High-manganese high-entropy alloy binder with high toughness, low thermal conductivity and preparation method and application thereof
By adding Mn and Ti elements to traditional binders, the composition and process of high-entropy alloy binders were optimized, solving the problem of high thermal conductivity in binders for armor-piercing projectiles. This resulted in high toughness and low thermal conductivity, thus improving penetration performance.
Patent Information
- Authority / Receiving Office
- CN · China
- Patent Type
- Applications(China)
- Current Assignee / Owner
- Filing Date
- 2026-01-13
- Publication Date
- 2026-04-03
AI Technical Summary
The high thermal conductivity of the binder used in existing armor-piercing projectiles causes the tip of the tungsten-high-entropy alloy composite material to become passivated during penetration, affecting its penetration performance.
By adding Mn and Ti elements to the traditional binders Fe and Ni, the alloy element composition of the high-entropy alloy binder is optimized, and a high-manganese high-entropy alloy binder with high toughness and low thermal conductivity is prepared. A single-phase FCC structure is formed by vacuum arc melting process.
It reduces thermal conductivity, increases adiabatic shear sensitivity, enhances the penetration performance of armor-piercing projectiles, maintains high toughness, and has a simple manufacturing process that facilitates industrialization.
Smart Images
Figure CN121780971A_ABST
Abstract
Description
Technical Field
[0001] This invention belongs to the technical field of high-entropy alloy materials for armor-piercing projectiles, and mainly relates to a high-toughness, low-thermal-conductivity, high-manganese, high-entropy alloy binder, its preparation method, and its application, specifically a high-manganese, high-entropy alloy binder for the core of a high-toughness, low-thermal-conductivity armor-piercing projectile. Background Technology
[0002] Tanks are known as the kings of land warfare. Since World War II, local wars around the world have shown that armored forces, led by tanks, have gradually become a crucial force in determining victory. Armor-piercing projectiles, as one of the most important anti-tank and anti-armor weapons, have developed rapidly in the struggle against armor protection. Among them, rod-type armor-piercing projectiles have become one of the most lethal types of projectiles against tanks worldwide. The projectile core is the main part of a rod-type armor-piercing projectile, achieving a length-to-diameter ratio of 15-30, with a penetration velocity typically between 1000 m / s and 1700 m / s. Due to the special service environment of armor-piercing projectiles, the core material requires high density, high hardness, high strength, and good toughness. Currently, the main materials for armor-piercing projectile cores are depleted uranium alloys and tungsten alloys. The quasi-static mechanical properties of depleted uranium alloys and tungsten alloys are very similar, but depleted uranium alloys have a stronger penetration capability against armor. Under otherwise identical conditions, depleted uranium alloys achieve a penetration depth approximately 10%–15% greater than tungsten alloys. This is primarily attributed to the lower specific heat capacity, thermal conductivity, and melting point of depleted uranium alloys, making them more prone to thermal softening and localized deformation during penetration, exhibiting higher adiabatic shear sensitivity. During high-speed penetration, the projectile head continuously undergoes damage and spalling, a phenomenon known as "self-sharpening," maintaining a relatively sharp projectile shape, reducing penetration resistance, and decreasing the aperture diameter, thereby significantly enhancing penetration capability. In contrast, tungsten alloys are insensitive to adiabatic shear, undergoing thermoplastic softening in the early stages of high-speed penetration, resulting in a "mushroom head" shape for the projectile head, followed by the formation of adiabatic shear bands. This leads to increased penetration resistance and significantly weakens their penetration performance.
[0003] As a new alloy design concept that has emerged in recent years, high-entropy alloys are solid solution alloys formed by mixing five or more alloying elements in equimolar or near-equimolar ratios. They have characteristics such as high mixing entropy, severe lattice distortion, short-range order, and hysteretic diffusion, which give them great advantages in high and low temperature performance, breaking the strong-plastic compatibility barrier, penetration self-sharpening performance, and radiation resistance. Therefore, they have broad application prospects in aero-engines, icebreaker propellers, artillery barrels, armor-piercing projectile cores, and nuclear energy.
[0004] First, the high mixing entropy effect of high-entropy alloys gives them excellent high-temperature stability. Second, the multi-principal-element alloy design concept of high-entropy alloys breaks free from the constraints of the inherent properties of the main elements, achieving atomic-level "free" design and combination, which is beneficial for breaking the strong-ductility barrier and achieving a strong-ductility match. Furthermore, the severe lattice distortion effect of high-entropy alloys increases phonon and electron scattering, thereby reducing thermal conductivity. During high-speed penetration, adiabatic shear bands are easily generated, achieving head self-sharpening. The short-range order / clusters in high-entropy alloys can exert a strong short-range barrier effect on the dynamic movement of dislocations, making the alloy exhibit high strain rate sensitivity and positive strain rate effect, thus giving it excellent impact resistance.
[0005] Tungsten-high-entropy alloy composites are composite high-entropy alloy phases with tungsten as the matrix. Tungsten is mixed with armor-piercing projectiles using a binder and then sintered to obtain the tungsten-high-entropy alloy composite. This composite combines the high density and high hardness of tungsten with the high-entropy effect, hysteresis diffusion effect, and cocktail effect of high-entropy alloys, resulting in a composite material that exhibits both low thermal conductivity and excellent performance. According to the adiabatic shear energy dissipation formula:
[0006] Γ= ( ) 1 / 4 , χ = Where ρ is the material density, c is the specific heat capacity, a is the thermal softening coefficient, χ is the thermal diffusivity, and λ is the thermal conductivity; when λ decreases, Γ decreases, which is beneficial to the adiabatic shear of the material and enhances its penetration performance. Traditional armor-piercing projectiles use Fe and Ni as the main binders. At room temperature, the thermal conductivity of iron is 80.4 W / (m·K), and that of nickel is 90.9 W / (m·K). High thermal conductivity affects the overall adiabatic shear sensitivity of the material. Consequently, armor-piercing projectiles made with Fe and Ni-based binders will cause the projectile core to take on a "mushroom head" shape during penetration, leading to increased penetration resistance and affecting the penetration performance of the armor-piercing projectile. Summary of the Invention
[0007] To address the issue that traditional binders, primarily composed of Fe and Ni with high thermal conductivity, lead to high thermal conductivity and head passivation in existing tungsten-high-entropy alloy composites, this invention provides a high-toughness, low-thermal-conductivity armor-piercing projectile core high-manganese high-entropy alloy binder, its preparation method, and its application. By optimizing the alloy element composition of the high-entropy alloy binder, the performance shortcomings of traditional binders in harsh service environments are overcome, resulting in a binder with low thermal conductivity and high toughness. This invention aims to improve the thermal shear sensitivity of tungsten-high-entropy alloy composites and enhance their penetration performance.
[0008] To achieve the above objectives, the present invention adopts the following technical solution: This invention protects a high-manganese high-entropy alloy binder for a high-toughness, low-thermal-conductivity armor-piercing projectile core. As shown in Table 1, this invention considers that Mn and Ti elements, while possessing low thermal conductivity, are beneficial for adiabatic shearing; therefore, Mn and Ti elements are added to the conventional binder Fe–Co–Ni. Based on atomic ratio, the composition of the high-manganese high-entropy alloy binder for the high-toughness, low-thermal-conductivity armor-piercing projectile core is: Mn... 35-y -Ti x -(Fe–Co-Ni) 65-x+y Where x is 0at.%~8at.%, y is 0at.%~5at.%, and x and y cannot be 0 at the same time.
[0009] This invention primarily involves adding and adjusting the elements and proportions in a high-manganese high-entropy alloy binder for high-toughness, low-thermal-conductivity armor-piercing projectile cores. Combined with the performance of the finished product, this invention designs a high-manganese high-entropy alloy binder that simultaneously possesses high toughness and low thermal conductivity. While ensuring the toughness of the high-manganese high-entropy alloy binder, this invention reduces its thermal conductivity, resulting in an elongation greater than 10% and a room-temperature thermal conductivity less than 10 W / (m·K). As shown in Table 2, the traditional armor-piercing projectile binder Fe... 31 –Co6–Ni 63 The thermal conductivity is 43.258 W / (m·K), which is much lower than that of the high-manganese high-entropy alloy binder used in this invention.
[0010] Preferably, the elongation of the high-manganese high-entropy alloy binder used in the high-toughness, low-thermal-conductivity armor-piercing projectile core is ≥10%.
[0011] This invention also protects a method for preparing a high-manganese, high-entropy alloy binder for a high-toughness, low-thermal-conductivity armor-piercing projectile core, comprising the following steps: According to the atomic ratio Mn 35-y -Ti x -(Fe–Co-Ni) 65-x+y Where x is 0 at.%~8 at.%, y is 0 at.%~5 at.%, calculate the required mass of each element, then weigh iron, cobalt, nickel, manganese and titanium, and smelt them using a non-consumable vacuum arc melting furnace to prepare a high-toughness, low thermal conductivity armor-piercing projectile core high-manganese high-entropy alloy binder.
[0012] Preferably, the melting conditions are: melting for 5 minutes under a stirring current of 10A~20A and a melting current of 350A~500A, followed by cooling, and repeating the melting process at least 8 times.
[0013] Preferably, the amount of iron, cobalt, nickel, manganese, and titanium weighed is 1.02 to 1.04 times their calculated value.
[0014] This invention also protects the application of high-manganese high-entropy alloy binders for high-toughness, low-thermal-conductivity armor-piercing projectile cores in the preparation of high-toughness, low-thermal-conductivity armor-piercing projectile cores.
[0015] Preferably, the application method is as follows: tungsten is mixed with a high-toughness, low-thermal-conductivity armor-piercing projectile core using a high-manganese, high-entropy alloy binder, and then sintered in a hydrogen or vacuum atmosphere to obtain a high-toughness, low-thermal-conductivity armor-piercing projectile core.
[0016] The mass ratio of tungsten to the high-manganese high-entropy alloy binder for the high-toughness, low-thermal-conductivity armor-piercing projectile core is 88~97:3~12; the sintering conditions are: sintering at 1400℃~1500℃ for 0.5h.
[0017] Compared with the prior art, the present invention has the following advantages due to the adoption of the above technical solution: 1. This invention aims to address the problem of insufficient penetration performance caused by the high thermal conductivity of Fe and Ni elements in existing binders, which leads to passivation of the thermoplasticized head of tungsten-high-entropy alloy composites. To address the shortcomings of existing high-entropy alloy binders for armor-piercing projectiles, this invention provides a high-entropy alloy binder for armor-piercing projectiles. By optimizing the alloy element composition and ratio of the high-entropy alloy binder, the performance limitations of traditional binders under harsh service environments are overcome. The high-entropy alloy binder designed in this invention is composed of five elements—Mn, Ti, Fe, Co, and Ni—in a specific atomic ratio and is prepared through a vacuum arc melting process to form a single-phase FCC structure, exhibiting excellent performance (elongation ≥10%, thermal conductivity ≤10 W / (m·K)). The high-manganese high-entropy alloy binder of this invention has low thermal conductivity, which helps reduce the adiabatic shear energy consumption of tungsten-high-entropy alloy composites, resulting in high adiabatic shear sensitivity during armor penetration, improving the penetration power of armor-piercing projectiles, and thus enhancing their penetration performance.
[0018] 2. High toughness: Through composition design, the high manganese high entropy alloy binder retains the high toughness characteristics of traditional binders.
[0019] 3. Low thermal conductivity: Through compositional design, the thermal conductivity of the high-manganese high-entropy alloy binder is significantly reduced compared to traditional binders. This low thermal conductivity helps reduce the adiabatic shear energy dissipation of the tungsten-high-entropy alloy composite material, resulting in high adiabatic shear sensitivity during armor penetration and thus improving the penetration power of the armor-piercing projectile.
[0020] 4. Simple process: The present invention adopts vacuum arc melting process, which is simple to prepare and easy to promote industrialization. Attached Figure Description
[0021] Figure 1 Mn in Embodiment 1 of the present invention 33 –Ti0–Fe 15 –Co 15–Ni 37 Composition phase diagram.
[0022] Figure 2 Mn in Embodiment 1 of the present invention 33 –Ti0–Fe 15 –Co 15 –Ni 37 Stretching curve.
[0023] Figure 3 Mn in Embodiment 1 of the present invention 33 –Ti0–Fe 15 –Co 15 –Ni 37 Tensile fracture analysis diagram.
[0024] Figure 4 Mn in Embodiment 1 of the present invention 33 –Ti0–Fe 15 –Co 15 –Ni 37 EBSD diagram.
[0025] Figure 5 Mn in Embodiment 2 of the present invention 33 –Ti5–Fe 20 –Co 10 –Ni 32 Composition diagram.
[0026] Figure 6 Mn in Embodiment 2 of the present invention 33 –Ti5–Fe 20 –Co 10 –Ni 32 Stretching curve.
[0027] Figure 7 Mn in Embodiment 2 of the present invention 33 –Ti5–Fe 20 –Co 10 –Ni 32 Tensile fracture analysis diagram.
[0028] Figure 8 Mn in Embodiment 2 of the present invention 33 –Ti5–Fe 20 –Co 10 –Ni 32 EBSD diagram.
[0029] Figure 9 Mn in Embodiment 3 of the present invention 35 –Ti8–Fe 10 –Co 20 –Ni 27 Composition phase diagram.
[0030] Figure 10 Mn, which is Comparative Example 2 of the present invention 40 –Ti5–Fe 15 –Co 15 -Ni 25 Composition phase diagram.
[0031] Figure 11 Mn, which is Comparative Example 2 of the present invention 40 –Ti5–Fe 15 –Co 15 -Ni 25 Stretching curve.
[0032] Figure 12 Mn, which is Comparative Example 3 of the present invention 35 –Ti 10 –Fe 15 –Co 15 -Ni 25 Composition phase diagram.
[0033] Figure 13 The components are Fe, Co, Ni, and Fe from Comparative Example 1. 31 –Co6–Ni 63 Mn in Example 1 33 –Ti0–Fe 15 –Co 15 –Ni 37 Mn in Example 2 33 –Ti5–Fe 20 –Co 10 –Ni 32 And Mn in Example 3 35 –Ti8–Fe 10 –Co 20 –Ni 27 A comparison chart of thermal conductivity. Detailed Implementation
[0034] The present invention will be specifically described below through embodiments. It should be noted that the following embodiments are only used to further illustrate the present invention and should not be construed as limiting the scope of protection of the present invention. Those skilled in the art can make some non-essential improvements and adjustments to the present invention based on the above content.
[0035] This invention provides a high-manganese, high-entropy alloy binder for the core of a high-toughness, low-thermal-conductivity armor-piercing projectile. Its composition, calculated by atomic ratio, is: Mn 35-y -Ti x -(Fe–Co-Ni) 65-x+y , where x is 0at.%~8at.% and y is 0at.%~5at.%.
[0036] Considering that the main components of traditional binders are Fe and Ni, which have high thermal conductivity, this invention provides a high-manganese high-entropy alloy binder for armor-piercing projectile cores with high toughness and low thermal conductivity. Compared with traditional binders, it effectively reduces thermal conductivity. In addition, it is generally believed that adding other metals to traditional binders will lead to a decrease in toughness. However, in this invention, the research results show that adding a certain amount of Mn and Ti to traditional binders still maintains the original toughness of traditional binders, that is, effectively reducing thermal conductivity while ensuring mechanical properties.
[0037] A high-manganese, high-entropy alloy binder for a high-toughness, low-thermal-conductivity armor-piercing projectile core is prepared according to the following steps: According to the atomic ratio Mn 35-y -Ti x -(Fe–Co-Ni) 65-x+y Where x is 0 at.%~8 at.% and y is 0 at.%~5 at.%, the required mass of each element is calculated, and material loss must be considered in the calculation process. A non-consumable vacuum arc melting furnace is used for melting to prepare a high manganese high entropy alloy binder sample, namely a high manganese high entropy alloy binder for high toughness and low thermal conductivity armor-piercing projectile core.
[0038] EBSD images of high-manganese high-entropy alloy binder samples were captured using a scanning electron microscope with an EBSD probe.
[0039] Using a wire cutting machine, the high-manganese high-entropy alloy binder sample was cut into tensile specimens of 40mm×9mm×1.5mm. Metallographic sandpaper was used to polish the surface and both sides of the tensile specimens to a smooth finish, free from defects such as burrs, scratches, and cracks. Then, a universal testing machine was used to perform tensile tests on the high-manganese high-entropy alloy binder used in the core of a high-toughness, low-thermal-conductivity armor-piercing projectile.
[0040] Fracture surfaces of tensile specimens made with high-manganese high-entropy alloy binders were photographed using a scanning electron microscope.
[0041] The thermal conductivity of the high-manganese high-entropy alloy binder samples at room temperature was tested using a thermal conductivity meter.
[0042] The technical solution of the present invention will be studied below using examples and comparative examples. The specific research methods and results are shown below: Example 1 A method for preparing a high-toughness, low-thermal-conductivity armor-piercing projectile core high-manganese high-entropy alloy binder, wherein the high-toughness, low-thermal-conductivity armor-piercing projectile core high-manganese high-entropy alloy binder is composed of Mn 33 –Ti0–Fe 15 –Co 15 –Ni 37 This includes the following steps: Based on atomic ratio, the high-manganese high-entropy alloy binder used in the core of a high-toughness, low-thermal-conductivity armor-piercing projectile is prepared from iron, cobalt, nickel, manganese, and titanium, yielding Mn. 35-y -Ti x -(Fe–Co-Ni) 65-x+y , where x is 0 at.% and y is 2 at.%.
[0043] According to the atomic ratio Mn 33 –Ti0–Fe 15 –Co 15 –Ni 37 Calculate the required mass of each element, weigh 40.13g of iron, 40.81g of cobalt, 101.723g of nickel, and 88.727g of manganese, and melt them using a non-consumable vacuum arc melting furnace. The melting conditions are: melting for 5 minutes at a stirring current of 15A and a melting current of 400A, followed by cooling, to prepare a rectangular high-manganese high-entropy alloy binder sample with a diameter of 70mm × 45mm × 10mm and a weight of 260g.
[0044] The component is Mn 33 –Ti0–Fe 15 –Co 15 –Ni 37 The high-toughness, low-thermal-conductivity armor-piercing projectile core uses a high-manganese, high-entropy alloy binder. The composition phase diagram was calculated using JMatPro, as follows: Figure 1 As shown, the phase diagram only contains the liquid phase and the FCC phase, and there are no other impurity phases such as intermetallic compounds. The impurity phases are relatively brittle and affect the plasticity of the composite material after forming a composite material with tungsten.
[0045] The component was identified using a scanning electron microscope with an EBSD probe; 33 –Ti0–Fe 15 –Co 15 –Ni 37 EBSD of high-toughness, low-thermal-conductivity armor-piercing projectile cores using high-manganese, high-entropy alloy binders, such as Figure 4 As shown, it can be seen that Mn 33 –Ti0–Fe 15 –Co 15 –Ni 37 The grains are relatively small, with an average grain size of 355.98 μm.
[0046] Using a wire cutting machine, the composition of Mn 33 –Ti0–Fe 15 –Co 15 –Ni 37The high-toughness, low-thermal-conductivity armor-piercing projectile core was cut into 40mm×9mm×1.5mm tensile specimens using a high-manganese, high-entropy alloy binder. The surface and sides of the tensile specimens were smoothed with metallographic sandpaper, removing burrs, scratches, cracks, and other defects. Tensile tests were then performed using a universal testing machine, yielding the following results: Figure 2 The tensile curves shown indicate that the tensile strength is around 480 MPa and the elongation is around 52%.
[0047] The component was identified using a scanning electron microscope as Mn. 33 –Ti0–Fe 15 –Co 15 –Ni 37 Fracture surfaces of tensile specimens using high-manganese high-entropy alloy binders for high-toughness, low-thermal-conductivity armor-piercing projectile cores, such as... Figure 3 As shown, there are many dimples at the fracture surface, indicating that the material underwent significant plastic deformation before fracture, which is a ductile fracture. Combined with the tensile curve, this shows that the material has good elongation.
[0048] The composition was determined to be Mn using a thermal conductivity meter. 33 –Ti0–Fe 15 –Co 15 –Ni 37 The room temperature thermal conductivity of the high-toughness, low thermal conductivity armor-piercing projectile core using a high-manganese, high-entropy alloy binder is shown in Table 2. It can be seen that Mn... 33 –Ti0–Fe 15 –Co 15 –Ni 37 Its room temperature thermal conductivity is 9.90 W / (m·K).
[0049] Example 2 A method for preparing a high-toughness, low-thermal-conductivity armor-piercing projectile core high-manganese high-entropy alloy binder, wherein the high-toughness, low-thermal-conductivity armor-piercing projectile core high-manganese high-entropy alloy binder is composed of Mn 33 –Ti5–Fe 20 –Co 10 –Ni 32 This includes the following steps: Based on atomic ratio, the high-manganese high-entropy alloy binder used in the high-toughness, low-thermal-conductivity armor-piercing projectile core is prepared from iron, cobalt, nickel, manganese, and titanium, yielding Mn. 35-y -Ti x -(Fe–Co-Ni) 65-x+y , where x is 5 at.% and y is 2 at.%.
[0050] According to the atomic ratio Mn 33 –Ti5–Fe 20 –Co 10 –Ni 32Calculate the required mass of each element, weigh 53.585g of iron, 26.717g of cobalt, 85.104g of nickel, 88.567g of manganese, and 13.027g of titanium, and melt them using a non-consumable vacuum arc melting furnace. The melting conditions are: melting for 5 minutes at a stirring current of 15A and a melting current of 400A, followed by cooling, to prepare a rectangular high-manganese high-entropy alloy binder sample with a diameter of 70mm × 45mm × 10mm and a weight of 260g.
[0051] The component is Mn 33 –Ti5–Fe 20 –Co 10 –Ni 32 The high-toughness, low-thermal-conductivity armor-piercing projectile core uses a high-manganese, high-entropy alloy binder. The composition phase diagram was calculated using JMatPro, as follows: Figure 5 As shown, the phase diagram contains only the liquid phase and the FCC phase, and no other impurity phases such as intermetallic compounds.
[0052] The component was identified using a scanning electron microscope with an EBSD probe; 33 –Ti5–Fe 20 –Co 10 –Ni 32 EBSD of high-toughness, low-thermal-conductivity armor-piercing projectile cores using high-manganese, high-entropy alloy binders, such as Figure 8 As shown, it can be seen that Mn 33 –Ti5–Fe 20 –Co 10 –Ni 32 The grains are relatively small, with an average grain size of 308.74 μm.
[0053] Using a wire cutting machine, the composition of Mn 33 –Ti5–Fe 20 –Co 10 –Ni 32 The high-toughness, low-thermal-conductivity armor-piercing projectile core was cut into 40mm×9mm×1.5mm tensile specimens using a high-manganese, high-entropy alloy binder. The surface and sides of the tensile specimens were smoothed with metallographic sandpaper, removing burrs, scratches, cracks, and other defects. Tensile tests were then performed using a universal testing machine, yielding the following results: Figure 6 The tensile curves shown indicate that the tensile strength is around 580 MPa and the elongation is around 14%.
[0054] The component was identified using a scanning electron microscope as Mn. 33 –Ti5–Fe 20 –Co 10 –Ni 32 Fracture surfaces of tensile specimens using high-manganese high-entropy alloy binders for high-toughness, low-thermal-conductivity armor-piercing projectile cores, such as... Figure 7As shown, the presence of a dissociation surface at the fracture surface indicates that the material underwent brittle fracture during tension; at the same time, tear ridges can also be seen at the fracture surface, indicating that the material underwent shear deformation during tension.
[0055] The composition was determined to be Mn using a thermal conductivity meter. 33 –Ti5–Fe 20 –Co 10 –Ni 32 The room temperature thermal conductivity of the high-toughness, low thermal conductivity armor-piercing projectile core using a high-manganese, high-entropy alloy binder is shown in Table 2. It can be seen that Mn... 33 –Ti5–Fe 20 –Co 10 –Ni 32 Its room temperature thermal conductivity is 9.250 W / (m·K).
[0056] Example 3 A method for preparing a high-toughness, low-thermal-conductivity armor-piercing projectile core high-manganese high-entropy alloy binder, wherein the high-toughness, low-thermal-conductivity armor-piercing projectile core high-manganese high-entropy alloy binder is composed of Mn 35 –Ti8–Fe 10 –Co 20 –Ni 27 This includes the following steps: Based on atomic ratio, the high-manganese high-entropy alloy binder used in the high-toughness, low-thermal-conductivity armor-piercing projectile core is prepared from iron, cobalt, nickel, manganese, and titanium, yielding Mn. 35-y -Ti x -(Fe–Co-Ni) 65-x+y , where x is 8 at.% and y is 0 at.%.
[0057] According to the atomic ratio Mn 35 –Ti8–Fe 10 –Co 20 –Ni 27 Calculate the required mass of each element, weigh 26.185g of iron, 53.567g of cobalt, 72.306g of nickel, 93.732g of manganese, and 21.424g of titanium, and melt them using a non-consumable vacuum arc melting furnace. The melting conditions are: melting for 5 minutes at a stirring current of 15A and a melting current of 400A, followed by cooling, to prepare a rectangular high-manganese high-entropy alloy binder sample with a diameter of 70mm × 45mm × 10mm and a weight of 260g.
[0058] The component is Mn 35 –Ti8–Fe 10 –Co 20 –Ni 27 The high-toughness, low-thermal-conductivity armor-piercing projectile core uses a high-manganese, high-entropy alloy binder. The composition phase diagram was calculated using JMatPro, as follows: Figure 9 As shown, the phase diagram contains only the liquid phase and the FCC phase, and no other impurity phases such as intermetallic compounds.
[0059] The composition was determined to be Mn using a thermal conductivity meter. 35 –Ti8–Fe 10 –Co 20 –Ni 27 The room temperature thermal conductivity of the high-toughness, low thermal conductivity armor-piercing projectile core using a high-manganese, high-entropy alloy binder is shown in Table 2. It can be seen that Mn... 35 –Ti8–Fe 10 –Co 20 –Ni 27 Its room temperature thermal conductivity is 8.957 W / (m·K).
[0060] Comparative Example 1 Preparation method of conventional adhesives, the component of conventional adhesives is Fe 31 –Co6–Ni 63 This includes the following steps: According to the atomic ratio Fe 31 –Co6–Ni 63 Calculate the required mass of each element, weigh 80.524g of iron, 15.683g of cobalt, and 163.793g of nickel, and melt them using an MZ-1250 non-consumable vacuum arc melting furnace. The melting conditions are: melting for 5 minutes at a stirring current of 15A and a melting current of 400A, followed by cooling, to prepare a rectangular high-manganese high-entropy alloy binder sample with a diameter of 70mm × 45mm × 10mm and a weight of 260g.
[0061] The composition was determined to be Fe using a thermal conductivity meter. 31 –Co6–Ni 63 The room temperature thermal conductivity of the conventional binder samples is shown in Table 2. It can be seen that Fe 31 –Co6–Ni 63 The room temperature thermal conductivity is 43.258 W / (m·k), which is much higher than that of the high-toughness, low thermal conductivity armor-piercing projectile core high-manganese high-entropy alloy binder in Examples 1, 2 and 3.
[0062] Comparative Example 2 A method for preparing high-entropy alloy binders, wherein the high-entropy alloy binder is composed of Mn. 40 –Ti5–Fe 15 –Co 15 -Ni 25 As a comparative example, manganese content was increased to 30%–35%, with an atomic ratio of 40%, resulting in a final overall composition of Mn. 40 –Ti5–Fe 15 –Co15 -Ni 25 This includes the following steps: According to the atomic ratio Mn 40 –Ti5–Fe 15 –Co 15 -Ni 25 Calculate the required mass of each element, weigh 107.125g of manganese, 13.394g of titanium, 40.176g of iron, 41.268g of cobalt, and 66.958g of nickel, and melt them using a model MZ-1250 non-consumable vacuum arc melting furnace. The melting conditions are: melting for 5 minutes at a stirring current of 15A and a melting current of 400A, followed by cooling, to prepare a rectangular high-entropy alloy binder sample with a diameter of 70mm × 45mm × 10mm and a weight of 260g.
[0063] component Mn 40 –Ti5–Fe 15 –Co 15 -Ni 25 The composition phase diagram of the high-entropy alloy binder was obtained through JMatPro calculation, as follows: Figure 10 As shown, when the manganese content exceeds 30% to 35%, many intermetallic compounds appear.
[0064] Using a wire cutting machine, the component Mn 40 –Ti5–Fe 15 –Co 15 -Ni 25 The high-entropy alloy binder was cut into tensile specimens of 40mm × 9mm × 1.5mm. The surface and both sides of the tensile specimens were polished smooth with metallographic sandpaper, free of burrs, scratches, cracks, and other defects. Tensile tests were then performed using a universal testing machine to obtain the following results: Figure 11 As shown in the stretching curve, the elongation is around 2.5%, which is only 5% of that in Example 1.
[0065] In the composition of high-entropy alloy binders, manganese content is increased to more than 30% to 35%. Adding manganese at an atomic ratio of less than 30% will ultimately result in a room temperature thermal conductivity greater than 10 W / (m·K).
[0066] Comparative Example 3 A method for preparing high-entropy alloy binders, wherein the high-entropy alloy binder is composed of Mn. 35 –Ti 10 –Fe 15 –Co 15 -Ni 25 As a comparative example, the titanium element was added at an atomic ratio of 10%, exceeding the range of 0% to 8%, resulting in a final overall composition of Mn. 35 –Ti 10–Fe 15 –Co 15 -Ni 25 This includes the following steps: According to the atomic ratio Mn 35 –Ti 10 –Fe 10 –Co 10 -Ni 25 Calculate the required mass of each element, weigh 93.732g of manganese, 24.379g of titanium, 40.1745g of iron, 41.478g of cobalt, and 66.954g of nickel, and melt them using a model MZ-1250 non-consumable vacuum arc melting furnace. The melting conditions are: melting for 5 minutes at a stirring current of 15A and a melting current of 400A, followed by cooling, to prepare a rectangular high-entropy alloy binder sample with a diameter of 70mm × 45mm × 10mm and a weight of 260g.
[0067] component Mn 35 –Ti 10 –Fe 15 –Co 15 -Ni 25 The composition phase diagram of the high-entropy alloy binder was obtained through JMatPro calculation, as follows: Figure 12 As shown, when the titanium content exceeds the range of 0% to 8%, many intermetallic compounds appear.
[0068] Table 1 Physical properties of each element Table 2 Comparison of room temperature thermal conductivity of Examples 1-3 and Comparative Example 1 Those skilled in the art will readily understand that the above description is merely a preferred embodiment of the present invention and is not intended to limit the present invention. Any modifications, equivalent substitutions, and improvements made within the spirit and principles of the present invention should be included within the scope of protection of the present invention.
Claims
1. A high-manganese, high-entropy alloy binder for a high-toughness, low-thermal-conductivity armor-piercing projectile core, characterized in that, Based on atomic ratio, the composition of the high-manganese high-entropy alloy binder used in the core of a high-toughness, low-thermal-conductivity armor-piercing projectile is: Mn 35-y -Ti x -(Fe–Co-Ni) 65-x+y Where x is 0at.%~8at.%, y is 0at.%~5at.%, and x and y cannot be 0 at the same time.
2. The high-toughness, low-thermal-conductivity armor-piercing projectile core high-manganese high-entropy alloy binder according to claim 1, characterized in that, The elongation of the high-manganese high-entropy alloy binder for the core of a high-toughness, low-thermal-conductivity armor-piercing projectile is ≥10%.
3. The high-manganese, high-entropy alloy binder for the core of a high-toughness, low-thermal-conductivity armor-piercing projectile according to claim 1, characterized in that, The room temperature thermal conductivity of the high-manganese high-entropy alloy binder used in the core of the high-toughness, low-thermal-conductivity armor-piercing projectile is ≤10W / (m·k).
4. A method for preparing a high-manganese high-entropy alloy binder for a high-toughness, low-thermal-conductivity armor-piercing projectile core as described in any one of claims 1 to 3, characterized in that, Includes the following steps: According to the atomic ratio Mn 35-y -Ti x -(Fe–Co-Ni) 65-x+y Where x is 0 at.%~8 at.%, y is 0 at.%~5 at.%, calculate the required mass of each element, then weigh iron, cobalt, nickel, manganese and titanium, and smelt them using a non-consumable vacuum arc melting furnace to prepare a high-toughness, low thermal conductivity armor-piercing projectile core high-manganese high-entropy alloy binder.
5. The preparation method of the high-manganese high-entropy alloy binder for the high-toughness, low-thermal-conductivity armor-piercing projectile core according to claim 4, characterized in that, The melting conditions are as follows: melt for 5 minutes under stirring current of 10A~20A and melting current of 350A~500A, then cool, and repeat the melting process at least 8 times.
6. The preparation method of the high-manganese high-entropy alloy binder for the high-toughness, low-thermal-conductivity armor-piercing projectile core according to claim 4, characterized in that, Weigh out 1.02 to 1.04 times the calculated values of iron, cobalt, nickel, manganese, and titanium.
7. The application of the high-manganese high-entropy alloy binder for the high-toughness, low-thermal-conductivity armor-piercing projectile core as described in claim 1 in the preparation of the high-toughness, low-thermal-conductivity armor-piercing projectile core.
8. The application according to claim 7, characterized in that, The application method is as follows: tungsten is mixed with a high-toughness, low-thermal-conductivity armor-piercing projectile core using a high-manganese, high-entropy alloy binder, and then sintered in a hydrogen or vacuum atmosphere to obtain a high-toughness, low-thermal-conductivity armor-piercing projectile core. The mass ratio of tungsten to the high-manganese high-entropy alloy binder used in the high-toughness, low-thermal-conductivity armor-piercing projectile core is 88~97:3~12.
9. The application according to claim 8, characterized in that, The sintering conditions are: sintering at 1400℃~1500℃ for 0.5h.