A casting-welding additive manufacturing method for three-dimensional ceramic / glass composite components

Abstract

This invention provides a casting-welding additive manufacturing method for three-dimensional ceramic / glass composite components, relating to the field of material joining technology. The method includes: Step S1, heating a base material with an inner cavity to a first temperature and performing a first heat treatment to obtain a first sample; wherein the base material is ceramic A; Step S2, pouring a molten glass B into the inner cavity of the first sample, heating to a second temperature, performing a second heat treatment, and cooling to room temperature to obtain the ceramic / glass composite component. For ceramic-glass connections at three-dimensional spatial interface surfaces, the method of this invention can produce ceramic / glass composite components with high welding rates and high connection strength.

Description

Technical Field

[0001] This invention relates to the field of material joining technology, and more specifically, to a casting-welding additive manufacturing method for three-dimensional ceramic / glass composite components. Background Technology

[0002] With the rapid iteration and upgrading of high-end equipment technology, single materials can no longer meet the multiple performance requirements of components under extreme working conditions. Ceramic-glass composite structures combine the high hardness, high temperature resistance, wear resistance, and corrosion resistance of ceramic materials with the advantages of good light transmittance, excellent dielectric properties, and high chemical stability of glass materials, achieving complementary performance advantages and realizing the design goal of "structural-functional integration". Currently, ceramic-glass composite structures have been widely used in many key fields such as aerospace optoelectronic detection, deep-sea optical detection, high-energy physics detection, and biomedical implants, and the industry demand continues to increase. Therefore, research on high-performance manufacturing and connection methods for ceramic-glass composite structures has significant industrial value and academic research significance.

[0003] Unlike single homogeneous material components, ceramics and glass are heterogeneous inorganic materials with vastly different properties. They exhibit significant differences in intrinsic physical properties such as thermal expansion coefficients, elastic moduli, and softening temperatures. This makes the joint interface prone to large residual stresses, leading to problems such as joint cracking, insufficient connection strength, and substandard optical transmittance – a persistent technical challenge in the field of joining heterogeneous inorganic materials. Furthermore, in terms of the morphology of the joint surface, high-end ceramic-glass composite structures used in aerospace, optoelectronic detection, and other fields typically require three-dimensional spatial surfaces to meet the requirements of optical path design, spatial layout, and assembly. These include continuous curved surfaces with large curvatures, complex cavity walls, and multi-corner straight-surface combinations, placing higher demands on the surface adaptability of the joining process compared to traditional two-dimensional planar connections.

[0004] Most current mainstream ceramic-glass joining technologies are developed for two-dimensional planar joining scenarios. When directly applied to three-dimensional joining surfaces, they suffer from several inherent and unresolved defects: First, conventional fusion welding processes are limited by the three-dimensional surface contour, making it difficult to evenly cover the entire joining surface with heat. This results in uneven fusion across the entire surface, leading to localized incomplete welding defects, low overall welding rate, insufficient joint strength and stability, and the potential for glass cracking due to uneven heating, resulting in extremely low yield. Second, for diffusion joining processes, it is difficult to achieve uniform pressure on complex three-dimensional surfaces. Pressure deviations at different locations on the surface can cause uneven interfacial bonding, leading to insufficient bonding strength in localized areas. Furthermore, diffusion joining requires high-temperature and high-pressure forming conditions, and high temperatures can easily cause glass crystallization and breakage. First, the inherent optical / dielectric properties of the glass are problematic, and the equipment costs are high and the production efficiency is low, making it unsuitable for the mass production of large-size and complex structural components. Second, for brazing, a large amount of active elements are often added to improve ceramic wettability, which easily generates a continuous thick layer of brittle phase at the joint interface, significantly reducing the impact resistance and load-bearing capacity of the joint. Furthermore, the residual stress from welding is more unevenly distributed on the three-dimensional joint surface, making it more prone to joint cracking. At the same time, impurities in the brazing filler metal affect the light transmittance of the glass side, failing to meet the requirements for optoelectronic components. Third, while bonding ceramic glass is a simple process that can adapt to complex surfaces, the adhesive layer itself has poor high-temperature resistance, is prone to aging and yellowing, and has poor optical stability, failing to meet the extreme operating conditions required in aerospace, high-energy detection, and other fields.

[0005] In summary, existing two-dimensional planar ceramic-glass connection technologies cannot meet the connection requirements of three-dimensional spatial connection surfaces, and are unable to solve the technical problems of low welding rate and insufficient connection strength. They also cannot meet the performance requirements of high-end equipment. Therefore, it is urgent to develop new high-performance ceramic-glass composite structure connection technologies for three-dimensional spatial connection surfaces. Summary of the Invention

[0006] The problem solved by this invention is that existing ceramic-glass joining technology cannot adapt to three-dimensional spatial joining surfaces, resulting in low welding rate and low joining strength of the composite components.

[0007] To address the above problems, this invention provides a casting-welding additive manufacturing method for three-dimensional ceramic / glass composite components, comprising: Step S1: Heat the base material with the inner cavity to a first temperature and perform a first heat preservation treatment to obtain a first sample; wherein, the base material is ceramic A; Step S2: Pour the melt of glass B into the inner cavity of the first sample, heat it to a second temperature, perform a second heat preservation treatment, and cool it to room temperature to obtain a ceramic / glass composite component; wherein, the melting point of ceramic A is T1, the softening temperature of glass B is T2, T1 is more than 300°C higher than T2, the temperature of the melt is 100°C to 500°C higher than T2, and the temperature of the outer wall of the first sample is maintained at the first temperature during the pouring process, the first temperature is 10°C to 200°C lower than T2; the second temperature is 300°C to 600°C higher than T2.

[0008] Optionally, in step S1, the shape of the inner cavity is selected from one of hemispherical, trumpet-shaped, and cubic.

[0009] Optionally, the ceramic A comprises AlN ceramic, and the glass B comprises borosilicate glass.

[0010] Optionally, the ceramic A includes SiC ceramic, and the glass B includes lithium aluminum silicon microcrystalline glass.

[0011] Optionally, the ceramic A comprises nickel-zinc ferrite, and the glass B comprises bismuth-boron nickel-iron doped glass.

[0012] Optionally, in step S2, the method for preparing the melt made of glass B includes: heating a block of glass B to a temperature 100°C to 500°C higher than T2, and holding it at that temperature under ultrasonic and stirring conditions to obtain the melt; wherein the power of the ultrasonic is 2000W to 3000W and the frequency is 10kHz to 30kHz.

[0013] Optionally, in step S2, the duration of the second heat preservation treatment is 10 min to 60 min.

[0014] Optionally, in step S2, during the second heat preservation process, the melt is ultrasonically treated by multiple ultrasonic amplitude rods arranged in an array and extending below the surface of the melt, and the first sample is ultrasonically treated by multiple ultrasonic amplitude rods evenly distributed along the outer wall of the first sample.

[0015] Optionally, in step S2, the power of the ultrasonic treatment of the melt is 2000W to 3000W, and the frequency is 20kHz to 40kHz.

[0016] Optionally, in step S2, the power of the ultrasonic treatment of the first sample is 200W to 600W, and the frequency is 10kHz to 20kHz.

[0017] Compared with related technologies, this invention integrates the casting and forming of the glass melt with the joining of ceramic glass in one step, achieving integrated casting and welding. Glass B, in its molten state, directly fills the three-dimensional cavity of the ceramic A base material. Since the melting point of ceramic A is much higher than the softening temperature of glass B, the base material itself will not deform, soften, or deteriorate in performance during the joining process. The melt temperature is 100°C to 500°C higher than the softening temperature of glass B, ensuring that the glass melt has sufficient fluidity and can uniformly wet and spread to all positions of the three-dimensional connection surface, even complex corners and large curvature cavity walls can be completely covered. During the casting process, the outer wall temperature of the first sample is continuously maintained at the first temperature. The first temperature is 10°C to 200°C lower than the softening temperature of glass B. This temperature maintains the slow cooling of the melt, avoiding the generation of additional residual stress, and also prevents excessive gas absorption by the glass melt due to excessive temperature, thus reducing the generation of porosity defects. The final second heat treatment temperature is 300°C to 600°C higher than the softening temperature of glass B. This provides sufficient energy for the diffusion of interfacial atoms, ensuring a stable and reliable interfacial bond between ceramic A and glass B. At the same time, it avoids excessive residual stress or excessive interfacial reaction caused by excessive temperature, thus avoiding defects such as joint cracking and the formation of thick brittle phases. Ultimately, ceramic / glass composite components with high welding rate and high connection strength can be produced. Attached Figure Description

[0018] Figure 1 This is a schematic diagram of the casting and welding additive manufacturing method for three-dimensional ceramic / glass composite components in an embodiment of the present invention; Figure 2 This is the final composite component sample obtained in Example 1 of the present invention; Figure 3 This is the final composite component sample obtained in Example 2 of the present invention; Figure 4 This is the final composite component sample obtained in Example 3 of the present invention; Figure 5 This is a scanning electron microscope image of the interface of the ceramic / glass composite component prepared in Example 1. Detailed Implementation

[0019] To make the above-mentioned objects, features, and advantages of the present invention more apparent and understandable, specific embodiments of the present invention will be described in detail below with reference to the accompanying drawings. Although some embodiments of the present invention are shown in the drawings, it should be understood that the present invention can be implemented in various forms and should not be construed as limited to the embodiments set forth herein. Rather, these embodiments are provided to provide a more thorough and complete understanding of the present invention. It should be understood that the accompanying drawings and embodiments of the present invention are for illustrative purposes only and are not intended to limit the scope of protection of the present invention.

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

[0021] The term "comprising" and its variations as used herein are open-ended, meaning "including but not limited to"; the term "based on" means "at least partially based on"; the term "one embodiment" means "at least one embodiment"; the term "another embodiment" means "at least one additional embodiment"; the term "some embodiments" means "at least some embodiments"; and the term "optionally" means "optional embodiments". Definitions of other terms will be given in the following description. It should be noted that the concepts of "first," "second," etc., mentioned in this invention are used to distinguish different objects, not to describe a specific order or hierarchy. Furthermore, the terms "first" and "second" are used for descriptive purposes only and should not be construed as indicating or implying relative importance or implicitly specifying the number of indicated technical features. Thus, a feature defined with "first" or "second" may explicitly or implicitly include one or more of that feature. In the description of this invention, unless otherwise stated, "a plurality of" means two or more.

[0022] It should be noted that, Figures 2 to 4 In the text, A represents ceramic (A), and B represents glass (B).

[0023] like Figure 1 As shown in the embodiment of the present invention, a casting-welding additive manufacturing method for a three-dimensional ceramic / glass composite component includes: Step S1: Heat the base material with the inner cavity to a first temperature and perform a first heat preservation treatment to obtain a first sample; wherein, the base material is ceramic A; Step S2: Pour the melt of glass B into the inner cavity of the first sample, heat it to a second temperature, perform a second heat preservation treatment, and cool it to room temperature to obtain a ceramic / glass composite component; wherein, the melting point of ceramic A is T1, the softening temperature of glass B is T2, T1 is more than 300°C higher than T2, the temperature of the melt is 100°C to 500°C higher than T2, and the temperature of the outer wall of the first sample is maintained at the first temperature during the pouring process, the first temperature is 10°C to 200°C lower than T2; the second temperature is 300°C to 600°C higher than T2.

[0024] This invention integrates the casting and bonding of glass melt with ceramic glass in a single step, achieving integrated casting and welding. Glass B, in molten state, directly fills the three-dimensional cavity of ceramic A. Since the melting point of ceramic A is much higher than the softening temperature of glass B, the base material itself will not deform, soften, or deteriorate during the bonding process. The melt temperature is 100°C to 500°C higher than the softening temperature of glass B, ensuring sufficient fluidity for uniform wetting and spreading across all positions of the three-dimensional bonding surface. Even complex corners and highly curved cavity walls can be completely covered. During the casting process, the outer wall temperature of the first sample is continuously maintained at the first temperature. The first temperature is 10°C to 200°C lower than the softening temperature of glass B. This allows the melt to cool slowly, avoiding the generation of additional residual stress, and also prevents excessive gas absorption by the glass melt due to excessive temperature, thus reducing the generation of porosity defects. The second temperature is 300°C to 600°C higher than the softening temperature of glass B. This provides sufficient energy for interfacial atomic diffusion, ensuring a stable and reliable interfacial bond between ceramic A and glass B. At the same time, it avoids excessive residual stress or excessive interfacial reaction caused by excessive temperature, thus avoiding defects such as joint cracking and the formation of thick brittle phases. Ultimately, ceramic / glass composite components with high welding rate and high connection strength can be produced.

[0025] In some embodiments of the present invention, in step S1, the shape of the inner cavity is exemplary, selected from one of hemispherical, trumpet-shaped, and cubic.

[0026] In some embodiments of the present invention, for example, the ceramic A comprises AlN ceramic and the glass B comprises borosilicate glass.

[0027] In some embodiments of the present invention, for example, the ceramic A comprises SiC ceramic and the glass B comprises lithium aluminum silicon microcrystalline glass.

[0028] In some embodiments of the present invention, for example, the ceramic A comprises nickel-zinc ferrite, and the glass B comprises bismuth-boron nickel-iron doped glass.

[0029] In some embodiments of the present invention, the method for preparing the melt made of glass B in step S2 includes: heating a block of glass B to a temperature 100°C to 500°C higher than T2, and holding it at that temperature under ultrasonic and stirring conditions to obtain the melt; wherein the power of the ultrasonic treatment is 2000W to 3000W, and the frequency is 10kHz to 30kHz. In this embodiment, the ultrasonic cavitation effect forms cavitation bubbles, promoting the nucleation and upward overflow of dissolved gases in the melt. Stirring further helps to reduce porosity defects by causing the gas bubbles to rise and overflow.

[0030] In some embodiments of the present invention, in step S2, the duration of the second heat preservation treatment is 10 min to 60 min.

[0031] In some embodiments of the present invention, during the second heat preservation process in step S2, ultrasonic treatment of the melt is performed by multiple ultrasonic amplitude transformers arranged in an array and extending below the surface of the melt, while ultrasonic treatment of the first sample is performed by multiple ultrasonic amplitude transformers uniformly distributed along the outer wall of the first sample. In this embodiment, ultrasonic treatment in the melt is applied to promote the uniform precipitation of fine whiskers in the glass melt, enhancing the strength and uniformity of the glass material itself; at the same time, uniform ultrasonic treatment is applied to the outer side of the first sample's outer wall to promote the uniform precipitation and growth of whiskers in the ceramic / glass interface region through the action of a high-energy sound field, strengthening the mechanical properties of the interface, thereby further improving the strength of the bonding interface. It should be noted that the object of ultrasonic treatment of the first sample is the outer wall of the first sample.

[0032] In some embodiments of the present invention, in step S2, the power of the ultrasonic treatment of the melt is 2000W to 3000W, and the frequency is 20kHz to 40kHz.

[0033] In some embodiments of the present invention, in step S2, the power of the first sample ultrasonic treatment is 200W to 600W, and the frequency is 10kHz to 20kHz.

[0034] The present invention will be further described below with reference to specific embodiments.

[0035] Example 1 A1. The base material with an inner cavity is heated to a first temperature and subjected to a first heat preservation treatment to obtain a first sample; wherein, the base material is a trumpet-shaped shell with a trumpet-shaped inner cavity, the outer diameter of the open end of the base material is 250mm, the inner diameter of the open end is 230mm, the outer diameter of the constricted end is 120mm, the inner diameter of the constricted end is 100mm, and the total height is 140mm. The material of the base material is ceramic A, which is reaction-sintered AlN ceramic, and the melting point of ceramic A is 2200℃; the first temperature is 450℃; and the time of the first heat preservation treatment is 30min.

[0036] A2. The block of glass B is heated to 960°C to melt it, and then held at that temperature under ultrasonic and stirring conditions to obtain a melt. Glass B is borosilicate glass, which is composed of SiO2, B2O3 and Na2O in a molar ratio of 32.3:64.7:3. The softening temperature of glass B is 500°C, and the ultrasonic power is 3000W with a frequency of 24kHz.

[0037] A3. The melt is poured into the inner cavity of the first sample, heated to a second temperature, subjected to a second heat treatment, and cooled to room temperature to obtain a ceramic / glass composite component; the ceramic / glass composite component is then machined to obtain the final composite component sample, such as... Figure 2 As shown; wherein, the temperature of the melt is 960℃, the temperature of the outer wall of the first sample is maintained at 450℃ during the casting process, and the second temperature is 1000℃; the second heat preservation treatment time is 30min, during the second heat preservation treatment, the melt is ultrasonically treated by multiple ultrasonic amplitude transformers arranged in an array and extending below the surface of the melt, and the first sample is ultrasonically treated by multiple ultrasonic amplitude transformers evenly distributed along the outer wall of the first sample. The power of the melt ultrasonic treatment is 2540W and the frequency is 37.9kHz, and the power of the first sample ultrasonic treatment is 375W and the frequency is 18.6kHz.

[0038] Example 2 A1. The base material with an inner cavity is heated to a first temperature and subjected to a first heat preservation treatment to obtain a first sample; wherein, the base material is a hemispherical shell with an inner diameter of 400 mm and an outer diameter of 418 mm, and the inner cavity is hemispherical; the material of the base material is ceramic A, which is reaction-sintered SiC ceramic, and the melting point of ceramic A is 2830℃; the first temperature is 720℃; and the time of the first heat preservation treatment is 30 min.

[0039] A2. The block of glass B is heated to 1100℃ to melt it, and then held at that temperature under ultrasonic and stirring conditions to obtain a melt. Glass B is a lithium aluminum silicon microcrystalline glass, which is composed of Li2O, Y2O3, SiO2 and Al2O3 in a mass ratio of 8.5:12:15:64.5. The softening temperature of glass B is 880℃, and the ultrasonic power is 3000W with a frequency of 27kHz.

[0040] A3. The melt is poured into the inner cavity of the first sample, heated to a second temperature, subjected to a second heat treatment, and cooled to room temperature to obtain a ceramic / glass composite component; the ceramic / glass composite component is then machined to obtain the final composite component sample, such as... Figure 3 As shown; wherein, the temperature of the melt is 1100℃, the temperature of the outer wall of the first sample is maintained at 720℃ during the casting process, and the second temperature is 1200℃; the second heat preservation treatment time is 40min, during the second heat preservation treatment, the melt is ultrasonically treated by multiple ultrasonic amplitude transformers arranged in an array and extending below the surface of the melt, and the first sample is ultrasonically treated by multiple ultrasonic amplitude transformers evenly distributed along the outer wall of the first sample. The power of the melt ultrasonic treatment is 2600W and the frequency is 40kHz, and the power of the first sample ultrasonic treatment is 200W and the frequency is 19kHz.

[0041] Example 3 A1. The base material with an inner cavity is heated to a first temperature and subjected to a first heat preservation treatment to obtain a first sample; wherein, the base material is a cubic shell with an outer contour side length of 250mm, the inner cavity is a cube with an inner cavity side length of 240mm, the material of the base material is ceramic A, ceramic A is nickel-zinc ferrite, and the melting point of ceramic A is 1300℃; the first temperature is 390℃; the time of the first heat preservation treatment is 30min.

[0042] A2. The bulk of glass B is heated to 850°C to melt it, and then held at that temperature under ultrasonic and stirring conditions to obtain a melt. Glass B is a bismuth-boron nickel-iron doped glass, which is composed of Bi2O3, B2O3, NiO and Fe2O3 in a molar ratio of 38.5:31.5:15:15. The softening temperature of glass B is 400°C, and the ultrasonic power is 3000W with a frequency of 27kHz.

[0043] A3. The melt is poured into the inner cavity of the first sample, heated to a second temperature, subjected to a second heat treatment, and cooled to room temperature to obtain a ceramic / glass composite component; the ceramic / glass composite component is then machined to obtain the final composite component sample, such as... Figure 4 As shown; wherein, the temperature of the melt is 850℃, the temperature of the outer wall of the first sample is maintained at 390℃ during the casting process, and the second temperature is 900℃; the second heat preservation treatment time is 15min, during the second heat preservation treatment, the melt is ultrasonically treated by multiple ultrasonic amplitude transformers arranged in an array and extending below the surface of the melt, and the first sample is ultrasonically treated by multiple ultrasonic amplitude transformers evenly distributed along the outer wall of the first sample. The power of the melt ultrasonic treatment is 2500W and the frequency is 21kHz, and the power of the first sample ultrasonic treatment is 260W and the frequency is 20kHz.

[0044] Comparative Example 1 The difference from Example 1 is that in step A3, no measures were taken during the casting process to ensure that the temperature of the outer wall of the first sample was 390°C.

[0045] Comparative Example 2 The difference from Example 1 is that step A2 is: heating the block of glass B to 850°C to melt it, holding it at that temperature to obtain a melt; wherein, glass B is a bismuth boron nickel iron doped glass, which is composed of Bi2O3, B2O3, NiO and Fe2O3 in a molar ratio of 38.5:31.5:15:15, and the softening temperature of glass B is 400°C.

[0046] Comparative Example 3 The difference from Example 1 is that, in step A3, the first sample was not subjected to ultrasonic treatment during the second heat preservation process.

[0047] Comparative Example 4 The difference from Example 1 is that step A3 is as follows: the melt is poured into the inner cavity of the first sample and cooled to room temperature to obtain a ceramic / glass composite component; the ceramic / glass composite component is machined to obtain the final composite component sample; wherein the temperature of the melt is 960°C and the temperature of the outer wall of the first sample is maintained at 450°C during the pouring process.

[0048] Comparative Example 5 The difference from Example 1 is that step A3 is as follows: the melt is poured into a mold and cooled to room temperature to obtain a glass ingot; the glass ingot is processed using a CNC machine tool to obtain a horn-shaped weldment whose shape and size match the inner cavity of the first sample; the horn-shaped weldment is installed in the inner cavity of the first sample and diffusion welding is performed under a pressure of 6 MPa to obtain a ceramic / glass composite component; the ceramic / glass composite component is machined to obtain the final composite component sample; wherein the diffusion welding temperature is 500℃ and the time is 90 min.

[0049] Effect Example The interface of the ceramic / glass composite component prepared in Example 1 was characterized by scanning electron microscopy, and the results are shown in the figure. Figure 5 ,from Figure 5 It can be seen that the ceramic / glass composite component prepared in Example 1 has a completely welded interface, and the whiskers are evenly distributed at the interface, which can enhance the mechanical properties of the interface and relieve residual stress.

[0050] Welding rate and shear strength were tested on the ceramic / glass composite components prepared in Examples 1 to 3 and Comparative Examples 1 to 5. The results are shown in Table 1. Table 1 shows that the ceramic / glass composite components prepared in Examples 1 to 3 had high welding rates and high shear strengths. No defects were found at the connection interfaces of the ceramic / glass composite components in Examples 1 to 3. Compared with Example 1, the ceramic / glass composite component prepared in Comparative Example 1 had lower welding rates and shear strengths, and visible cracks appeared at the connection interfaces of the composite component. Compared with Example 1, the ceramic / glass composite component prepared in Comparative Example 2 had lower welding rates and shear strengths, and dispersed pore defects were present at the connection interfaces of the composite component. Compared with Example 1, the ceramic / glass composite component prepared in Comparative Example 3 had lower shear strengths, and a large amount of whiskers precipitated and grew unevenly at the connection interfaces of the composite component. Compared with Example 1, the ceramic / glass composite components prepared in Comparative Examples 4 and 5 could not be welded and had lower shear strengths.

[0051] Table 1

[0052] It should be noted that in Table 1, "-" indicates that the shear strength is too small to be measured.

[0053] While the present invention has been disclosed above, its scope of protection is not limited thereto. Those skilled in the art can make various changes and modifications without departing from the spirit and scope of the present invention, and all such changes and modifications will fall within the scope of protection of the present invention.

Claims

1. A method for casting and welding additive manufacturing of a three-dimensional ceramic / glass composite component, characterized in that, include: Step S1: Heat the base material with the inner cavity to a first temperature and perform a first heat preservation treatment to obtain a first sample; wherein, the base material is ceramic A; Step S2: Pour the melt of glass B into the inner cavity of the first sample, heat it to a second temperature, perform a second heat preservation treatment, and cool it to room temperature to obtain a ceramic / glass composite component; wherein, the melting point of ceramic A is T1, the softening temperature of glass B is T2, T1 is more than 300°C higher than T2, the temperature of the melt is 100°C to 500°C higher than T2, and the temperature of the outer wall of the first sample is maintained at the first temperature during the pouring process, the first temperature is 10°C to 200°C lower than T2; the second temperature is 300°C to 600°C higher than T2.

2. The method for casting and welding additive manufacturing of three-dimensional ceramic / glass composite components according to claim 1, characterized in that, In step S1, the shape of the inner cavity is selected from one of hemispherical, trumpet-shaped, and cubic.

3. The casting-welding additive manufacturing method for three-dimensional ceramic / glass composite components according to claim 1, characterized in that, The ceramic A includes AlN ceramic, and the glass B includes borosilicate glass.

4. The method for casting and welding additive manufacturing of three-dimensional ceramic / glass composite components according to claim 1, characterized in that, The ceramic A includes SiC ceramic, and the glass B includes lithium aluminum silicon microcrystalline glass.

5. The method for casting and welding additive manufacturing of three-dimensional ceramic / glass composite components according to claim 1, characterized in that, The ceramic A comprises nickel-zinc ferrite, and the glass B comprises bismuth-boron nickel-iron doped glass.

6. The method for casting and welding additive manufacturing of three-dimensional ceramic / glass composite components according to claim 1, characterized in that, In step S2, the method for preparing the melt made of glass B includes: heating a block of glass B to a temperature 100°C to 500°C higher than T2, and holding it at that temperature under ultrasonic and stirring conditions to obtain the melt; wherein the power of the ultrasonic is 2000W to 3000W and the frequency is 10kHz to 30kHz.

7. The method for casting and welding additive manufacturing of three-dimensional ceramic / glass composite components according to claim 1, characterized in that, In step S2, the second heat preservation treatment lasts for 10 to 60 minutes.

8. The method for casting and welding additive manufacturing of three-dimensional ceramic / glass composite components according to claim 1, characterized in that, In step S2, during the second heat preservation process, the melt is ultrasonically treated by multiple ultrasonic amplitude rods arranged in an array and extending below the surface of the melt, and the first sample is ultrasonically treated by multiple ultrasonic amplitude rods evenly distributed along the outer wall of the first sample.

9. The method for casting and welding additive manufacturing of three-dimensional ceramic / glass composite components according to claim 8, characterized in that, In step S2, the power of the ultrasonic treatment of the melt is 2000W to 3000W, and the frequency is 20kHz to 40kHz.

10. The method for casting and welding additive manufacturing of a three-dimensional ceramic / glass composite component according to claim 8, characterized in that, In step S2, the power of the ultrasonic treatment of the first sample is 200W to 600W, and the frequency is 10kHz to 20kHz.

Images