrostatic suspension mode, and the zirconium-niobium alloy for the shaped charge liner is obtained. Precipitation of brittle phases in the zirconium-niobium alloy preparation process can be effectively controlled, the component and structure uniformity of the zirconium-niobium alloy can be improved, and the shaped charge liner machining formability and damage effect stability are guaranteed.

Description

Technical Field

[0001] This invention belongs to the field of alloy preparation technology, specifically relating to a zirconium-niobium alloy for drug-formed liner with high activity and high density, and its preparation method. Background Technology

[0002] Zirconium-niobium alloys possess excellent comprehensive properties such as corrosion resistance, oxidation resistance, and biocompatibility, making them widely used in the nuclear industry, aerospace, medical and health, chemical and energy sectors. They are ideal materials for nuclear reactor fuel cladding and high-temperature components of aero-engines. Furthermore, as an active alloy, zirconium-niobium alloys are also among the best candidate materials for warhead liner and fragmentation. Meanwhile, the lethality of liner and fragmentation is significantly related to material density; the higher the material density, the greater the kinetic energy of the jet formed by the liner. High-density materials such as tantalum, copper, molybdenum, and their alloys exhibit good lethality and have a wide range of applications.

[0003] Compared to traditional metal shaped charge shields, zirconium-niobium alloys, while possessing good reactivity, have a lower density, limiting the damage effect of the resulting penetrator on the target. Therefore, the density of zirconium-niobium active alloys can be increased by adding high-density metal elements such as tungsten, thereby enhancing the damage capability of the zirconium-niobium active alloy shaped charge shield. However, tungsten has a density of 18 and a melting point of 3499℃. High-density tungsten powder tends to deposit downwards or even leak away under gravity during production. Furthermore, its high melting point means that tungsten powder cannot melt directly into the Zr alloy molten pool, leading to segregation. Therefore, controlling the compositional uniformity of zirconium-niobium-tungsten alloys is difficult. Thus, the addition of high-density alloying elements poses a challenge to the uniformity control of zirconium-niobium alloys and may also form a brittle W₂Zr phase within the matrix, causing cracking during processing. Summary of the Invention

[0004] To address the aforementioned problems, this invention provides a zirconium-niobium alloy for shaped charge liner applications with high activity and high density, along with its preparation method. This method effectively controls the precipitation of brittle phases during the preparation of the zirconium-niobium alloy and improves its compositional and microstructure uniformity, ensuring the formability of the shaped charge liner and the stability of its damage response.

[0005] The present invention solves the above-mentioned technical problems through the following technical solutions.

[0006] The first objective of this invention is to provide a method for preparing a zirconium-niobium alloy for a shaped charge liner with high activity and high density, comprising the following steps: S1. Weigh out Zr blocks, Nb blocks, and W blocks according to the elemental mass percentages of the zirconium-niobium alloy, and mix them to form a mixture.

[0007] S2. The mixed powder is melted into button ingots using vacuum arc melting to obtain button ingots, and the button ingots are crushed to obtain billets.

[0008] S3. The billet is remelted using laser melting to obtain pellets.

[0009] S4. Using electrostatic levitation, the material balls are laser-heated and subjected to deep supercooling cycles to obtain a zirconium-niobium alloy for shaped charges with high activity and high density.

[0010] Furthermore, the zirconium-niobium alloy is composed of the following elements by mass percentage: Nb: 16.0 wt.% to 18.5 wt.%, W: 3.5 wt.% to 7.0 wt.%, with the balance being Zr and unavoidable impurities, totaling 100%.

[0011] Furthermore, during the vacuum arc melting process, the melting temperature is 3500℃~4000℃, and the button ingot is melted 4 to 6 times. After each melting and solidification, the ingot is flipped over before the next melting. The vacuum degree before melting does not exceed 10. -3 Pa.

[0012] Furthermore, the diameter of the material balls is 2.5mm to 2.7mm.

[0013] Furthermore, during the laser melting process, the remelting temperature is 1960℃~1970℃, and the laser melting is performed 4 to 6 times.

[0014] Furthermore, the temperature of the light heating is 1960℃~1970℃, the degree of supercooling is 250K~300K, and the number of laser heating and deep supercooling cycles is 2 to 3.

[0015] Furthermore, the purity of Zr powder, Nb powder, and W powder is not less than 99.9%.

[0016] A second objective of this invention is to provide a zirconium-niobium alloy for drug-formed liner materials with high activity and high density, which is prepared using the above-described preparation method.

[0017] Compared with the prior art, the present invention has the following advantages: (0) The preparation method provided by the present invention uses vacuum arc melting to melt the mixed powder into button ingots. By repeatedly turning the arc melting over and over, the high-density elements are uniformly distributed in the button ingots. Melting in a high vacuum environment can avoid the oxidation of the Zr-Nb-W alloy. By using electrostatic suspension, the Zr-Nb-W alloy is subjected to deep supercooling and rapid solidification, achieving a high degree of homogeneity in microstructure and composition. In addition, deep supercooling and rapid solidification effectively suppresses the precipitation of a large amount of brittle W2Zr phase, reduces deformation resistance, and facilitates subsequent hot working and forming.

[0018] (1) The zirconium-niobium alloy for shaped charges provided by the present invention, by mass percentage, comprises the following elements: Nb: 16.0 wt.%~18.5 wt.%, W: 3.5 wt.%~7.0 wt.%, with the balance being Zr. Using Nb and Zr as the matrix, by controlling the element ratio of the zirconium-niobium alloy and introducing W, the density of the high-activity zirconium-niobium alloy is increased, resulting in a zirconium-niobium alloy with high activity and high density, which enhances the damage capability of the shaped charge and is an ideal material for preparing high-damage shaped charges. Attached Figure Description

[0019] Figure 1 This is a SEM image of the Zr-16Nb-7W alloy prepared in Example 1 of the present invention.

[0020] Figure 2 EDS image of the Zr-16Nb-7W alloy prepared in Example 1 of this invention.

[0021] Figure 3 SEM image of the Zr-18.5Nb-3.5W alloy prepared in Example 2 of this invention.

[0022] Figure 4 EDS image of the Zr-18.5Nb-3.5W alloy prepared in Example 2 of this invention.

[0023] Figure 5 This is a solidification microstructure diagram of the Zr-16Nb-7W alloy prepared in Comparative Example 1 of this invention. Detailed Implementation

[0024] The technical solutions of the embodiments of the present invention will be clearly and completely described below with reference to the accompanying drawings. Obviously, the described embodiments are only some embodiments of the present invention, and not all embodiments. Based on the embodiments of the present invention, all other embodiments obtained by those skilled in the art without creative effort are within the scope of protection of the present invention.

[0025] It should be noted that the technical terms used in this invention are only for the purpose of describing specific embodiments and are not intended to limit the scope of protection of this invention. Unless otherwise specified, all raw materials, reagents, instruments and equipment used in the following embodiments of this invention can be purchased from the market or prepared by existing methods.

[0026] Existing methods increase the density of zirconium-niobium active alloys by adding high-density metallic elements, thereby enhancing the damage capability of zirconium-niobium active alloy liner. However, the addition of high-density alloying elements makes it difficult to control the uniformity of the zirconium-niobium alloy and may also lead to the formation of brittle W2Zr phases in the matrix, causing cracking during processing. Therefore, it is crucial to select the zirconium-niobium alloy composition and suppress the precipitation of brittle phases through effective solidification methods. Based on this, this invention provides a highly active, high-density zirconium-niobium alloy and its rapid solidification preparation method, which improves the damage capability of the liner, effectively controls the precipitation of brittle phases during the preparation of the zirconium-niobium alloy, and improves its composition and microstructure uniformity, ensuring the formability of the liner and the stability of the damage effect. Details are as follows:

[0027] A method for preparing a zirconium-niobium alloy for a high-activity / high-density shaped charge liner includes the following steps: S1. Weigh out Zr blocks, Nb blocks, and W blocks according to the elemental mass percentages of the zirconium-niobium alloy, and mix them to form a mixture.

[0028] In this invention, the purity of the Zr block, Nb block, and W block is not less than 99.9%, and the weighing accuracy during the weighing process is 0.1 mg.

[0029] S2. The mixture is melted into button ingots using vacuum arc melting to obtain button ingots, and the button ingots are crushed to obtain billets.

[0030] In this invention, the crushing method is physical crushing. In a preferred embodiment, when calculating the proportion of each element, the total amount is 300mg to 500mg and the mass of the billet is 30mg to 50mg.

[0031] In this invention, during the vacuum arc melting process, the melting temperature is 3500℃~4000℃, and the button ingot is melted 4 to 6 times. After each melting and solidification, the ingot is flipped over before the next melting. The vacuum degree before melting does not exceed 10. - 3 Pa. Through multiple up-and-down arc melting processes, the high-density elements are uniformly distributed in the button ingot, and melting in a high vacuum environment can prevent the oxidation of the Zr-Nb-W alloy.

[0032] S3. The billet is remelted using laser melting to obtain pellets.

[0033] In this invention, during the laser melting process, the remelting temperature is 1960℃~1970℃, and the number of laser melting cycles is 4 to 6; the diameter of the material ball is 2.5mm~2.7mm.

[0034] S4. Using electrostatic levitation, the material balls are laser-heated and supercooled to obtain a zirconium-niobium alloy for shaped charges with high activity and high density.

[0035] In this invention, electrostatic levitation technology is a containerless levitation technique for charged materials under high vacuum / high pressure, where the electrostatic field balances the gravitational field. The high vacuum environment and containerless conditions avoid the oxidation problem of highly reactive metals at high temperatures, while simultaneously enabling rapid heating and melting of the metal material followed by deep undercooling and rapid solidification. This promotes uniform composition distribution, suppresses excessive precipitation of brittle phases, and facilitates the homogenization of highly reactive / high-density zirconium-niobium alloys for shaped charge liner preparation. Specifically, the number of laser heating and deep undercooling cycles is 2-3 times, the undercooling degree is 250K-300K, and the laser heating temperature is 1960℃-1970℃. This invention utilizes electrostatic levitation for the rapid undercooling solidification of Zr-Nb-W alloys, achieving a high degree of homogenization in microstructure and composition. Furthermore, rapid undercooling solidification effectively suppresses the excessive precipitation of the brittle W2Zr phase, reducing deformation resistance and facilitating subsequent hot working.

[0036] In this invention, the zirconium-niobium alloy is composed of the following elements by mass percentage: Nb: 16.0 wt.% to 18.5 wt.%, W: 3.5 wt.% to 7.0 wt.%, with the balance being Zr and unavoidable impurities, totaling 100%.

[0037] It should be noted that in the chemical composition of the Zr-Nb-W alloy provided by this invention, Nb and Zr are used as the matrix. Increasing the Nb content is beneficial to improving the elastic modulus of the zirconium-niobium alloy. The matrix is ​​mainly β-(Zr,Nb) solid solution. However, as a material for propellant liner, although the zirconium-niobium alloy has good activity characteristics, its density is lower than that of traditional pure copper, tantalum, and molybdenum propellant liner. Therefore, by controlling the element ratio of the zirconium-niobium alloy and introducing W, the material density is increased through the addition of W, thereby achieving both activity and density. While the process enhances the effectiveness of the Zr-Nb-W alloy, W elements readily combine with Zr elements in the alloy to precipitate the brittle W2Zr phase, an intermetallic compound that easily precipitates at grain boundaries, thus deteriorating the material's deformation and processing properties. This invention, through rapid solidification, suppresses W element segregation, reduces the possibility of W2Zr brittle phase precipitation at grain boundaries, and increases the density of the high-activity zirconium-niobium alloy, resulting in a zirconium-niobium alloy with high activity and high density. This enhances the damage capability of the shaped charge shield and makes it an ideal material for preparing high-damage shaped charge shields, ensuring the feasibility of cold and hot processing of the Zr-Nb-W alloy.

[0038] The following specific examples will provide further explanation.

[0039] Example 1 A highly active / high-density Zr-16Nb-7W zirconium-niobium alloy is composed of the following elements by mass percentage: Nb: 16wt.%, W: 7.0wt.%, with the balance being Zr and unavoidable impurities, totaling 100%.

[0040] The preparation method of the above-mentioned Zr-16Nb-7W zirconium-niobium alloy includes the following steps: S1. Calculate the batching according to the elemental mass percentages of the Zr-16Nb-7W zirconium-niobium alloy. The total amount of each element is 300mg. Use high-purity metals of Zr, Nb, and W with a mass fraction of not less than 99.9wt.%, weigh and dispense them using a high-precision electronic balance with a weighing accuracy of 0.1mg, and mix them to form a mixed powder.

[0041] S2. Button ingots are melted using a vacuum arc furnace. The vacuum arc melting current is 200A, and the melting temperature is 3500℃. A total of four melting processes are performed, with the ingots flipped over after solidification in each melting process before the next melting. The vacuum degree before melting must not exceed 10°C. -3 Pa, the finished button ingots are physically crushed, weighed and reassembled to obtain blanks, each blank weighing 30mg to 50mg.

[0042] S3. The billet is remelted three times using laser melting at a temperature of 1969℃ to obtain Zr-16Nb-7W pellets with a diameter of 2.5mm.

[0043] S4. An electrostatic levitation system is used to perform two laser heating and deep supercooling cycles on the material balls. The laser melting heating temperature is 1969℃, and the supercooling degree is 300K, to obtain a zirconium-niobium alloy for the shaped charge liner with high activity and high density.

[0044] Example 2 A highly active / high-density Zr-18.5Nb-3.5W zirconium-niobium alloy, which is composed of the following elements by mass percentage: Nb: 18.5wt.%, W: 3.5wt.%, with the balance being Zr and unavoidable impurities, totaling 100%.

[0045] The preparation method of the above-mentioned Zr-18.5Nb-3.5W zirconium-niobium alloy includes the following steps: S1. Calculate the batching according to the elemental mass percentages of the Zr-18.5Nb-3.5W zirconium-niobium alloy. The total amount of each element is 500mg. Use high-purity metals of Zr, Nb, and W with a mass fraction of not less than 99.9wt.%, weigh and dispense them using a high-precision electronic balance with a weighing accuracy of 0.1mg, and mix them to form a mixed powder.

[0046] S2. Button ingots are melted using a vacuum arc furnace. The vacuum arc melting current is 200A, and the melting temperature is 3500℃. A total of 6 melting cycles are performed, with the ingots flipped over after solidification in each cycle before the next melting cycle. The vacuum degree before melting must not exceed 10°C. -3 Pa, the finished button ingots are physically crushed, weighed and reassembled to obtain blanks, each blank weighing 30~50mg.

[0047] S3. The billet is remelted four times using laser melting at a temperature of 1960℃ to obtain Zr-18.5Nb-3.5W spheres with a diameter of 2.5mm.

[0048] S4. An electrostatic levitation system is used to perform three laser heating and deep supercooling cycles on the spheres. The laser melting heating temperature is 1960℃, and the supercooling degree is 250K, to obtain a zirconium-niobium alloy for shaped charges with high activity and high density.

[0049] Example 3 A highly active / high-density Zr-12Nb-7W zirconium-niobium alloy is composed of the following elements by mass percentage: Nb: 12wt.%, W: 7.0wt.%, with the balance being Zr and unavoidable impurities, totaling 100%.

[0050] The preparation method of the above-mentioned Zr-12Nb-7W zirconium-niobium alloy includes the following steps: S1. Calculate the proportions of each element in the Zr-12Nb-7W zirconium-niobium alloy according to their elemental mass percentages. The total amount of each element is 300mg. Use high-purity metals of Zr, Nb, and W with a mass fraction of not less than 99.9wt.%, weigh and dispense them using a high-precision electronic balance with a weighing accuracy of 0.1mg, and mix them to form a mixed powder.

[0051] S2. Button ingots are melted using a vacuum arc furnace. The vacuum arc melting current is 200A, and the melting temperature is 3500℃. A total of four melting processes are performed, with the ingots flipped over after solidification in each melting process before the next melting. The vacuum degree before melting must not exceed 10°C. -3 Pa, the finished button ingots are physically crushed, weighed and reassembled to obtain blanks, each blank weighing 30mg to 50mg.

[0052] S3. The billet is remelted three times using laser melting at a temperature of 1969℃ to obtain Zr-12Nb-7W pellets with a diameter of 2.5mm.

[0053] S4. An electrostatic levitation system is used to perform two laser heating and deep supercooling cycles on the material balls. The supercooling degree is 295K, the laser melting heating temperature is 1969℃, and the supercooling degree is 300K, resulting in a zirconium-niobium alloy for the shaped charge liner with high activity and high density.

[0054] Comparative Example 1 A Zr-16Nb-7W zirconium-niobium alloy, the zirconium-niobium alloy is composed of the following elements by mass percentage: Nb: 16wt.%, W: 7.0wt.%, with the balance being Zr and unavoidable impurities, the total of all elements being 100%.

[0055] The preparation method of the above-mentioned Zr-16Nb-7W zirconium-niobium alloy includes the following steps: S1. Calculate the batching according to the elemental mass percentages of the Zr-16Nb-7W zirconium-niobium alloy. The total amount of each element is 300mg. Use high-purity metals of Zr, Nb, and W with a mass fraction of not less than 99.9wt.%, weigh and dispense them using a high-precision electronic balance with a weighing accuracy of 0.1mg, and mix them to form a mixture.

[0056] S2. Button ingots are melted using a vacuum arc furnace. The vacuum arc melting current is 200A, and the melting temperature is 3500℃. A total of four melting processes are performed, with the ingots flipped over after solidification in each melting process before the next melting. The vacuum degree before melting must not exceed 10°C. -3 Pa, the finished button ingots are physically crushed, weighed and reassembled to obtain blanks, each blank weighing 30mg to 50mg.

[0057] S3. The billet is remelted three times using laser melting at a temperature of 1969℃ to obtain Zr-16Nb-7W pellets with a diameter of 2.5mm.

[0058] S4. Using an electrostatic levitation system, the material ball is subjected to laser heating and cooling once. The laser melting heating temperature is 1969℃ and the cooling temperature is 300K to obtain Zr-16Nb-7W zirconium-niobium alloy.

[0059] Comparative Example 2 A Zr-18.5Nb-3.5W zirconium-niobium alloy, the zirconium-niobium alloy is composed of the following elements by mass percentage: Nb: 18.5wt.%, W: 3.5wt.%, balance Zr and unavoidable impurities, the total of all elements being 100%.

[0060] The preparation method of the above-mentioned Zr-18.5Nb-3.5W zirconium-niobium alloy includes the following steps: S1. Calculate the batching according to the elemental mass percentages of the Zr-18.5Nb-3.5W zirconium-niobium alloy. The total amount of each element is 300mg. Use high-purity metals of Zr, Nb, and W with a mass fraction of not less than 99.9wt.%, weigh and dispense them using a high-precision electronic balance with a weighing accuracy of 0.1mg, and mix them to form a mixture.

[0061] S2. Button ingots are melted using a vacuum arc furnace. The vacuum arc melting current is 200A, and the melting temperature is 3500℃. A total of four melting processes are performed, with the ingots flipped over after solidification in each melting process before the next melting. The vacuum degree before melting must not exceed 10°C. -3 Pa, the finished button ingots are physically crushed, weighed and reassembled to obtain blanks, each blank weighing 30~50mg.

[0062] S3. The billet is remelted three times using laser melting at a temperature of 1960℃ to obtain Zr-18.5Nb-3.5W pellets.

[0063] S4. Using an electrostatic levitation system, the material ball is subjected to laser heating and cooling once. The laser melting heating temperature is 1969℃ and the cooling temperature is 250K, to obtain Zr-18.5Nb-3.5W zirconium-niobium alloy.

[0064] The structure and properties of the nickel-based zirconium-niobium alloys prepared in the examples and comparative examples were tested, and the results are as follows.

[0065] Figure 1 This is a SEM image of the 300K deep supercooled Zr-16Nb-7W alloy obtained in Example 1 of the present invention. Figure 2 This is the EDS image of the 300K deep supercooled Zr-16Nb-7W alloy obtained in Example 1 of this invention. Figure 1 and Figure 2 It can be seen that the amount of brittle phase precipitated by W2Zr is relatively small, and the distribution of each element is relatively uniform.

[0066] Figure 3 This is a SEM image of the 250K deep supercooled Zr-18.5Nb-3.5W alloy obtained in Example 2 of this invention. Figure 4 This is the EDS image of the 250K deep supercooled Zr-18.5Nb-3.5W alloy obtained in Example 2 of this invention. Figure 3 and Figure 4 It can be seen that the amount of brittle phase precipitated by W2Zr is relatively small, and the distribution of each element is relatively uniform.

[0067] Figure 5The image shows a SEM image of the low-undercooled Zr-16Nb-7W alloy obtained in Comparative Example 1 of this invention. As shown in the figure, compared with the morphology image of the cold Zr-16Nb-7W alloy prepared in Example 1, it can be seen that the amount of precipitated phase in the deeply undercooled sample obtained by multiple heating and cooling cycles is significantly lower.

[0068] The zirconium-niobium alloys prepared in Examples 1-2 and Comparative Examples 1-2 were subjected to nanoindentation tests. The results are shown in Table 1. The average nanohardness of the Zr-16Nb-7W alloy prepared in Example 1 was 3.56 GPa, the average nanohardness of the Zr-18.5Nb-3.5W alloy prepared in Example 2 was 3.31 GPa, the average nanohardness of the Zr-16Nb-7W alloy prepared in Comparative Example 1 was 3.28 GPa, and the average nanohardness of the Zr-18.5Nb-3.5W alloy prepared in Comparative Example 2 was 2.77 GPa. The supercooling degree obtained by Comparative Examples 1 and 2 after one heating and cooling cycle was low, and the hardness was reduced compared with the deeply supercooled samples of the same composition.

[0069] Table 1. Results of nanoindentation testing on zirconium-niobium alloys It should be noted that when numerical ranges are involved in this invention, it should be understood that both endpoints of each numerical range and any value between the two endpoints can be selected. Since the steps and methods used are the same as in the embodiments, preferred embodiments are described here to avoid redundancy. Although preferred embodiments of the invention have been described, those skilled in the art, once they understand the basic inventive concept, can make other changes and modifications to these embodiments. Therefore, the appended claims are intended to be interpreted as including the preferred embodiments as well as all changes and modifications falling within the scope of this invention.

[0070] Obviously, those skilled in the art can make various modifications and variations to this invention without departing from its spirit and scope. Therefore, if these modifications and variations fall within the scope of the claims of this invention and their equivalents, this invention also intends to include these modifications and variations.

Claims

1. A method for producing a zirconium-niobium alloy for a high-activity / high-density shaped charge, characterized by, The method comprises the following steps: According to the elemental mass percentage of the zirconium-niobium alloy, Zr blocks, Nb blocks and W blocks are weighed and mixed to form a mixture; The mixed powder is subjected to button ingot smelting by vacuum arc smelting to obtain button ingots, and the button ingots are crushed to obtain billets; The billets are subjected to remelting by laser smelting to obtain material balls; The material balls are subjected to laser heating and deep undercooling cycles by electrostatic suspension to obtain a zirconium-niobium alloy with high activity and high density for a liner.

2. The method of producing a zirconium-niobium alloy for a high-activity / high-density muffler according to claim 1, characterized in that, The zirconium-niobium alloy is composed of the following mass percentages of elements : Nb: 16.0wt.%-18.5wt.%, W: 3.5wt.%-7.0wt.%, the balance being Zr and unavoidable impurities, and the total of the elements being 100%.

3. The method of producing a zirconium-niobium alloy for a high-activity / high-density muffler according to claim 1, characterized in that, The temperature of the vacuum arc melting process is 3500-4000℃, the number of melting of the button ingot is 4-6 times, and the button ingot is turned up and down after solidification of each melting and then the next melting is carried out. The vacuum degree before melting is not more than 10 -3 Pa.

4. The method of producing a zirconium-niobium alloy for a high-activity / high-density muffler according to claim 1, characterized in that, The diameter of the material balls is 2.5mm-2.7mm.

5. The method of producing a zirconium-niobium alloy for a high-activity / high-density muffler according to claim 1, characterized in that, During the laser smelting process, the remelting temperature is 1960℃-1970℃, and the number of laser smelting is 4-6 times.

6. The method of producing a zirconium-niobium alloy for a high-activity / high-density muffler according to claim 1, characterized in that, The laser heating temperature is 1960℃-1970℃, the undercooling degree of deep undercooling is 250K-300K, and the number of laser heating and deep undercooling cycles is 2-3 times.

7. The method of producing a zirconium-niobium alloy for a high-activity / high-density muffler according to claim 1, characterized in that, The purity of the Zr powder, Nb powder and W powder is not less than 99.9%.

8. A zirconium-niobium alloy for a high activity / high density shaped charge, characterized by The preparation method is prepared by any one of claims 1-7.

Images