A method of forming a ballistic panel module

Abstract

This invention provides a method for molding a bulletproof plate module, comprising the following steps: 3D printing a ceramic blank with interconnected pores; filling the cavities of the ceramic blank with metal powder, subjecting it to preliminary vibration and compaction until the metal powder completely fills all the voids in the porous ceramic structure, obtaining a ceramic-metal blank; determining a co-sintering temperature based on the thermal shrinkage curves of the ceramic and metal; placing the ceramic-metal blank in a sintering furnace, and performing ultrasonic vibration sintering treatment based on the co-sintering temperature to obtain the bulletproof plate module. The bulletproof plate module provided by this invention has the advantages of strong armor penetration resistance and resistance to multiple impacts, is simple to manufacture, and can be widely used in specific scenarios requiring protection, such as bulletproof vests and armored vehicles.

Description

Technical Field

[0001] This invention belongs to the field of bulletproof armor technology, and more specifically, relates to a method for molding a bulletproof plate module. Background Technology

[0002] With the development of modern military defense, ballistic plates, as the core of protective equipment, are constantly being upgraded and improved. While the earliest single-piece steel plates could stop bullets, they were too heavy and the impact transmission was lethal. Through continuous technological advancements, the concept of composite armor was introduced. Its core lies in a synergistic defense mechanism combining rigidity and flexibility. The front section uses ultra-high hardness and high strength ceramic panels (such as boron carbide and silicon carbide), which, upon contact with the projectile, blunt and shatter the high-speed projectile, consuming most of its kinetic energy and dispersing the impact force. The rear section is supported by a high-toughness fiber composite backing plate (such as ultra-high molecular weight polyethylene), responsible for catching all fragments and absorbing and dissipating the remaining energy through its own tensile and tearing plastic deformation, ultimately preventing penetration and achieving a protective effect. Besides these, composite ballistic plates also include ceramic / metal and metal / polymer types, but different manufacturing methods greatly affect the performance of the composite materials.

[0003] CN 115161508 A discloses a method for preparing a designable metal / ceramic dual-phase three-dimensional interconnected protective material and its product. The specific method includes: designing a three-dimensional ceramic skeleton structure, wherein the ceramic skeleton cell of the three-dimensional ceramic skeleton model includes a lattice structure and a minimal surface structure and its topology-optimized structure; preparing a ceramic slurry required for printing the ceramic skeleton; preparing the ceramic skeleton using 3D printing technology; and filling the space around the ceramic skeleton with molten metal through vacuum infiltration technology, wherein the vacuum infiltration temperature is 500-1800℃, to obtain a designable metal / ceramic dual-phase three-dimensional interconnected protective material.

[0004] Due to the significant differences in growth and melting temperatures, thermal expansion coefficients, and chemical compatibility between ceramics and metals, conventional methods such as co-sintering or vacuum infiltration can easily generate cavities, pores, cracks, and residual stress in ceramic / metal composites due to the extremely poor flowability of metal powders. This results in numerous pore defects and low strength in ceramic / metal composites. Summary of the Invention

[0005] The problem to be solved by the present invention is to provide a method for forming a bulletproof plate module. The bulletproof plate module is a ceramic interpenetrating composite metal, which combines the advantages of high strength of ceramic and plasticity of metal. It improves the fluidity of metal powder, promotes the compaction of metal powder in the ceramic blank with interconnected pore structure, improves the bonding between ceramic and metal interface, and reduces porosity and defects.

[0006] To solve the above problems, the present invention is achieved through the following technical solution: A method for molding a bulletproof plate module includes the following specific steps: (1) A ceramic blank with interconnected pore structure is formed by 3D printing, wherein the ceramic blank with interconnected pore structure includes a shell and a porous ceramic structure, the shell includes a plurality of closed surfaces and at least one opening, the plurality of closed surfaces form a cavity for accommodating the porous ceramic structure; (2) Fill the cavity of the ceramic blank with metal powder, and after preliminary vibration and compaction, until the metal powder completely fills all the voids of the porous ceramic structure to obtain a ceramic metal blank. The sintering temperature of the metal powder is T1, the sintering temperature of the ceramic blank is T2, and T2-T1≤800℃. (3) Determine the co-sintering temperature based on the thermal shrinkage curves of ceramics and metals; (4) The ceramic metal blank is placed in a sintering furnace and subjected to ultrasonic vibration sintering treatment based on the co-sintering temperature to obtain the bulletproof plate module.

[0007] Preferably, step (1) includes: A bulletproof plate model with a pre-defined interconnected hole structure is designed and generated based on a computer-aided system. Based on the bulletproof plate model, a ceramic blank with interconnected holes is formed by 3D printing. The ceramic blank with interconnected holes includes a shell and a porous ceramic structure, which are integrally formed.

[0008] Preferably, step (1) includes: A bulletproof plate model with a pre-defined interconnected hole structure is designed and generated based on a computer-aided system. Based on the bulletproof plate model, a shell is formed by 3D printing. The shell includes several closed surfaces and at least one opening. The several closed surfaces form a cavity for accommodating a porous ceramic structure. Based on the bulletproof plate model, a porous ceramic structure was formed by 3D printing. The porous ceramic structure is placed inside the cavity to obtain a ceramic blank with interconnected pores.

[0009] Preferably, the porous ceramic structure is placed inside the cavity, and the porous ceramic structure includes multiple pores that are interconnected to form a porous channel; The volume of the porous channel is V1, and the volume of the cavity is V2. V1 and V2 satisfy: V2 = (1.8~2.2)V1.

[0010] Preferably, the ceramic body comprises any one of single-phase ceramics and composite ceramics; the single-phase ceramic is any one of alumina, zirconium oxide, silicon nitride, silicon carbide, boron carbide, titanium diboride, aluminum oxynitride, aluminum magnesium spinel, and seron ceramics; the composite ceramic is any one of zirconium oxide toughened alumina, alumina composite silicon carbide, and alumina composite boron carbide. The metal powder is any one or more of tungsten and its alloys, titanium and its alloys, aluminum and its alloys, zirconium and its alloys, iron and its alloys, and magnesium and its alloys; The particle size range of the tungsten and its alloys is 1~12μm; The particle size range of the titanium and its alloys is 15~60μm; The particle size range of the aluminum and its alloys is 10~80μm; The zirconium and its alloys have a particle size range of 5~60 μm; The particle size range of the iron and its alloys is 8~65μm; The particle size range of the magnesium and its alloys is 3~80μm.

[0011] Preferably, in step (2), the volume ratio of ceramic to metal in the ceramic-metal blank is (1~4):(1~4). The initial vibration mode is any one or both of ultrasonic vibration and mechanical vibration; The frequency of the ultrasonic vibration is 20~40kHz, and the frequency of the mechanical vibration is 10~150Hz; The vibration lasts for 10 to 15 minutes.

[0012] Preferably, in step (3), determining the co-sintering temperature based on the thermal shrinkage curves of the ceramic and the metal includes: The thermal shrinkage curves of ceramics and metals were obtained by thermomechanical analysis. Based on the thermal shrinkage curve of the ceramic, the melting growth temperature range of the ceramic is determined. The melting growth temperature range includes Ts and Te, where Ts is the shrinkage start point of the thermal shrinkage curve of the ceramic, and Te is the shrinkage end point of the thermal shrinkage curve of the ceramic. Based on the thermal shrinkage curves of the ceramic and the metal, within the melting growth temperature range of the ceramic, the temperature corresponding to the absolute value of the difference in shrinkage rates between the metal and the ceramic being ≤20% is taken as the co-sintering temperature.

[0013] Preferably, in step (4), the ceramic metal blank is placed in a sintering furnace and subjected to ultrasonic vibration sintering treatment based on the co-sintering temperature to obtain a bulletproof plate module comprising: The ceramic-metal blank is placed in a sintering furnace; The temperature is raised to the co-sintering temperature at a preset heating rate, and ultrasonic vibration is performed in multiple heating point intervals for a preset constant temperature duration. The bulletproof plate module was obtained by cooling it to room temperature in the furnace.

[0014] Preferably, the process of heating to the co-sintering temperature at a preset heating rate, performing ultrasonic vibration in multiple heating point intervals, and maintaining the temperature for a preset duration includes: The temperature is increased to 150℃~200℃ at a rate of 2℃ / min~4℃ / min, and held for 60~90min. At the same time, ultrasonic vibration with a frequency ≥20kHz is applied for 20min~40min. The temperature is increased to 300℃~400℃ at a rate of 1℃ / min~3℃ / min, and held for 60~90min. At the same time, ultrasonic vibration with a frequency ≥20kHz is applied for 20min~40min. The temperature is increased to 500℃~600℃ at a rate of 1℃ / min~3℃ / min, and held for 30~60min. At the same time, ultrasonic vibration with a frequency ≥20kHz is applied for 20min~40min. The temperature is increased to 1000℃~1100℃ at a rate of 4℃ / min~6℃ / min and held for 60~90min, while ultrasonic vibration with a frequency ≥20kHz is applied for 20min~40min. Heat to the co-sintering temperature at a rate of 5℃ / min to 8℃ / min, and hold at the co-sintering temperature for 160-240 minutes.

[0015] Accordingly, the present invention provides a bulletproof plate module, which is manufactured by the molding method of the bulletproof plate module.

[0016] Compared with the prior art, the present invention has the following beneficial effects: (1) This invention uses 3D printing to form a ceramic blank with interconnected pores, and fills the cavity of the ceramic blank with metal powder. The co-sintering temperature is determined according to the thermal shrinkage curves of the ceramic and metal. The ceramic-metal blank is placed in a sintering furnace, and ultrasonic vibration sintering is performed based on the co-sintering temperature. The bulletproof plate module obtained by this invention can achieve high hardness and strong armor penetration resistance through the ceramic phase and plastic deformation capability through the metal phase. By using the interpenetrating composite molding of the ceramic and metal phases, the performance of the ceramic and metal phases is complementary. Moreover, the oxide film on the surface of the metal and ceramic particles can be broken during ultrasonic vibration sintering, promoting mutual diffusion and interlocking at the interface, forming a three-dimensional network of interconnected microstructures, significantly improving stress transmission efficiency, and avoiding the interface peeling failure common in traditional composite bulletproof plate materials.

[0017] (2) The bulletproof plate module made by the molding method of the bulletproof plate module provided by the present invention has the advantages of high hardness of ceramic and plasticity of metal. It has the advantages of strong resistance to armor penetration and resistance to multiple hits. The process is simple and can be widely used in specific scenarios that require protection, such as bulletproof vests and armored vehicles. Attached Figure Description

[0018] Figure 1 This is a schematic flowchart of a method for molding a bulletproof plate module according to the present invention; Figure 2 Schematic diagrams of different structures of porous ceramic structures; Figure 3 This is the model after the square hole structure is closed; Figure 4 This is a schematic diagram of the structure of a ceramic blank; Figure 5 This is a schematic diagram of the structure of a ceramic-metal preform; Figure 6 Thermal shrinkage curves for ceramics and metals; Figure 7 This is a schematic diagram of the structure sintered by ultrasonic vibration. Figure 8 This is a microstructure diagram of the ceramic and metal combination in Example 1; Figure 9 This is a microstructure diagram of the ceramic and metal combination in Example 2; Figure 10 This is a microstructure diagram of the ceramic and metal combination in Comparative Example 1. Figure 11 This is a microstructure diagram of the ceramic and metal combination in Comparative Example 2. Detailed Implementation

[0019] To make the objectives, technical solutions, and advantages clearer, the present invention will be further described in detail below with reference to the accompanying drawings and specific embodiments.

[0020] Unless otherwise defined, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention pertains. The terminology used herein in the description of the invention is for the purpose of describing particular embodiments only and is not intended to be limiting of the invention.

[0021] In this invention, numerical ranges are involved. Unless otherwise specified, the numerical ranges are considered continuous and include the minimum and maximum values ​​of the range, as well as every value between the minimum and maximum values. Furthermore, when the range refers to integers, it includes every integer between the minimum and maximum values ​​of the range. Additionally, when multiple ranges are provided to describe features or characteristics, the ranges may be merged. In other words, unless otherwise specified, all ranges disclosed herein should be understood to include any and all subranges to which they are included.

[0022] In this invention, the technical features described in an open-ended manner include both closed-ended technical solutions composed of the listed features and open-ended technical solutions that include the listed features.

[0023] like Figure 1 As shown, the present invention provides a method for molding a bulletproof plate module, comprising the following specific steps: S1. A ceramic blank with interconnected pores is formed by 3D printing, wherein the ceramic blank with interconnected pores includes a shell and a porous ceramic structure, the shell includes a plurality of closed surfaces and at least one opening, the plurality of closed surfaces forming a cavity for accommodating the porous ceramic structure; In some embodiments, step S1 includes: S101. Based on a computer-aided system, design and generate a bulletproof plate model with a pre-defined interconnected hole structure; S102. Based on the bulletproof plate model, a ceramic blank with interconnected holes is formed by 3D printing. The ceramic blank with interconnected holes includes a shell and a porous ceramic structure, which are integrally formed.

[0024] By designing a bulletproof plate model in one piece, a ceramic blank with an interconnected hole structure is formed by single continuous 3D printing. This eliminates the connection interface between traditional multi-part components, avoids stress concentration and fatigue fracture common at connection points, and ensures the consistency of the ceramic blank.

[0025] Specifically, such as Figure 2As shown, the porous ceramic structure can be any one of a simple pore structure, a lattice structure, and a cubic periodic minimum surface structure. The simple pore structure includes a square pore structure, a spherical pore structure, or a cylindrical pore structure. The lattice structure is a body-centered cubic, face-centered cubic, octet, Kelvin, or fluorite structure. The cubic periodic minimum surface structure is a Primitive, Gyroid, Diamond, Split P, Neovius, or Lidinoid surface structure.

[0026] Taking a square hole structure as an example, such as Figure 3 As shown, the model after its five faces are closed is as follows: Figure 3 As shown in the left figure, the cross-section of the closed model is as follows: Figure 3 As shown in the right figure, interconnected square hole structures can be observed in the figure.

[0027] Preferably, the total volume of the pore structure in the porous ceramic structure is V1, and the total volume of the porous ceramic structure is V2. V1 and V2 satisfy: V2 = (1.8~2.2)V1.

[0028] Because the porous ceramic structure is made of ceramic, and the pores within the porous ceramic structure are filled with metal powder, a specific volume ratio of ceramic and metal composites is used to achieve interpenetrating molding of ceramic and metal, improving the overall ballistic protection performance of the formed bulletproof plate. When V2 is greater than 2.2*V1, the amount of metal powder is too small. As the main energy-absorbing phase, the metal cannot effectively restrain the brittle fracture of the ceramic. When impacted by a bullet, the ceramic is prone to large-scale fragmentation, losing its structural integrity. This prevents the metal from fully absorbing residual energy. Moreover, the metal cannot form a continuous network, resulting in insufficient mechanical interlocking and metallurgical bonding with the ceramic, and the interface is prone to detachment. When V2 is less than 1.8*V1, the amount of metal powder is too large, significantly increasing the overall mass of the bulletproof plate, which is not conducive to the lightweighting of the bulletproof module. In addition, the projectile may not fully break apart before entering the metal layer. Although the metal can absorb energy through plastic deformation, when impacted by a bullet, excessive deformation of the metal may compress the internal space of the bulletproof plate, causing secondary injury to personnel or equipment.

[0029] In other embodiments, step S1 includes: S110. Based on a computer-aided system, design and generate a bulletproof plate model with a pre-defined interconnected hole structure; S120. Based on the bulletproof plate model, a shell is formed by 3D printing, the shell including a plurality of closed surfaces and at least one opening, the plurality of closed surfaces forming a cavity for accommodating a porous ceramic structure; S130. Based on the bulletproof plate model, a porous ceramic structure is formed by 3D printing; S140. The porous ceramic structure is placed inside the cavity to obtain a ceramic blank with interconnected pores.

[0030] The porous ceramic structure is first printed in the optimal orientation and then placed in a shell cavity that can accommodate the porous ceramic structure. This method does not require consideration of complex internal supports during the design process and avoids the physical limitation of having to print layer by layer from the bottom.

[0031] Preferably, such as Figure 4 As shown, the porous ceramic structure 2 is placed inside the cavity of the shell 3. The porous ceramic structure 2 includes multiple pores, which are interconnected to form porous channels. The smallest unit pore 1 can be a simple pore type, such as a square pore structure, a spherical pore structure, or a cylindrical pore structure; it can be a lattice structure, such as a face-centered cubic structure, a body-centered cubic structure, an octet structure, a Kelvin structure, or a fluorite structure; or it can be a cubic periodic minimum surface structure, such as a Primitive surface, a Gyroid surface, a Diamond surface, a Split P surface, a Neovius surface, or a Lidinoid surface.

[0032] Furthermore, the volume of the porous channel is V1, and the volume of the cavity is V2, where V1 and V2 satisfy: V2 = (1.8~2.2)V1.

[0033] Because the porous ceramic structure is made of ceramic, and the interconnected pores form porous channels filled with metal powder, a specific volume ratio of ceramic and metal composites is used to achieve interpenetrating molding of ceramic and metal, improving the overall ballistic protection performance of the formed bulletproof plate. When V2 is greater than 2.2*V1, the amount of metal powder is too small. As the main energy-absorbing phase, the metal cannot effectively restrain the brittle fracture of the ceramic. When impacted by a bullet, the ceramic is prone to large-scale fragmentation, losing its structural integrity. This prevents the metal from fully absorbing residual energy. Moreover, the metal cannot form a continuous network, resulting in insufficient mechanical bonding and metallurgical adhesion with the ceramic, and the interface is prone to detachment. When V2 is less than 1.8*V1, the amount of metal powder is too large, significantly increasing the overall mass of the bulletproof plate, which is not conducive to the lightweighting of the bulletproof module. In addition, the projectile may not fully break apart before entering the metal layer. Although the metal can absorb energy through plastic deformation, excessive deformation of the metal after impact may compress the internal space of the bulletproof plate, causing secondary injury to personnel or equipment.

[0034] It should be noted that, since the porous ceramic structure is placed inside the cavity, the total volume of the porous ceramic structure can be considered equivalent to the volume of the cavity.

[0035] In some embodiments, the 3D printing technology is any one of photopolymerization molding, material extrusion molding, binder jetting molding, and selective laser sintering molding. Among them, photopolymerization molding is suitable for almost all ceramics that can be made into uniform suspension slurries, such as common alumina, zirconia, and zirconia-toughened alumina composite ceramics. Specifically, ceramic powder, photosensitive resin, and photoinitiator are mixed to form a high-solids-content, low-viscosity ceramic slurry, which is then used for printing.

[0036] Material extrusion molding involves mixing ceramic powder with water-based, gel, thermoplastic, or other binders to create a "ceramic ink" with shear-thinning properties. This ink is then extruded through a needle and, based on a bulletproof plate model design, is printed using self-supporting or gelation methods.

[0037] Adhesive spray molding involves laying a layer of ceramic powder on a powder bed, then selectively spraying liquid adhesive through a nozzle to bond the ceramic powder together. This powder-laying and spraying process is repeated to print the final shape.

[0038] Selective laser sintering uses a laser to sinter powders together. Specifically, a low-melting-point polymer binder is coated on the outside of ceramic powder, and the binder is melted by a laser to form the desired shape.

[0039] In some embodiments, the ceramic body includes any one of single-phase ceramics and composite ceramics; the single-phase ceramic is any one of alumina, zirconium oxide, silicon nitride, silicon carbide, boron carbide, titanium diboride, aluminum oxynitride, aluminum magnesium spinel, and seron ceramics; the composite ceramic is any one of zirconium oxide toughened alumina, alumina composite silicon carbide, and alumina composite boron carbide.

[0040] Typically, high-strength and high-hardness ceramics are suitable for use as the surface layer of bulletproof plates. When a high-speed projectile impacts the ceramic surface, its kinetic energy is instantly converted into destructive energy against the projectile. The high strength and hardness of the ceramic cause the projectile to blunt or fracture. While stopping the projectile, the ceramic itself forms a fragmentation cone at the point of impact, where the ceramic fragments into fine particles. Furthermore, the fragmentation cone disperses the remaining impact force of the projectile to nearby areas, transferring it to nearby ductile metals. Through deformation and tearing, the remaining energy is further absorbed and dissipated, ultimately trapping all the ceramic and projectile fragments, achieving a protective effect. Therefore, both single-phase and multi-phase ceramics with high strength and hardness can be used as raw materials for ceramic blanks.

[0041] S2. Fill the cavity of the ceramic blank with metal powder, and after preliminary vibration and compaction, until the metal powder completely fills all the voids of the porous ceramic structure to obtain a ceramic metal blank. The sintering temperature of the metal powder is T1, the sintering temperature of the ceramic blank is T2, and T2-T1≤800℃. Preferably, the volume ratio of ceramic to metal in the ceramic-metal preform is (1~4):(1~4). The initial vibration mode is any one or both of ultrasonic vibration and mechanical vibration; The frequency of the ultrasonic vibration is 20~40kHz, and the frequency of the mechanical vibration is 10~150Hz; The vibration lasts for 10 to 15 minutes.

[0042] In some embodiments, such as Figure 5 As shown, a ceramic blank with interconnected pores is completely immersed in metal powder. The good fluidity of the metal powder allows it to quickly fill the porous ceramic structure. After initial vibration and compaction, the metal powder completely fills all the pores of the porous ceramic structure, resulting in a ceramic metal blank 4. This method can significantly improve the success rate of metal powder impregnation and the uniformity of filling in the pores.

[0043] Preferably, the initial vibration can be ultrasonic vibration or mechanical vibration alone, or a combination of ultrasonic vibration and mechanical vibration. Mechanical vibration can rapidly fill the porous ceramic structure with metal powder over a large area, while the acoustic cavitation and acoustic flow effects generated by ultrasonic vibration can further compact the dense metal powder, allowing it to enter the finest pores and ensuring that the metal powder completely fills all gaps, so that the ceramic and metal are in complete contact, laying the foundation for the formation of a beneficial interface in subsequent sintering.

[0044] Furthermore, after initial vibration and compaction, the metal powder completely fills all the voids. In the subsequent sintering process, the metal powder only needs to penetrate the tiny gaps between the powder particles. The required flow path is shorter and the resistance is lower. Therefore, complete impregnation can be achieved under lower pressure and closer to the melting temperature, which simplifies the process and reduces costs and the risk of thermal damage.

[0045] It should be noted that the volume ratio of ceramic to metal in the obtained ceramic-metal blank is (1~4):(1~4). Within the above range, a three-dimensional interpenetrating network structure composite material of ceramic and metal can be obtained through subsequent sintering process. This material has both strength and hardness close to that of ceramic and toughness close to that of metal. It is both strong and tough. When the bulletproof plate module is impacted by a bullet, the ceramic skeleton breaks and consumes energy, while the metal network absorbs the remaining energy through plastic deformation and tearing, and "sticks" the ceramic fragments, avoiding the problem of "local failure leading to overall failure".

[0046] Preferably, the metal powder is any one or more of tungsten and its alloys, titanium and its alloys, aluminum and its alloys, zirconium and its alloys, iron and its alloys, and magnesium and its alloys; Tungsten, in particular, possesses extremely high density and hardness, with a density of approximately 19.25 g / cm³. 3 With a hardness of 300~450HV, tungsten alloys also possess this advantage, including YG6, YG8, YG15, YG20, tungsten-nickel-iron, and tungsten-nickel-copper alloys. Using tungsten and its alloys in bulletproof plate modules can effectively dissipate the energy generated by projectile impact through their significant mass effect and plasticity, achieving a protective effect. Furthermore, the particle size range of tungsten and its alloys is 1~12μm. Such a small particle size facilitates filling the finest and most tortuous channels of the ceramic blank under vibration and compaction, achieving seamless filling. The small particle size also leads to a higher packing density, meaning that fewer residual voids need to be filled in subsequent sintering steps, making it easier to obtain a completely dense ceramic interpenetrating composite metal material and reducing internal defects.

[0047] Titanium and its alloys provide high resistance to plastic deformation and dynamic strength to support the ceramic structure after a projectile impact. These alloys include Ti-6Al-4V, Ti-4Al-2.5V-1.5Fe, TC21, and VT23, with a grain size range of 15–60 μm. Under high-speed projectile impact, they induce localized, intense shear deformation and temperature rise to dissipate energy, thus contributing to the dissipation of significant impact energy. While maintaining high strength, titanium and its alloys possess better fracture toughness and crack propagation resistance. This means that after the first or subsequent impacts, the titanium alloy network can better maintain its integrity, continuing to provide effective support for the ceramic skeleton and preventing overall back-side collapse, thereby improving multi-projectile protection capabilities.

[0048] Aluminum and its alloys can undergo significant plastic flow and tearing under the impact of a projectile, absorbing a large amount of kinetic energy through plasticity. These alloys include the 5000 series, 7000 series, and 2000 series, with a grain size range of 10~80μm. Compared to brittle metals, aluminum and its alloys can still maintain good integrity in the remaining area after being hit by a projectile once.

[0049] Zirconium and its alloys are suitable for special scenarios in ballistic protection applications, including Zr-Ti-Cu-Ni-Be, UNS R60702, and UNSR60705, with a grain size range of 5~60μm. These are used in special armor or protective structures in nuclear environments, providing effective protection against bullets and fragments while minimizing the impact on reactor neutron shielding, without significantly interfering with nuclear reactions or increasing the difficulty of radiation shielding. Furthermore, zirconium alloys possess a good balance of strength, toughness, and plasticity. In a ceramic interpenetrating composite metal three-dimensional network structure, they can effectively absorb impact energy, support the ceramic layer, and maintain performance stability under dynamic loads, which is beneficial for resisting ballistic impacts.

[0050] Iron and its alloys are low-cost materials, including 4100 series martensitic steel, 4300 series martensitic steel, silicon-manganese steel, and chromium-manganese steel, with a grain size range of 8~65μm. As part of ballistic armor modules, they can provide high strength, high toughness, and good impact load resistance. Among them, 4100 series martensitic steel is suitable for high-performance general-purpose ballistic armor, helicopter armor, and key parts of medium-sized vehicles; 4300 series martensitic steel is suitable for top-level composite armor against armor-piercing projectiles and main armor of special vehicles; silicon-manganese steel is suitable for ballistic structures with strict limitations on backplate indentation, such as vehicle interior ballistic armor; and chromium-manganese steel is suitable for large-scale deployment of economical composite armor and fortification protection modules.

[0051] Magnesium and its alloys possess excellent specific strength and specific stiffness. The AZ, ZK, and WE series, with a grain size range of 3–80 μm, enable the creation of the lightest armor systems for the same protection level. This significantly reduces weight, providing effective structural support and energy absorption with minimal weight. When a ballistic plate module is impacted by a projectile, magnesium alloys not only absorb energy through plastic deformation but also dissipate a large amount of vibrational energy through friction within their internal microstructure. This helps reduce secondary vibrations and stress wave reflections within the armor system, potentially improving resistance to multiple impacts.

[0052] It should be noted that materials can be flexibly selected to balance overall performance and the needs of different application scenarios.

[0053] In some preferred embodiments, the metal powder selected in this invention needs to match the sintering temperature of the ceramic to meet the requirements of co-sintering compatibility and performance complementarity. Specifically, the sintering temperature of the metal powder is T1, and the sintering temperature of the ceramic body is T2, where T2-T1≤800℃.

[0054] When the difference between the sintering temperature of the metal powder and the sintering temperature of the ceramic body is within 800℃, a good metallurgical bonding interface can be achieved during co-sintering. Cracks are less likely to form at the interface, and the metal can fully penetrate into the pores of the ceramic body, forming a three-dimensional continuous interpenetrating structure, thus preventing delamination or detachment at the interface. For example, for alumina, the metal powder used is titanium and its alloys, nickel-based and cobalt-based superalloys; for silicon carbide and boron carbide, the metal powder used is mainly zirconium alloy or pure titanium.

[0055] S3. Determine the co-sintering temperature based on the thermal shrinkage curves of ceramics and metals; Preferably, determining the co-sintering temperature based on the thermal shrinkage curves of ceramics and metals includes the following steps: S301. The thermal shrinkage curves of ceramics and metals were obtained by testing with a thermomechanical analyzer; S302. Based on the thermal shrinkage curve of the ceramic, determine the melting growth temperature range of the ceramic, wherein the melting growth temperature range includes Ts and Te, wherein Ts is the shrinkage start point of the thermal shrinkage curve of the ceramic, and Te is the shrinkage end point of the thermal shrinkage curve of the ceramic; S303. Based on the thermal shrinkage curves of the ceramic and the metal, within the melting growth temperature range of the ceramic, the temperature corresponding to the absolute value of the difference in shrinkage rates between the metal and the ceramic being ≤20% is taken as the co-sintering temperature.

[0056] Thermomechanical analyzers can continuously and accurately measure the rate of dimensional change of ceramics and metals from room temperature to the sintering termination temperature. Due to the significant difference in the coefficients of thermal expansion between ceramics and metals, ceramics shrink slowly through solid-phase diffusion, while metals may undergo rapid shrinkage during liquid-phase sintering. During the sintering stage, if the shrinkage initiation temperature, maximum shrinkage rate temperature, and shrinkage amount of the ceramic and metal are highly synchronized, they can achieve good co-firing without delamination or deformation. However, if the metal shrinks before the ceramic, it will generate compressive stress on the unshrinked ceramic, potentially causing warping; conversely, it will generate tensile stress, which may lead to cracking.

[0057] The melting growth temperature of ceramics refers to the temperature range in which the solid and liquid phases coexist. Within this temperature range, ceramics shrink rapidly and have a high degree of densification, enabling them to complete sintering in a relatively short time. During this process, the ceramics actively and forcefully shrink and compress the metal powder encased within them, greatly promoting the densification of the metal particles and their bonding.

[0058] In some embodiments, such as Figure 6As shown, the thermal shrinkage curves of ceramics and metals are obtained by thermomechanical analysis. Based on the thermal shrinkage curve of the ceramics, the melting growth temperature range (Ts, Te) of the ceramics is determined. Within this temperature range, the temperature range corresponding to the absolute value of the difference between the shrinkage rates of the metal and the ceramics being ≤20% is (Ts1, Te). Therefore, the co-sintering temperature of the ceramics and metals can be determined as (Ts1, Te).

[0059] In some embodiments, since the ceramic-metal blank is completely immersed in the metal powder, the metal powder can be completely filled by simultaneously applied ultrasonic vibration during the co-sintering process, thereby compensating for the shrinkage difference of less than 20% between the metal and the ceramic, making the ceramic and the metal nearly completely dense without gaps, and obtaining a crack-free, regularly shaped, dense ceramic interpenetrating composite metal bulletproof plate module.

[0060] S4. The ceramic metal blank is placed in a sintering furnace and subjected to ultrasonic vibration sintering treatment based on the co-sintering temperature to obtain the bulletproof plate module.

[0061] Preferably, the ceramic-metal blank is placed in a sintering furnace and subjected to ultrasonic vibration sintering treatment based on the co-sintering temperature to obtain the bulletproof plate module, including the following steps: S401. Place the ceramic-metal blank in a sintering furnace; S402. Heat to the co-sintering temperature at a preset heating rate, perform ultrasonic vibration in multiple heating point intervals, and maintain the temperature for a preset duration. Preferably, the process of heating to the co-sintering temperature at a preset heating rate, performing ultrasonic vibration in multiple heating point intervals, and maintaining the temperature for a preset duration includes: The temperature is increased to 150℃~200℃ at a rate of 2℃ / min~4℃ / min, and held for 60~90min. At the same time, ultrasonic vibration with a frequency ≥20kHz is applied for 20min~40min. The temperature is increased to 300℃~400℃ at a rate of 1℃ / min~3℃ / min, and held for 60~90min. At the same time, ultrasonic vibration with a frequency ≥20kHz is applied for 20min~40min. The temperature is increased to 500℃~600℃ at a rate of 1℃ / min~3℃ / min, and held for 30~60min. At the same time, ultrasonic vibration with a frequency ≥20kHz is applied for 20min~40min. The temperature is increased to 1000℃~1100℃ at a rate of 4℃ / min~6℃ / min and held for 60~90min, while ultrasonic vibration with a frequency ≥20kHz is applied for 20min~40min. Heat to the co-sintering temperature at a rate of 5℃ / min to 8℃ / min, and hold at the co-sintering temperature for 160 to 240 minutes.

[0062] During the co-sintering process, a staged heating method is adopted. Within the heating range of room temperature to 600℃, the metal is far from reaching the melting and infiltration temperature. In this range, the main process is staged degreasing and binder removal, and firing is carried out at a slower heating rate. This allows the different components of the binder, plasticizer, and other organic materials in the ceramic body to be removed sequentially in their respective temperature ranges without damaging the ceramic powder skeleton. At the same time, ultrasonic vibration is applied, which can promote the filling of small metal powder with an average particle size of less than 10μm into the small gaps in the ceramic body, laying the foundation for the smooth infiltration of the metal and the firm bonding of the interface.

[0063] Within the heating range above 600℃, the porous ceramic skeleton is essentially free of organic residues and defects. As it gradually sintersulates and densifies, it is fired at a relatively rapid heating rate, allowing the metal to melt and infiltrate. Simultaneously, ultrasonic vibration is applied, and the acoustic cavitation and acoustic flow effects generated by the ultrasound can promote the melting of the metal powder. Furthermore, as the temperature rises, the metal powder enters a semi-solid state, and the ultrasound can alter the thixotropic properties of the semi-solid metal powder, significantly increasing its fluidity. This facilitates the realization of an interpenetrating structure between the ceramic skeleton and the metal network, achieving a high-strength interfacial bond and enhancing the overall protective performance of the bulletproof plate.

[0064] If the temperature is increased to the co-sintering temperature in one step, the binder in the ceramic body will decompose and vaporize rapidly at high temperatures, generating a large amount of gas. This gas expands rapidly inside the ceramic body and cannot escape through the tiny pores, creating enormous internal pressure. When this internal pressure exceeds the strength of the ceramic body itself, various defects such as cracking, blistering, and deformation will occur. Most of these defects cannot be repaired or eliminated during subsequent sintering and metal infiltration processes, ultimately leading to cracking or collapse of the overall structure and a decline in overall performance.

[0065] In some embodiments, such as Figure 7 As shown, the ceramic metal blank 4, which is immersed in metal powder, is placed in a sintering furnace 5. The sintering furnace 5 is equipped with a vibration device, and the ceramic metal blank 4 in the sintering furnace is subjected to ultrasonic vibration sintering treatment by the ultrasonic waves 6 generated by the vibration device.

[0066] Preferably, the vibration device of the sintering furnace includes either an external or an internal type. The external type refers to placing the vibration device outside the sintering furnace and transmitting the vibration to the high-temperature zone inside the sintering furnace through a transmission component, which can achieve high-power, large-amplitude vibration and is suitable for large-scale industrial production. The internal type refers to installing the vibration device directly in the high-temperature zone inside the sintering furnace, which has a short vibration transmission path, high efficiency, and low energy loss, and can achieve more precise and rapid vibration response and control.

[0067] Specifically, during the ultrasonic vibration sintering process, the frequency of ultrasonic vibration is set to ≥20kHz. Within this range, high-frequency ultrasonic vibration can effectively remove the finest pores inside the ceramic metal blank. These pores are the source of crack initiation and propagation when the bulletproof plate is impacted. Eliminating them can significantly improve the dynamic strength of the bulletproof plate. Moreover, in the early stage of sintering, the ultrasonic acoustic flow effect can make the metal powder particles achieve the most compact packing, laying the foundation for the formation of a uniform ceramic interpenetrating composite metal, resulting in a bulletproof plate with very few internal defects.

[0068] It should be noted that within the above range, ultrasonic energy is highly concentrated at the ceramic-metal interface, which can break the oxide film on the surface of the metal and ceramic particles. Ultrasonic vibration greatly enhances the diffusion ability of atoms, allowing the metal phase to undergo moderate and controllable interfacial diffusion or reaction with the ceramic phase at temperatures far below normal, forming a strong and tough metallurgical bonding layer, rather than simple mechanical interlocking. The resulting strong and tough interface can ensure that stress is effectively transferred from the broken ceramic to the tough metal, achieving synergistic energy dissipation and preventing overall collapse caused by debonding of the ceramic-metal interface.

[0069] In addition, the vibration time in each heating interval is 20~40 minutes. This is because the plasticity, diffusion coefficient and liquid phase content of the material are different at different temperatures. Furthermore, each heating interval contains key temperature points, such as the temperature at which the metal begins to flow plastically, the temperature at which the ceramic solid phase softens, and the temperature at which the ceramic liquid phase appears. Continuous ultrasonic treatment in each heating interval can remove the main defects generated in that stage and create the best conditions for densification in the next stage, ultimately resulting in a bulletproof plate module with the fewest defects.

[0070] S403. Cool to room temperature in the furnace to obtain the bulletproof plate module.

[0071] In summary, this invention provides a bulletproof plate module that combines the advantages of high hardness of ceramics and plasticity of metals. Utilizing an ultrasonic vibration sintering process, the oxide film on the surfaces of both metal and ceramic particles is broken during sintering, promoting mutual diffusion and interlocking at the interface. This forms a three-dimensional, interconnected microstructure, significantly improving stress transfer efficiency and avoiding the interface delamination failure common in traditional composite bulletproof plate materials. It also avoids the problem of "local failure leading to overall failure" in traditional bulletproof plates. This bulletproof plate module offers strong resistance to armor penetration and repeated impacts, is simple to manufacture, and can be widely applied in specific scenarios requiring protection, such as bulletproof vests and armored vehicles.

[0072] The following description, in conjunction with specific embodiments, further elaborates on this point. Example 1 This embodiment 1 provides a method for molding a bulletproof plate module, using alumina as the ceramic raw material and titanium alloy as the metal raw material, including the following specific steps: (1) Using alumina as ceramic raw material, a ceramic blank with interconnected pore structure is formed by 3D printing, wherein the ceramic blank with interconnected pore structure includes a shell and a porous ceramic structure, the shell includes several closed surfaces and at least one opening, and the several closed surfaces form a cavity for accommodating the porous ceramic structure. S110. Based on a computer-aided system, design and generate a bulletproof plate model with a pre-defined interconnected hole structure; S120. Based on the bulletproof plate model, a shell is formed by 3D printing, the shell including a plurality of closed surfaces and at least one opening, the plurality of closed surfaces forming a cavity for accommodating a porous ceramic structure; S130. Based on the bulletproof plate model, a porous ceramic structure is formed by 3D printing; S140. The porous ceramic structure is placed inside the cavity to obtain a ceramic blank with interconnected pores.

[0073] A porous ceramic structure is placed within the cavity. The porous ceramic structure comprises multiple pores that are interconnected to form a porous channel. Specifically, the volume of the porous channel is 3100 mm². 3 The volume of the cavity is 6125 mm. 3 .

[0074] (2) The ceramic green body with interconnected pores is completely immersed in titanium alloy metal powder. The metal powder is rapidly filled into the porous ceramic structure. After preliminary vibration and compaction, the frequency of the preliminary vibration is 50 Hz and the vibration time is 10 min until the metal powder completely fills all the pores of the porous ceramic structure to obtain a ceramic metal green body. The sintering temperature of the titanium alloy metal powder is 1350℃, the sintering temperature of the alumina ceramic green body is 1650℃, and the volume ratio of ceramic to metal in the ceramic metal green body is 1:1.

[0075] (3) The thermal shrinkage curves of the ceramic and the metal are determined by a thermomechanical analyzer. The growth melting temperature range of the alumina ceramic is 1600~1700℃. Within this temperature range, the temperature corresponding to the absolute value of the difference in shrinkage rate between the titanium alloy metal and the alumina ceramic is ≤20% is taken as the co-sintering temperature. The co-sintering temperature is selected as 1650℃. At this temperature, the alumina ceramic will shrink, but the volume of the titanium alloy is in a steady state, and its shrinkage size will be smaller than that of the ceramic.

[0076] (4) The ceramic metal blank immersed in metal powder is placed in a sintering furnace and heated to 200°C at a rate of 4°C / min, held for 90 min, and ultrasonic vibration at a frequency of 20 kHz is applied for 40 min; heated to 400°C at a rate of 3°C / min, held for 90 min, and ultrasonic vibration at a frequency of 20 kHz is applied for 40 min; heated to 600°C at a rate of 1°C / min, held for 60 min, and ultrasonic vibration at a frequency of 20 kHz is applied for 20 min; heated to 1100°C at a rate of 6°C / min, held for 60 min, and ultrasonic vibration at a frequency of 20 kHz is applied for 40 min; heated to the co-sintering temperature at a rate of 8°C / min, held at the co-sintering temperature for 240 min, and cooled with the furnace. After cooling, the bulletproof plate module is obtained.

[0077] The bulletproof plate module obtained in Example 1 has the following microstructure: Figure 8 As shown, by Figure 8 It can be seen that the ceramic and metal interface in Example 1 is continuous, dense, and crack-free, with the metal phase fully wetting and filling the ceramic, and the interface is well bonded.

[0078] Example 2 This embodiment 2 provides a method for molding a bulletproof plate module, using silicon nitride as the ceramic raw material and titanium metal as the metal raw material, including the following specific steps: (1) Using silicon nitride as ceramic raw material, a ceramic blank with interconnected pore structure is formed by 3D printing, wherein the ceramic blank with interconnected pore structure includes a shell and a porous ceramic structure, the shell includes several closed surfaces and at least one opening, and the several closed surfaces form a cavity for accommodating the porous ceramic structure. S101. Based on a computer-aided system, design and generate a bulletproof plate model with a pre-defined interconnected hole structure; S102. Based on the bulletproof plate model, a ceramic blank with interconnected holes is formed by 3D printing. The ceramic blank with interconnected holes includes a shell and a porous ceramic structure, which are integrally formed.

[0079] A porous ceramic structure is placed within the cavity. The porous ceramic structure comprises multiple pores that are interconnected to form a porous channel. Specifically, the volume of the porous channel is 6300 mm². 3 The volume of the cavity is 12500 mm. 3 .

[0080] (2) Fill the cavity of the ceramic blank with titanium metal powder, and then perform preliminary vibration and compaction. The frequency of the preliminary vibration is 10 Hz and the vibration time is 15 min until the metal powder completely fills all the voids of the porous ceramic structure to obtain a ceramic metal blank. The sintering temperature of the titanium metal powder is 1400℃ and the sintering temperature of the silicon nitride ceramic blank is 1800℃. The volume ratio of ceramic to metal in the ceramic metal blank is 1:1 to 1:1.5.

[0081] (3) The thermal shrinkage curves of the ceramic and the metal are determined by a thermomechanical analyzer. The growth and melting temperature range of silicon nitride ceramic is 1750~1850℃. Within this temperature range, the temperature corresponding to the absolute value of the difference in shrinkage rate between titanium metal and silicon nitride ceramic is ≤20% is taken as the co-sintering temperature. The co-sintering temperature is selected as 1800℃. At this temperature, silicon nitride ceramic will shrink, but the volume of titanium metal is in a steady state, and its shrinkage size will be smaller than that of ceramic.

[0082] (4) The ceramic metal blank is placed in a sintering furnace and heated to 150°C at a rate of 2°C / min, held for 60 min, and simultaneously subjected to ultrasonic vibration at a frequency of 30 kHz for 20 min; heated to 300°C at a rate of 1°C / min, held for 60 min, and simultaneously subjected to ultrasonic vibration at a frequency of 30 kHz for 20 min; heated to 500°C at a rate of 3°C / min, held for 30 min, and simultaneously subjected to ultrasonic vibration at a frequency of 30 kHz for 40 min; heated to 1000°C at a rate of 4°C / min, held for 90 min, and simultaneously subjected to ultrasonic vibration at a frequency of 30 kHz for 20 min; heated to the co-sintering temperature at a rate of 5°C / min, held at the co-sintering temperature for 160 min, and cooled with the furnace. After cooling, the bulletproof plate module is obtained.

[0083] The bulletproof plate module obtained in Example 2 has the following microstructure: Figure 9 As shown, by Figure 9 It can be seen that the ceramic and metal interface in Example 2 is continuous, dense, and crack-free, with the metal phase fully wetting and filling the ceramic, and the interface is well bonded.

[0084] Comparative Example 1 Comparative Example 1 provides a method for forming a bulletproof plate module, which differs from Example 1 in that: in step (3), the co-sintering temperature is 1450℃, which is not within the determined co-sintering temperature range.

[0085] In step (4), the ceramic metal blank immersed in metal powder is placed in a sintering furnace and heated from room temperature at a rate of 4℃ / min. During the heating process, ultrasonic vibrations with a frequency of 20kHz are applied four times, each vibration lasting 40min. When the temperature reaches the co-sintering temperature of 1450℃, it is held at the co-sintering temperature for 240 minutes and then cooled with the furnace. After cooling, the bulletproof plate module is obtained.

[0086] The microstructure of the bulletproof plate module obtained in Comparative Example 1 is as follows: Figure 10 As shown, by Figure 10 It can be seen that the ceramic-metal interface in Comparative Example 1 has gaps and obvious cracks.

[0087] Comparative Example 2 Comparative Example 2 provides a method for forming a bulletproof plate module, which differs from Example 1 in that: in step (3), the co-sintering temperature is 1450℃, which is not within the determined co-sintering temperature range; In step (4), the ceramic metal blank immersed in metal powder is placed in a sintering furnace and heated from room temperature to co-sintering temperature of 1450℃ at a rate of 4℃ / min. The temperature is held at the co-sintering temperature for 240 minutes and then cooled with the furnace. After cooling, the bulletproof plate module is obtained.

[0088] The microstructure of the bulletproof plate module obtained in Comparative Example 2 is as follows: Figure 11 As shown, by Figure 11 It can be seen that the ceramic-metal interface in Comparative Example 2 has gaps and large cracks, reflecting that ultrasonic vibration sintering is extremely important for the densification of metal and ceramic.

[0089] Therefore, the bulletproof plate module provided by this invention combines the advantages of high hardness of ceramics and plasticity of metals. It adopts an ultrasonic vibration sintering process, which can break the oxide film on the surface of metal and ceramic particles during sintering, promote mutual diffusion and interlocking at the interface, and form a three-dimensional network microstructure that is interconnected. This significantly improves stress transmission efficiency, avoids the interface peeling failure common in traditional composite bulletproof plate materials, and avoids the problem of "local failure leading to overall failure" in traditional bulletproof plates. It has the advantages of strong armor penetration resistance and resistance to multiple hits, and can be widely used in specific scenarios requiring protection, such as bulletproof vests and armored vehicles.

[0090] The above description is merely a preferred embodiment of the present invention and should not be construed as limiting the scope of the invention. Therefore, any equivalent variations made in accordance with the claims of the present invention are still within the scope of the present invention.

Claims

1. A method for molding a bulletproof plate module, characterized in that, Includes the following steps: (1) A ceramic blank with interconnected pore structure is formed by 3D printing, wherein the ceramic blank with interconnected pore structure includes a shell and a porous ceramic structure, the shell includes a plurality of closed surfaces and at least one opening, the plurality of closed surfaces form a cavity for accommodating the porous ceramic structure; (2) Fill the cavity of the ceramic blank with metal powder, and after preliminary vibration and compaction, until the metal powder completely fills all the voids of the porous ceramic structure to obtain a ceramic metal blank. The sintering temperature of the metal powder is T1, the sintering temperature of the ceramic blank is T2, and T2-T1≤800℃. (3) Determine the co-sintering temperature based on the thermal shrinkage curves of ceramics and metals; (4) The ceramic metal blank is placed in a sintering furnace and subjected to ultrasonic vibration sintering treatment based on the co-sintering temperature to obtain the bulletproof plate module.

2. The molding method of a bulletproof plate module according to claim 1, characterized in that, Step (1) includes: A bulletproof plate model with a pre-defined interconnected hole structure is designed and generated based on a computer-aided system. Based on the bulletproof plate model, a ceramic blank with interconnected holes is formed by 3D printing. The ceramic blank with interconnected holes includes a shell and a porous ceramic structure, which are integrally formed.

3. The molding method of a bulletproof plate module according to claim 1, characterized in that, Step (1) includes: A bulletproof plate model with a pre-defined interconnected hole structure is designed and generated based on a computer-aided system. Based on the bulletproof plate model, a shell is formed by 3D printing. The shell includes several closed surfaces and at least one opening. The several closed surfaces form a cavity for accommodating a porous ceramic structure. Based on the bulletproof plate model, a porous ceramic structure was formed by 3D printing. The porous ceramic structure is placed inside the cavity to obtain a ceramic blank with interconnected pores.

4. The molding method of a bulletproof plate module according to claim 3, characterized in that, The porous ceramic structure is placed inside the cavity, and the porous ceramic structure includes multiple pores that are interconnected to form a porous channel. The volume of the porous channel is V1, and the volume of the cavity is V2. V1 and V2 satisfy: V2 = (1.8~2.2)V1.

5. The molding method of a bulletproof plate module according to claim 1, characterized in that, The ceramic body includes any one of single-phase ceramics and composite ceramics; the single-phase ceramic is any one of alumina, zirconium oxide, silicon nitride, silicon carbide, boron carbide, titanium diboride, aluminum oxynitride, aluminum magnesium spinel, and seron ceramics; the composite ceramic is any one of zirconium oxide toughened alumina, alumina composite silicon carbide, and alumina composite boron carbide. The metal powder is any one or more of tungsten and its alloys, titanium and its alloys, aluminum and its alloys, zirconium and its alloys, iron and its alloys, and magnesium and its alloys; The particle size range of the tungsten and its alloys is 1~12μm; The particle size range of the titanium and its alloys is 15~60μm; The particle size range of the aluminum and its alloys is 10~80μm; The zirconium and its alloys have a particle size range of 5~60 μm; The particle size range of the iron and its alloys is 8~65μm; The particle size range of the magnesium and its alloys is 3~80μm.

6. The molding method of a bulletproof plate module according to claim 1, characterized in that, In step (2), the volume ratio of ceramic to metal in the ceramic-metal blank is (1~4):(1~4). The initial vibration mode is any one or both of ultrasonic vibration and mechanical vibration; The frequency of the ultrasonic vibration is 20~40kHz, and the frequency of the mechanical vibration is 10~150Hz; The vibration lasts for 10 to 15 minutes.

7. The molding method of a bulletproof plate module according to claim 1, characterized in that, In step (3), the co-sintering temperature is determined based on the thermal shrinkage curves of the ceramic and the metal, including: The thermal shrinkage curves of ceramics and metals were obtained by thermomechanical analysis. Based on the thermal shrinkage curve of the ceramic, the melting growth temperature range of the ceramic is determined. The melting growth temperature range includes Ts and Te, where Ts is the shrinkage start point of the thermal shrinkage curve of the ceramic, and Te is the shrinkage end point of the thermal shrinkage curve of the ceramic. Based on the thermal shrinkage curves of the ceramic and the metal, within the melting growth temperature range of the ceramic, the temperature corresponding to the absolute value of the difference in shrinkage rates between the metal and the ceramic being ≤20% is taken as the co-sintering temperature.

8. The molding method of a bulletproof plate module according to claim 1, characterized in that, In step (4), the ceramic-metal blank is placed in a sintering furnace and subjected to ultrasonic vibration sintering based on the co-sintering temperature to obtain a bulletproof plate module comprising: The ceramic-metal blank is placed in a sintering furnace; The temperature is raised to the co-sintering temperature at a preset heating rate, and ultrasonic vibration is performed in multiple heating point intervals for a preset constant temperature duration. The bulletproof plate module was obtained by cooling it to room temperature in the furnace.

9. The molding method of a bulletproof plate module according to claim 8, characterized in that, The process involves heating to the co-sintering temperature at a preset heating rate, performing ultrasonic vibration at multiple heating point intervals, and maintaining the temperature for a preset preset duration, including: The temperature is increased to 150℃~200℃ at a rate of 2℃ / min~4℃ / min, and held for 60~90min. At the same time, ultrasonic vibration with a frequency ≥20kHz is applied for 20min~40min. The temperature is increased to 300℃~400℃ at a rate of 1℃ / min~3℃ / min, and held for 60~90min. At the same time, ultrasonic vibration with a frequency ≥20kHz is applied for 20min~40min. The temperature is increased to 500℃~600℃ at a rate of 1℃ / min~3℃ / min, and held for 30~60min. At the same time, ultrasonic vibration with a frequency ≥20kHz is applied for 20min~40min. The temperature is increased to 1000℃~1100℃ at a rate of 4℃ / min~6℃ / min and held for 60~90min, while ultrasonic vibration with a frequency ≥20kHz is applied for 20min~40min. Heat to the co-sintering temperature at a rate of 5℃ / min to 8℃ / min, and hold at the co-sintering temperature for 160 to 240 minutes.

10. A bulletproof plate module, characterized in that, It is manufactured by the molding method of a bulletproof plate module as described in any one of claims 1 to 9.

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