A high-density cordierite ceramic slurry and a preparation method thereof

Abstract

The application provides a high-density cordierite ceramic slurry and a preparation method thereof. The ceramic slurry is prepared from raw materials including the following components in parts by weight: 10-25 parts of end-methyl acrylate group polymethylphenylsiloxane resin, 20-35 parts of talcum powder, 15-25 parts of aluminum oxide powder, 5-15 parts of silicon dioxide powder, 0.5-3 parts of a photoinitiator, and 0.1-2 parts of a dispersing agent. The high-density cordierite ceramic slurry has a significantly improved density: by combining the 'pre-crosslinking hole sealing mechanism' of a specific structure PSO with 'low organic content setting', the generation of macroscopic pores in the sintering process is fundamentally reduced, so that the apparent porosity of the final ceramic product can be reduced to below 8%, and the bulk density is increased to 2.3 g / cm 3 above.

Description

Technical Field

[0001] This invention belongs to the field of ceramic materials technology, specifically relating to a high-density cordierite ceramic slurry and its preparation method. Background Technology

[0002] Cordierite (2MgO•2Al2O3•5SiO2) ceramics are widely used in heat-resistant devices, automotive exhaust purification carriers, and electronic packaging materials due to their extremely low coefficient of thermal expansion, excellent thermal shock stability, and good dielectric properties.

[0003] Digital light processing (DLP) technology, as a high-precision surface projection additive manufacturing technology, provides strong support for the molding of complex cordierite ceramics. Currently, cordierite ceramics can be prepared using the polymer-derived ceramics (PDCs) route via DLP. As described in existing technology (Ceramics International, 2023, 31210), photosensitive polysiloxane (PSO) is used as the resin matrix, silicon source, and pore-forming agent, blended with talc and alumina fillers to prepare a slurry. Although this method can successfully prepare cordierite ceramics, the complete decomposition of PSO during sintering, generating a large amount of gas, results in a high porosity in the final product (typically forming a hierarchical pore structure of 1-50 μm), limiting its application in scenarios requiring high density and high mechanical strength. Cordierite ceramics prepared by existing technologies typically have an apparent porosity of over 30% and a bulk density of approximately 1.75 g / cm³. 3 This makes it difficult to meet the requirements of structural components.

[0004] In addition, the formation of cordierite is extremely sensitive to sintering temperature and has a narrow sintering window. If the temperature is not properly controlled, too much glass phase is easily generated or the product softens and deforms, making it difficult to obtain cordierite ceramics with both high purity and high density at the same time.

[0005] Therefore, developing a special slurry capable of forming high-density, low-porosity, and high-purity cordierite phase through photopolymerization 3D printing technology, along with a matching precision sintering process, to overcome the contradictions in existing technologies where high porosity due to high organic content and the difficulty in balancing high density and printability, has become an urgent problem to be solved in this field. Summary of the Invention

[0006] In view of this, the present invention aims to overcome the defects in the prior art and proposes a high-density cordierite ceramic slurry and its preparation method.

[0007] To achieve the above objectives, the technical solution of the present invention is implemented as follows: A high-density cordierite ceramic slurry, wherein the ceramic slurry is made from raw materials comprising the following parts by weight: 10-25 parts of methacrylate-terminated polymethylphenylsiloxane resin, 20-35 parts talcum powder 15-25 parts of alumina powder 5-15 parts of silica powder Photoinitiator 0.5-3 parts, Dispersant 0.1-2 parts.

[0008] Furthermore, the general structural formula of the terminal methacrylate-based polymethylphenylsiloxane resin is: (R1)3SiO-(R2SiO) x -(R3SiO) γ -Si(R1)3, wherein R1 is methacryloyloxypropyl, R2 is phenyl or methyl, R3 is glycidyl etheroxypropyl, and based on the total molar number of siloxane segments as 100%, the proportion of phenyl siloxane segments is 15-30%, the proportion of glycidyl etheroxypropyl siloxane segments is 2-5%, and the remainder is dimethyl siloxane segments; the ceramic yield of the terminal methacrylate-based polymethylphenyl siloxane resin at 1300℃ is 75-80%.

[0009] Furthermore, the preparation method of the terminal methacrylate-based polymethylphenylsiloxane resin includes the following steps: mixing hydrogen-terminated polymethylphenylsiloxane, glycidoxypropylmethyldimethoxysilane and allyl methacrylate, adding a platinum catalyst, and carrying out hydrosilylation reaction and silanol condensation reaction, and obtaining the terminal methacrylate-based polymethylphenylsiloxane resin after the reaction is completed.

[0010] Furthermore, the weight proportions of the talc powder, alumina powder, silica powder, and methacrylate-terminated polymethylphenylsiloxane resin in the ceramic slurry satisfy the following formulas (I)-(II): W A =0.538×α×W T Equation (I) W S =(0.791×β-0.633)×W T -K×W P Formula (II) The weight parts of the talc powder are W. T The alumina powder has a weight ratio of W. A The silicon dioxide powder has a weight ratio of W. S The methacrylate-terminated polymethylphenylsiloxane resin described herein has a weight ratio of W. P; 0.538 is a constant derived from the MgO content in talc and the theoretical mass ratio of Al2O3 / MgO in cordierite; 0.791 is a constant derived from the MgO content in talc and the theoretical mass ratio of SiO2 / MgO in cordierite; 0.633 is the content coefficient of intrinsic SiO2 in talc (63.3 wt%); α is the aluminum-rich liquid phase control coefficient, α=1.2-1.3, which inhibits the decomposition of cordierite and the generation of a high-viscosity aluminum-rich glass phase in the temperature range of 1350-1385℃ to prevent product deformation; β is the silicon-rich liquid phase control coefficient, β=1.7-1.9, which generates an appropriate amount of low-viscosity liquid phase to promote particle rearrangement and pore filling; K is the equivalent coefficient of polysiloxane resin to SiO2, K=0.75-0.80.

[0011] Furthermore, the ceramic slurry also includes a sintering aid, which is at least one of yttrium fluoride or potassium fluorozirconate.

[0012] Furthermore, the silica powder is at least one of fused silica powder or cristobalite powder; the particle size D of the silica powder is... 50 It is 0.5-5 μm.

[0013] Furthermore, the apparent porosity of the ceramic slurry is less than 8%, and the bulk density is greater than 2.3 g / cm³. 3 .

[0014] The present invention also provides a method for preparing a high-density cordierite ceramic slurry, comprising the following steps: first, mixing methacrylate-terminated polymethylphenylsiloxane resin, photoinitiator and dispersant evenly, then adding talc powder, alumina powder, silica powder and sintering aid, and after ball milling and degassing, obtaining the high-density cordierite ceramic slurry; the ball milling step is performed at a speed of 200-400 rpm for 2-6 hours.

[0015] The present invention also provides a method for preparing high-density cordierite ceramics using the aforementioned ceramic slurry, comprising the following steps: (1) The ceramic slurry is photocured and 3D printed to obtain a green body; (2) The green body is degreased and sintered to obtain the high-density cordierite ceramic.

[0016] Furthermore, in step (1), the thickness of the photopolymer 3D printing layer is 20-100 μm, the single-layer exposure time is 5-30 s, and the exposure energy is 10-50 mJ / cm². 2The degreasing and sintering steps in step (2) are as follows: the temperature is raised to 600℃ at a rate of 0.5-3℃ / min and held at that temperature to complete the degreasing, and then the temperature is raised to 1370-1380℃ at a rate of 1-3℃ / min and held at that temperature for 1-3 hours.

[0017] The high-density cordierite ceramic slurry of this invention, through a combination of a pre-crosslinking and sealing mechanism of PSO with a specific structure and a low organic content setting, fundamentally reduces the formation of macroscopic pores during sintering. The PSO of this invention uses low-viscosity polymethylphenylsiloxane as a flexible main chain, concentrating photocurable double bonds at the chain ends to ensure rapid DLP molding. Simultaneously, trace amounts of epoxy groups are introduced into the side chains, spontaneously crosslinking to form a dense network in the early stages of debinding, confining the trace gases generated by resin pyrolysis to the nanoscale and blocking the formation of macroscopic pores. Silica is precisely introduced as the main inorganic silicon source according to formulas (I)-(II), reducing the proportion of organic decomposition products from the source. Furthermore, through precise setting of α and β coefficients, combined with narrow-temperature precision sintering and trace sintering aids, a significant improvement in the density of the ceramic body is achieved synergistically.

[0018] Compared with the prior art, the present invention has the following advantages: The high-density cordierite ceramic slurry of the present invention significantly improves the density: reducing the apparent porosity of the final ceramic product to below 8% and increasing the bulk density to 2.3 g / cm³. 3 above.

[0019] The high-density cordierite ceramic slurry of this invention takes into account both printing rheology and curing properties: the introduction of a flexible phenylsiloxane backbone significantly reduces the viscosity of high-solids slurry; the concentration of photosensitive double bonds at the chain ends eliminates steric hindrance in polymerization, ensuring extremely high double bond conversion rate and green strength during DLP printing.

[0020] The sintering process window of the preparation method described in this invention is more controllable: by precisely setting the coefficients α and β in the formula, and combining it with precision sintering in a narrow temperature range of 1350-1385 ℃, the decomposition of the cordierite phase and the generation of excessive glass phase are effectively avoided, ensuring the formation of high-purity cordierite phase and the maintenance of the shape of the product. Attached Figure Description

[0021] Figure 1 This is a scanning electron microscope (SEM) image of the cross-section of the high-density cordierite ceramic described in Embodiment 1 of the present invention; Figure 2 This is a photograph of a green body obtained by photopolymerization 3D printing of the ceramic slurry described in Embodiment 1 of the present invention. Detailed Implementation

[0022] Unless otherwise defined, the technical terms used in the following embodiments have the same meanings as commonly understood by those skilled in the art. Unless otherwise specified, the experimental reagents used in the following embodiments are conventional biochemical reagents; and the experimental methods described are conventional methods.

[0023] The present invention will be described in detail below with reference to the embodiments.

[0024] Example 1 A method for preparing high-density cordierite ceramics includes the following steps: (1) Synthesis of low-viscosity, high-conformity photocurable polysiloxane resin: In a three-necked flask equipped with a condenser, 100 g of hydrogen-terminated polymethylphenylsiloxane (with a phenylsiloxane molar percentage of 20%, glycidyl etheroxypropylsiloxane molar percentage of 3%, Si-H bond molar concentration of 0.15 mol / 100 g, and a viscosity of 600 mPa•s at 25 °C), 3 g of glycidyl etheroxypropylmethyldimethoxysilane, and 0.5 g of catalyst (Karstedt platinum catalyst, platinum content 3000 ppm) were added. Under nitrogen protection, the mixture was stirred at 80 °C for 2 hours to induce silanol condensation. The temperature was then lowered to 65 °C, and 18 g of allyl methacrylate (AMA) was added dropwise, controlling the dropping rate to keep the system temperature below 70 °C. After the addition was complete, the reaction was maintained at this temperature, and the reaction was monitored by infrared spectroscopy at 2160 cm⁻¹. -1 The reaction stopped after the Si-H characteristic peaks disappeared completely. Low-boiling substances were removed under vacuum at 50°C to obtain a pale yellow, transparent, viscous liquid, namely methacrylate-terminated polymethylphenylsiloxane resin. The resin was tested and found to have a viscosity of 650 mPa•s and a ceramic yield of 78% under nitrogen at 1300°C (i.e., conversion equivalent coefficient K=0.78). (2) Slurry preparation and formulaic feeding: Set the target parameter: Let W T =30 portions, W P =20 parts; Based on the narrow temperature range sintering characteristics at 1375℃, the aluminum-rich liquid phase control coefficient α=1.24 and the silicon-rich liquid phase control coefficient β=1.88 are selected, and substituted into equation (Ⅰ) to calculate: W A =0.538×1.24×30=20.01 portions; Substitute into formula (II) to calculate: W S =(0.791×1.88-0.633)×30-0.78×20=(1.487-0.633)×30-15.6=25.62-15.6=10.02 portions; Weigh out the following components: 30 parts talc powder, 20 parts alumina powder, 10 parts silica powder, and 1 part methacrylate-terminated polymethylphenylsiloxane resin. First, place the photocurable polysiloxane resin, 1.5g photoinitiator TPO, and 1.0g dispersant BYK-111 in a beaker and mix them evenly with mechanical stirring. Then, add talc powder (800 mesh), alumina powder (γ phase, 50 nm), and fused silica powder (D). 50 =2μm); the mixture was transferred to a planetary ball mill and ball-milled at 300 rpm for 4 hours. After discharge, the material was degassed under vacuum to obtain a high-density cordierite ceramic slurry; (3) DLP printing: Pour the ink into the feed tank of the DLP printer and set the printing parameters: layer thickness 50μm, single-layer exposure time 8s, light intensity 10mW / cm². 2 Because the double bonds of photocurable polysiloxane resin are concentrated at the chain ends and there is no steric hindrance, the curing depth is excellent, and the green body with a smooth surface and no defects is printed. (4) Degreasing and sintering: The green body was placed in a muffle furnace and heated from room temperature to 600°C at a rate of 0.5°C / min and held for 2 hours. During this stage, the trace epoxy groups of the PSO side chains undergo thermal cross-linking to form a dense protective shell, ensuring that the gas generated by the decomposition of organic matter cannot accumulate and form pores. Subsequently, the temperature was increased to 1375°C at a rate of 2°C / min and held for 2 hours. At 1375°C, the silicon-rich liquid phase (β-controlled) designed in the formula promotes particle rearrangement, and the aluminum-rich liquid phase (α-controlled) provides support to prevent deformation. After cooling with the furnace, a high-density cordierite ceramic sample was obtained, denoted as X1.

[0025] Example 2 The difference from Example 1 is that it uses methacrylate-terminated polymethylphenylsiloxane resins with different repeating unit ratios. The specific synthesis steps are as follows: In a three-necked flask equipped with a condenser, 100 g of hydrogen-terminated polymethylphenylsiloxane (with a phenylsiloxane molar percentage of 25%, glycidyl etheroxypropylsiloxane molar percentage of 4%, Si-H bond molar concentration of 0.18 mol / 100 g, and viscosity of 850 mPa·s at 25 °C), 4.5 g of glycidyl etheroxypropylmethyldimethoxysilane, and 0.5 g of catalyst (Karstedt platinum catalyst, platinum content 3000 ppm) were added. Under nitrogen protection, the mixture was stirred at 80 °C for 2 hours to induce silanol condensation. The temperature was then lowered to 65 °C, and 20 g of allyl methacrylate (AMA) was added dropwise, controlling the dropping rate to keep the system temperature below 70 °C. After the addition was complete, the reaction was maintained at this temperature, and the reaction was monitored by infrared spectroscopy at 2160 cm⁻¹. -1The reaction stopped after the Si-H characteristic peaks completely disappeared. Low-boiling-point substances were removed under vacuum at 50℃ to obtain a pale yellow, transparent, viscous liquid. The resin viscosity was tested to be 850 mPa·s, and the ceramic yield at 1300℃ under nitrogen was 76% (i.e., conversion equivalent coefficient K = 0.76). When preparing the slurry, W... T =30 portions, W P =20 parts, α=1.24, β=1.88, calculate W using the formula. A =20.01 copies, W S =(0.791×1.88-0.633)×30-0.76×20=25.62-15.2=10.42 portions. The remaining process steps are the same as in Example 1. The obtained sample is denoted as X2.

[0026] Example 3 The only difference from Example 1 is that: W T =32 portions, W P =15 parts, α=1.29, β=1.74, calculate W using the formula. A =22.0 copies, W S =10.1 portions, the resulting sample is denoted as X3.

[0027] Example 4 The only difference from Example 1 is that 0.1 parts of yttrium fluoride, a sintering aid, were added in step (2). The resulting sample was denoted as X4.

[0028] Comparative Example 1 A method for preparing high-density cordierite ceramics includes the following steps: (1) Preparation of ceramic slurry: 40 parts of commercially available photosensitive polysiloxane (without epoxy side groups and phenyl links, ceramic yield approximately 45%), 1.5 parts of photoinitiator TPO, and 1.0 parts of dispersant BYK-111 were placed in a beaker and mechanically stirred until homogeneous. Then, 24 parts of talc powder (800 mesh) and 18 parts of alumina powder (γ phase, 50 nm) were added. The mixture was transferred to a planetary ball mill and ball-milled at 300 rpm for 4 hours. After discharge, the material was degassed under vacuum to obtain a high-density cordierite ceramic slurry. (2) DLP printing: Pour the ink into the feed tank of the DLP printer and set the printing parameters: layer thickness 50μm, single-layer exposure time 8s, light intensity 10mW / cm². 2 ; (3) Degreasing and sintering: The green body was placed in a muffle furnace and heated from room temperature to 600℃ at a rate of 0.5℃ / min and held for 2 hours; then, the temperature was increased to 1375℃ at a rate of 2℃ / min and held for 2 hours; after cooling in the furnace, a high-density cordierite ceramic sample was obtained, denoted as D1.

[0029] Comparative Example 2 The only difference from Example 1 is that the methacrylate-terminated polymethylphenylsiloxane resin is replaced with methacrylate-terminated polydimethylsiloxane without glycidoxypropyl side groups, while the rest of the composition and process are the same as in Example 1.

[0030] The general structural formula of the terminal methacrylate polydimethylsiloxane without glycidyl etheroxypropyl side groups is: (R1)3SiO-(R2SiO) x -Si(R1)3, where R1 is methacryloyloxypropyl (-C3H6OCOC(CH3)=CH2), R2 is phenyl (-C6H5, approximately 20 mol%) or methyl (-CH3, approximately 80 mol%), and x is the degree of polymerization of the siloxane chain segment. This resin can be visually represented as: CH2=C(CH3)COO-C3H6-Si(CH3)2O-[Si(CH3)(C6H5)O]m-[Si(CH3)2O]n-Si(CH3)2-C3H6OCOC(CH3)=CH2, where m / (m+n)≈20%. The ceramic yield of this resin at 1300℃ is approximately 72%. The obtained sample is designated D2.

[0031] Comparative Example 3 Cordierite ceramics were prepared using the traditional solid-state sintering method: talc powder, alumina powder and silica powder were mixed in stoichiometric ratio, PVA binder was added, the mixture was dry-pressed and then sintered at 1375℃ for 2 hours. The resulting sample was designated as D3.

[0032] Comparative Example 4 Using the same raw material ratio as in Example 1 (30 parts talc, 20 parts alumina, 10 parts silica, and 20 parts methacrylate-terminated polymethylphenylsiloxane resin), the methacrylate-terminated polymethylphenylsiloxane resin, 1.5 parts photoinitiator TPO, and 1.0 part dispersant BYK-111 were first mixed evenly. Then, talc, alumina, and fused silica powder were added, and the mixture was ball-milled at 300 rpm for 4 hours until homogeneous. After discharge, the mixture was degassed under vacuum to obtain a slurry. The slurry was poured into a mold and dry-pressed under a pressure of 5 MPa to obtain a green body. The green body was placed in a muffle furnace and heated to 600°C at 0.5°C / min and held for 2 hours, then heated to 1375°C at 2°C / min and held for 2 hours. After cooling in the furnace, a cordierite ceramic sample, designated D4, was obtained.

[0033] Performance testing: The apparent porosity and bulk density of the ceramic samples obtained in each embodiment and comparative example were tested (Archimedes' displacement method). The viscosity of the slurry was measured using a rotational viscometer at 25°C for 10 s. -1 The results were measured at the shear rate and are shown in Table 1.

[0034] Table 1 Ceramic Properties As shown in Table 1, the apparent porosity of the ceramics prepared in Examples 1-4 was controlled below 8%, and the bulk density was greater than 2.3 g / cm³. 3 This is significantly better than the comparative example. Furthermore, the slurry viscosity of Examples 1-4 remains within the suitable printing range of 1250-1550 mPa•s, balancing printing rheology and molding accuracy. Example 2 used a resin with a higher phenyl chain segment percentage (25%) and a higher epoxy chain segment percentage (4%), resulting in a slightly lower ceramic yield (76%) than Example 1 (78%), leading to a slight change in the compensation amount in formula (II). The results showed that the apparent porosity of Example 2 (7.2%) was comparable to that of Example 1 (7.8%), and the bulk density (2.36 g / cm³) was... 3 Slightly higher than Example 1 (2.32 g / cm³) 3 This indicates that appropriately increasing the proportion of epoxy chain segments can enhance the pre-crosslinking sealing effect and further reduce porosity formation. The slurry viscosity of Example 2 (1210 mPa·s) is slightly lower than that of Example 1 (1250 mPa·s). This is because the phenyl group has a large volume and a strong "internal plasticizing" effect, which can significantly reduce the resin viscosity. This example verifies that within the scope of protection of this invention, adjusting the resin chain segment ratio can also yield highly dense cordierite ceramics, proving the rationality of the PSO resin structural parameter range of this invention.

[0035] In Example 4, after adding a trace amount of yttrium fluoride sintering aid, the apparent porosity was further reduced to 5.9%, and the density increased to 2.41 g / cm³. 3 This demonstrates that the trace sintering aid and the aluminum-rich / silicon-rich liquid phase system in this invention have an excellent synergistic densification effect.

[0036] Comparative Example 1 uses commercially available PSO with high organic content and no pre-crosslinking mechanism, which forms a large number of macroscopic pores after pyrolysis, resulting in extremely low density.

[0037] A comparison between Comparative Example 2 and Example 1 shows that although Comparative Example 2 used a photosensitive resin with end groups and had the same phenyl repeating unit content, it lacked glycidyl etheroxypropyl side groups, thus failing to form a pre-crosslinked network to block pore channels in the early stages of degreasing. Its apparent porosity was significantly higher than that of Example 1, and its bulk density was also significantly lower. This strongly demonstrates that the pre-crosslinking and pore-sealing mechanism of PSO side-chain epoxy groups is one of the core elements for achieving high density.

[0038] Comparative Example 3 uses the traditional solid-state sintering method. Although it does not involve the decomposition and gas generation problem of the photocurable resin, its apparent porosity is lower than that of Comparative Examples 1 and 2, but still much higher than that of Examples 1-4. More importantly, the traditional dry pressing method cannot prepare complex shaped parts and does not have the molding flexibility of DLP 3D printing.

[0039] Comparative Example 4 used the exact same formulation as Example 1, but replaced DLP printing with dry pressing. Its apparent porosity was still significantly worse than that of Example 1, indicating that, under the same low-organic formulation, the uniform three-dimensional network formed by the photocuring of resin during DLP printing facilitates densification in the subsequent debinding and sintering stages, while the density achieved by dry pressing is far inferior to that of DLP printing. Furthermore, the slurry viscosity of Comparative Example 4 was 1350 mPa·s, higher than that of Example 1. This is because the low-viscosity PSO resin designed in Example 1, along with the formulated particle size distribution, synergistically optimized the rheological properties of the slurry. Even so, Comparative Example 4 still could not obtain a highly dense product through DLP printing, further highlighting the inseparable synergy between the specific structure of PSO, the formulated formulation, and DLP printing in this invention.

[0040] The above description is only a preferred embodiment of the present invention and is not intended to limit the present invention. Any modifications, equivalent substitutions, improvements, etc., made within the spirit and principles of the present invention should be included within the protection scope of the present invention.

Claims

1. A high-density cordierite ceramic slurry, characterized in that: The ceramic slurry is made from raw materials comprising the following parts by weight: 10-25 parts of methacrylate-terminated polymethylphenylsiloxane resin, 20-35 parts talcum powder 15-25 parts of alumina powder 5-15 parts of silica powder Photoinitiator 0.5-3 parts, Dispersant 0.1-2 parts.

2. The high-density cordierite ceramic slurry according to claim 1, characterized in that: The general structural formula of the terminal methacrylate-based polymethylphenylsiloxane resin is: (R1)3SiO-(R2SiO) x -(R3SiO) γ -Si(R1)3, wherein R1 is methacryloyloxypropyl, R2 is phenyl or methyl, R3 is glycidyl etheroxypropyl, and based on the total molar number of siloxane segments as 100%, the proportion of phenyl siloxane segments is 15-30%, the proportion of glycidyl etheroxypropyl siloxane segments is 2-5%, and the remainder is dimethyl siloxane segments; the ceramic yield of the terminal methacrylate-based polymethylphenyl siloxane resin at 800℃ is 75-80%.

3. The high-density cordierite ceramic slurry according to claim 2, characterized in that: The preparation method of the terminal methacrylate-based polymethylphenylsiloxane resin includes the following steps: mixing hydrogen-terminated polymethylphenylsiloxane, glycidyl etheroxypropylmethyldimethoxysilane and allyl methacrylate, adding a platinum catalyst, and carrying out hydrosilylation reaction and silanol condensation reaction. After the reaction is completed, the terminal methacrylate-based polymethylphenylsiloxane resin is obtained.

4. The high-density cordierite ceramic slurry according to claim 1, characterized in that: The weight proportions of the talc powder, alumina powder, silica powder, and methacrylate-terminated polymethylphenylsiloxane resin in the ceramic slurry satisfy the following formulas (I)-(II): W A =0.538×α×W T Equation (I) W S =(0.791×β-0.633)×W T -K×W P Formula (II) The weight parts of the talc powder are W. T The alumina powder has a weight ratio of W. A The silicon dioxide powder has a weight ratio of W. S The methacrylate-terminated polymethylphenylsiloxane resin described herein has a weight ratio of W. P ; α is the aluminum-rich liquid phase control coefficient, α=1.2-1.3; β is the silicon-rich liquid phase control coefficient, β=1.7-1.9; K is the equivalent coefficient of polysiloxane resin to SiO2, K=0.75-0.

80.

5. The high-density cordierite ceramic slurry according to claim 1, characterized in that: The ceramic slurry also includes a sintering aid, which is at least one of yttrium fluoride or potassium fluorozirconate.

6. The high-density cordierite ceramic slurry according to claim 1, characterized in that: The silica powder is at least one of fused silica powder or cristobalite powder; the particle size D of the silica powder is... 50 It is 0.5-5 μm.

7. The high-density cordierite ceramic slurry according to claim 1, characterized in that: The ceramic slurry has an apparent porosity of less than 8% and a bulk density greater than 2.3 g / cm³. 3 .

8. The method for preparing the high-density cordierite ceramic slurry according to any one of claims 1-7, characterized in that: The process includes the following steps: First, a methacrylate-terminated polymethylphenylsiloxane resin, a photoinitiator, and a dispersant are mixed evenly. Then, talc powder, alumina powder, silica powder, and a sintering aid are added to the mixture. After ball milling and degassing, the high-density cordierite ceramic slurry is obtained. The ball milling step is performed at a speed of 200-400 rpm for 2-6 hours.

9. A method for preparing high-density cordierite ceramics using the ceramic slurry according to any one of claims 1-7, characterized in that: Includes the following steps: (1) The ceramic slurry is photocured and 3D printed to obtain a green body; (2) The green body is degreased and sintered to obtain the high-density cordierite ceramic.

10. The method for preparing high-density cordierite ceramics according to claim 9, characterized in that: In step (1), the photopolymer 3D printing layer thickness is 20-100 μm, the single-layer exposure time is 5-30 s, and the exposure energy is 10-50 mJ / cm². 2 The degreasing and sintering steps in step (2) are as follows: the temperature is raised to 600℃ at a rate of 0.5-3℃ / min and held at that temperature to complete the degreasing, and then the temperature is raised to 1370-1380℃ at a rate of 1-3℃ / min and held at that temperature for 1-3 hours.

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