High-simulation and high-performance stone-imitating bright ceramic tile and preparation method thereof

Abstract

The invention discloses a high-simulation and high-performance stone-imitating bright ceramic tile which sequentially comprises a high-strength green body layer, a functional ground glaze layer, a multi-mode digital texture layer, an interface strengthening-optical adaptation transition layer and a high-transmittance protective glaze layer from bottom to top. The raw materials of the high-strength green body layer comprise spodumene tailing powder and a compound of zirconium silicate and zinc oxide serving as a sintering aid, the water absorption rate is smaller than or equal to 0.2% after sintering, the fracture modulus is larger than or equal to 42 MPa, the high-strength green body layer is covered with the functional ground coat layer, and the raw materials of the functional ground coat layer comprise a porous forming agent and active components capable of reacting with follow-up ink. According to the invention, through multi-modal data acquisition and morphology channel printing, full-dimensional physical recarving of natural stone from macroscopic color veins to micro-crystal fluctuations is realized, and high-refractive-index ink and an interface strengthening-optical adaptation transition layer are combined, so that the appearance of the natural stone is enhanced. The product can present the specific deep feeling, moist feeling and mineral crystal flash of natural stone under any illumination, and the vivid degree which is difficult to distinguish by naked eyes is achieved.

Description

A high-simulation, high-performance stone-look glossy ceramic tile and its preparation method Technical Field

[0001] This invention relates to the field of building decoration materials technology, and in particular to a high-simulation, high-performance imitation stone glossy ceramic tile and its preparation method. Background Technology

[0002] Natural stone, with its unique texture, warm feel, and luxurious luster, has long been regarded as a core material for high-end architectural decoration. However, its inherent defects severely limit its application and development: First, the mining of non-renewable minerals causes permanent damage to the ecological environment, which is inconsistent with the global consensus on sustainable development; second, in order to achieve the high brightness and high transparency required by the market, most natural stone needs to undergo secondary processing such as glue injection, wax injection, and polishing. This process will continuously release harmful gases such as formaldehyde and benzene compounds, posing a health hazard to the indoor environment; third, natural stone itself has shortcomings in physical properties, such as low strength, high brittleness, high water absorption, and susceptibility to freeze-thaw weathering, and some varieties are radioactive, making it unsuitable for use in places with stringent requirements such as underfloor heating, high-rise curtain walls, hospitals, and laboratories.

[0003] To replace natural stone, stone-look ceramic tiles have become a key focus of industry research and development. To closely resemble the effect of natural stone, current stone-look technology mainly achieves this through the following approaches: 1) Physical texture simulation: Early technologies focused on simulating the mineral grain texture and macroscopic color differences of natural stone. Representative methods include mixing decorative particles of different colors, such as microcrystalline glass particles, into the tile blank powder, or pressing multiple layers of different colored blank powder together to form random, interwoven color bands and particles within the tile body. While such technologies can mimic the rough texture of granite and other stones to some extent, their simulation is extremely low for luxury stones such as marble and jade, which have continuous, flowing, and delicate textures. The patterns are stiff, repetitive, and lack natural charm. 2) Surface glazing and printing: With the popularization of inkjet printing technology, stone imitation technology has entered a stage focused on surface decoration. Its core logic is to build texture and feel by applying a base glaze, inkjet printing patterns, and then covering functional glazes on the base tile blank. This is the current mainstream technology. 3) Body strengthening: This mainly focuses on improving the physical properties of ceramic tiles. By adjusting the mineral composition and chemical ratio of the base raw materials of the body and optimizing the corresponding preparation and sintering processes, it makes the tiles surpass natural stone in strength, stability, and durability.

[0004] Due to the lack of effective system integration among the aforementioned technical approaches, each technology often develops independently, failing to achieve a perfect unity of texture simulation, surface texture shaping, and overall body performance. Surface decoration technologies pursuing highly realistic textures are often incompatible with material and process systems aimed at improving the physical properties of the body, making it difficult to achieve a balance between aesthetic appeal and physical durability. Conversely, surface glazing technologies aimed at enhancing three-dimensionality and special gloss may affect texture clarity or sacrifice some key properties of the substrate. Therefore, the market urgently needs a technical solution that enables global collaborative innovation from material systems and process logic to product design to systematically resolve these contradictions, thereby producing a new generation of stone-like ceramic tile products that can comprehensively replace and surpass natural stone in terms of visual effects, physical performance, and environmental safety. Summary of the Invention

[0005] The purpose of this invention is to provide a highly realistic, high-performance imitation stone ceramic tile and its preparation method, which can accurately replicate the charm of natural stone and surpass natural stone in all physical and chemical properties.

[0006] To achieve the above objectives, the present invention provides the following technical solution: a high-simulation, high-performance imitation stone glossy ceramic tile, comprising, from bottom to top, a high-strength body layer, a functional base glaze layer, a multimodal digital texture layer, an interface-strengthened-optical-adaptive transition layer, and a high-transparency protective glaze layer. The high-strength body layer contains spodumene tailings powder and a composite of zirconium silicate and zinc oxide as a sintering aid. After firing, its water absorption rate is ≤0.2%, and its modulus of rupture is ≥42MPa. The functional base glaze layer covers the high-strength body layer, and its raw materials include a pore-forming agent and active components that can react with subsequent inks. The surface of the functional base glaze layer has a microporous structure with an average pore size of 0.5-5μm and a porosity of 5-15. The multimodal digital texture layer is printed on the functional base glaze layer and contains color information and micro-topological structure reconstructed based on the fusion of three-dimensional morphology and spectral data of natural stone. The micro-topological structure is formed by the local stacking of high refractive index functional inks, and the surface roughness Ra is 0.5-10μm. The interface strengthening-optical adaptation transition layer is located on the multimodal digital texture layer. It is an intermediate layer formed in situ during the firing process with a continuous gradient change in composition and structure. The high-transparency protective glaze layer is located on the outermost layer of the ceramic tile. Its raw materials include low-melting-point high-refractive-index glass powder. The glass powder is borosilicate glass containing barium oxide and titanium oxide. After firing, the visible light transmittance is not less than 90%, and the glaze surface Mohs hardness is ≥7.

[0007] The introduction of spodumene tailings powder not only reduces raw material costs, but more importantly, the lithium element it contains can play a strong role in fluxing and mineralizing at high temperatures, promoting full densification of the green body at a relatively low firing temperature, reducing energy consumption and inhibiting excessive grain growth.

[0008] Furthermore, the high-strength blank layer comprises, by weight percentage of the total raw materials: 20-28% high-plasticity clay, 25-35% quartz, 12-20% calcined bauxite, 5-10% spodumene tailings powder, and 3-6% nano-zirconium silicate-zinc oxide composite powder. The weight ratio of zirconium silicate to zinc oxide in the nano-zirconium silicate-zinc oxide composite powder is (1.5-4):1, and the average particle size D50 of the nano-zirconium silicate-zinc oxide composite powder is less than 100 nanometers.

[0009] The ratio and average particle size of nano-zirconium silicate and zinc oxide nanocomposite powders are limited to achieve nano-sintering and functional compositing of sintering aids. The nano-sized particles (D50<100nm) ensure high surface activity and uniform dispersion in the green body, significantly reducing the sintering activation energy. The specific ratio range ((1.5-4):1) enables the best synergy between the effects of zirconium silicate (improving strength and stability) and zinc oxide (promoting sintering and toughening), which together promote the development and interweaving of needle-like mullite crystals at high temperatures, thereby obtaining an ultra-high strength and ultra-low absorption green body with "water absorption ≤0.2% and fracture modulus ≥42MPa".

[0010] Furthermore, the functional base glaze layer comprises, by weight percentage of the total raw materials: 40-55% potassium feldspar, 15-25% quartz, 10-20% kaolin, 3-8% pore-forming agent, and 2-6% active component. The pore-forming agent is at least one of calcium carbonate, magnesium carbonate, or polymethyl methacrylate microspheres, and the active component is at least one of nano zinc oxide or nano cerium oxide.

[0011] Furthermore, the refractive index of the high refractive index functional ink is not less than 1.70.

[0012] Furthermore, the high-transparency protective glaze layer comprises, by weight percentage of the total raw materials: 15-30% borosilicate glass powder containing barium oxide and titanium oxide, 5-15% nano-alumina, 10-25% quartz, 20-30% potassium feldspar, 5-10% kaolin, and 3-8% calcium carbonate, wherein the content of barium oxide in the borosilicate glass powder containing barium oxide and titanium oxide is 5-15 wt%, and the content of titanium oxide is 2-8 wt%.

[0013] Nano-alumina, as a reinforcing phase, is uniformly dispersed in the molten glaze glass, significantly improving the microhardness and wear resistance of the glaze surface. This is key to achieving a Mohs hardness of ≥7 for the glaze, without affecting the transparency of the glaze layer. Barium oxide effectively reduces the high-temperature viscosity of the glass phase, giving it excellent leveling properties at specific firing temperatures, while also possessing a high refractive index. Titanium oxide is a powerful refractive index enhancer and strengthens the chemical stability of the glaze layer. The combination of these two components in the borosilicate glass system gives the glaze powder both a low melting point (facilitating co-firing with the underlying layer) and a high refractive index.

[0014] This invention also provides a method for preparing highly realistic, high-performance stone-look ceramic tile, comprising the following steps: S1. Multimodal digital model generation: collecting microscopic three-dimensional morphology data and multispectral data of natural stone samples, and generating a multimodal digital model containing independent color channel printing files and morphology channel printing files through algorithm fusion, providing a data foundation for physical-level simulation; S2. Green body preparation: preparing green body powder according to the raw material ratio of the high-strength green body layer, wet ball milling to a fineness of ≤0.3% on a 10,000-pore sieve, spray granulation, and pressing into shape under a pressure of 35-45MPa through a mold to obtain the green body, i.e., the high-strength green body layer; S3. Functional base glaze slurry preparation: weighing each component according to the raw material ratio of the functional base glaze layer, mixing, adding water and electrolyte, and wet ball milling until the fineness reaches ≤0.5% on a 10,000-pore sieve, producing a specific gravity of 1.65-1.75 g / cm³. 3 S4. Functional base glaze slurry; Application and pre-firing of functional base glaze: Apply functional base glaze slurry to the surface of the body, with an application amount of 80-120 g / m². 2 The mixture is then pre-fired at 300-450℃ to form a functional base glaze layer with a microporous structure. Pre-firing decomposes or burns the pore-forming agent, constructing a uniform microporous structure with an average pore size of 0.5-5μm and a porosity of 5-15% within the functional base glaze layer. These micropores significantly increase the specific surface area of ​​the functional base glaze layer, providing strong physical anchoring points for subsequent inkjet printing, effectively preventing ink diffusion and ensuring the sharpness of the printed texture. The active components (nano zinc oxide, nano cerium oxide) can undergo a controllable interfacial chemical reaction with the ink components (especially high-refractive-index functional inks) in the digital texture layer during the subsequent high-temperature firing stage. This reaction is the chemical driving force that enables the interface strengthening-optical adaptation transition layer to "form in situ" and achieve a chemical composition gradient, fundamentally strengthening the interlayer bonding force.

[0015] S5. Multi-channel digital inkjet printing: The color channel file and morphology channel file generated in step S1 are simultaneously input into an industrial inkjet printer. A multi-channel ink system containing at least C, M, Y, K, W and one high-refractive-index functional ink is used to print on the pre-fired functional base glaze layer to form a multimodal digital texture layer. The morphology channel file controls the stacking of ink droplets of high-refractive-index functional ink in a preset area to form micro-undulations. Using the morphology channel file, the high-refractive-index ink is precisely stacked at the micrometer level (Ra 0.5-10μm) in the corresponding area. This is equivalent to pre-constructing physical undulations corresponding to the microstructure of the stone surface on a two-dimensional plane. The selection of high-refractive-index ink (refractive index ≥1.70) aims to make its optical properties after firing closer to natural mineral crystals, laying the foundation for the subsequent generation of three-dimensional optical effects.

[0016] S6. Application of High-Transparency Protective Glaze: Prepare a high-transparency protective glaze according to the raw material ratio of the high-transparency protective glaze layer, ball mill it until the residue on a 10,000-mesh sieve is ≤0.05%, and adjust it to a specific gravity of 1.82-1.88 g / cm³. 3 The glaze slurry is then evenly applied to the surface of the printed blank, with an application rate of 200-250 g / m². 2 This process forms a highly transparent protective glaze layer; the grinding fineness is ≤0.05% on a 10,000-pore sieve, ensuring that all components of the glaze are highly uniform and can melt quickly and completely during firing, forming an extremely smooth and transparent glassy surface without bubbles or impurities. This is the process guarantee for achieving a visible light transmittance of not less than 90%.

[0017] S7. Dynamic Response Gradient Firing: The glazed body is placed in a roller kiln and the following staged temperature-controlled firing process is executed: a) Dehydration and Pre-oxidation Stage: Starting from room temperature, the temperature is increased to 450℃ at a rate of 60-80℃ / h. During this process, the physically bound water and organic matter in the body and glaze layer are fully discharged to prevent cracking; b) Vitrification-Interface Reaction Stage: The temperature is increased from 450℃ to the initial melting temperature T1 of the high-transparency protective glaze at a rate of 120-150℃ / h to promote the initial vitrification of the body and initiate the initial interface reaction between the functional base glaze layer and the digital texture layer; The initial melting temperature T1 of the high-transparency protective glaze, ranging from 850-1050℃, is a dynamic process inflection point. Its specific value depends on the specific type and content of glass powder, flux, etc. in the glaze. Usually, the glaze is made into test strips and measured by thermal expansion method using a high-temperature thermal expansion instrument or high-temperature microscope.

[0018] c) Melting-Densification Main Reaction Stage: The temperature is increased from the initial melting temperature T1 of the high-transparency protective glaze to the maximum firing temperature Tmax at a rate of 80-100℃ / h. The maximum firing temperature Tmax is 1220-1260℃, and the holding time is t. This allows the glaze to completely melt and the body to become highly densified. An interface strengthening-optical adaptation transition layer is generated in situ between the multimodal digital texture layer and the high-transparency protective glaze layer. The generation process of the interface strengthening-optical adaptation transition layer: At high temperature, the active components (nano zinc oxide or nano cerium oxide) in the functional base glaze layer migrate first and undergo a preliminary interface chemical reaction with the ink of the multimodal digital texture layer, forming an extremely thin interpenetration reaction zone, which lays the foundation for subsequent reactions. When the temperature reaches the initial melting temperature T1 of the high-transparency protective glaze, the glaze melts to form a highly active liquid phase. This melt penetrates downwards, dissolving the substances on the surface of the multimodal digital texture layer on the one hand, and undergoing a violent chemical reaction and bidirectional ion diffusion with the active components of the functional base glaze layer on the other hand. Under prolonged high-temperature insulation (the insulation time t is calculated using the formula t=k×d, ranging from 40 to 70 minutes), the concentrations of each component (such as SiO2, Al2O3, ZnO, BaO) form a continuous and smooth gradient distribution in the vertical direction, rather than an abrupt interface. During slow cooling, this gradient component structure is frozen and solidified, forming a unique glass-microcrystalline composite transition layer. The continuous component gradient eliminates clear physical interfaces and thermal stress concentration, achieving strong adhesion and fundamentally solving the risk of glaze cracking. The continuously changing refractive index minimizes the scattering loss of light when passing through the interlayer, allowing most of the light to penetrate deep into the interior and be reflected by the texture, thus presenting the transparency and luster of natural stone, rather than surface glare. This layer is an in-situ self-generated structure that is inevitably produced through high-temperature liquid phase reaction and diffusion.

[0019] d) Controlled cooling stage: After firing, the billet is rapidly cooled at a rate of 100-120℃ / h in a temperature range above 700℃ to suppress grain coarsening, and then slowly cooled in a temperature range below 700℃ until it leaves the kiln to avoid thermal stress cracking.

[0020] S8. Post-processing: After firing, the ceramic tiles undergo cold processing to obtain the finished product.

[0021] Furthermore, in step S5, the inkjet printing resolution is not less than 1200 dpi.

[0022] Furthermore, in step S7, the heat preservation time t and the thickness d of the ceramic tile body after molding satisfy the following relationship: t=k×d, where the heat preservation time t is in minutes, the thickness d is in millimeters, and k is a proportionality coefficient with a value range of 3-5 minutes / millimeter. The heat preservation time t of products with different thicknesses is calculated using this formula to ensure that products with different thicknesses can obtain a sufficiently consistent degree of sintering and performance.

[0023] Compared with the prior art, the beneficial effects of the present invention are: 1. The present invention achieves a full-dimensional physical replication of natural stone from macroscopic color veins to microscopic crystal undulations through multimodal data acquisition and morphology channel printing. Combined with high refractive index ink and interface strengthening-optical adaptation transition layer, the product can present the unique depth, luster and mineral crystal shimmer of natural stone under any lighting conditions, achieving a level of realism that is difficult to distinguish with the naked eye.

[0024] 2. The products produced by this invention have advantages such as high strength (modulus of rupture ≥42MPa), low water absorption (≤0.2%), high surface hardness (≥7 grade), excellent thermal stability and chemical corrosion resistance. Their performance indicators not only far exceed those of natural stones such as marble and granite, but also significantly exceed those of existing ordinary imitation stone ceramic tiles. They can be safely used in places with strict material requirements, such as underfloor heating systems, high-rise building curtain walls, hospitals, and laboratories.

[0025] 3. This invention, through a functional base glaze layer and a dynamic response gradient firing process, successfully constructs an in-situ generated interface strengthening-optical adaptation transition layer between the multimodal digital texture layer and the high-transparency protective glaze layer. This fundamentally solves the core contradiction in traditional technologies, namely, the poor bonding between high-strength body and decorative layer, and the difficulty in balancing high-simulation decoration and high-performance substrate, thus achieving a perfect unity of aesthetics and mechanics.

[0026] 4. This invention introduces spodumene tailings powder, realizing the resource utilization of solid waste. At the same time, the entire production process does not require secondary processing of the product such as glue or waxing as natural stone, thus eliminating the introduction of indoor pollutants such as formaldehyde and benzene from the source. The product itself has no radioactive hazards and is a green and healthy decorative material. Detailed Implementation

[0027] To make the technical problems solved, technical solutions, and beneficial effects of the present invention clearer, the present invention will be further described in detail below with reference to embodiments. It should be understood that the specific embodiments described herein are merely illustrative of the invention and are not intended to limit the invention. Embodiments

[0028] A high-simulation, high-performance stone-look ceramic tile comprises, from bottom to top, a high-strength body layer, a functional base glaze layer, a multimodal digital texture layer, an interface-strengthening-optical adaptation transition layer, and a high-transparency protective glaze layer. The functional base glaze layer covers the high-strength body layer and has a microporous structure with an average pore size of 0.5-5μm and a porosity of 5-15%. The multimodal digital texture layer is printed on the functional base glaze layer and contains color information and micro-topological structure reconstructed based on the fusion of three-dimensional morphology and spectral data of natural stone. The micro-topological structure is formed by the local stacking of high-refractive-index functional inks and has a surface roughness Ra of 0.5-10μm. The interface-strengthening-optical adaptation transition layer is located on the multimodal digital texture layer and is an intermediate layer formed in situ during the firing process with a continuous gradient change in composition and structure. The high-transparency protective glaze layer is located on the outermost layer of the ceramic tile.

[0029] The method for preparing this ceramic tile includes the following steps: S1. Multimodal digital model generation: Collecting microscopic three-dimensional morphological data and multispectral data of natural stone samples, and generating a multimodal digital model containing independent color channel printing files and morphological channel printing files through algorithm fusion; S2. Green body preparation: Preparing green body powder according to the raw material ratio of the high-strength green body layer, wet ball milling to a fineness of 0.25% residue on a 10,000-mesh sieve, then spray granulation, and pressing it into shape under a pressure of 40MPa through a mold to obtain the green body, i.e., the high-strength green body layer; the raw material ratio of the high-strength green body layer (based on the total weight of raw materials) (By proportion): 25% high-plasticity clay, 30% quartz, 16% calcined bauxite, 8% spodumene tailings powder, and 4.5% nano-zirconium silicate-zinc oxide composite powder. The weight ratio of zirconium silicate to zinc oxide in the nano-zirconium silicate-zinc oxide composite powder is 2.5:1, and the average particle size D50 of the nano-zirconium silicate-zinc oxide composite powder is equal to 100 nanometers; S3. Preparation of functional base glaze slurry: Weigh each component according to the raw material ratio of the functional base glaze layer, mix them, add water and electrolyte, and perform wet ball milling until the fineness reaches 0.45% residue on a 10,000-mesh sieve, resulting in a specific gravity of 1.70 g / cm³. 3 Functional base glaze slurry; Raw material ratio of functional base glaze layer (by total weight percentage of raw materials): potassium feldspar 50%, quartz 20%, kaolin 15%, pore-forming agent 6%, active component 4.5%, the pore-forming agent is calcium carbonate, and the active component is nano zinc oxide; S4. Application and pre-firing of functional base glaze: Apply functional base glaze slurry to the surface of the body, the application amount is 100g / m 2Then, it is pre-fired at 380℃ for 20 minutes to form a functional base glaze layer with a microporous structure; S5. Multi-channel digital inkjet printing: The color channel file and morphology channel file generated in step S1 are simultaneously input into an industrial inkjet printer. A multi-channel ink system (eight-color inkjet printer, printing resolution 1200dpi) containing at least C, M, Y, K, W and one high refractive index functional ink (refractive index 1.75) is used to print on the pre-fired functional base glaze layer to form a multimodal digital texture layer. The morphology channel file controls the high refractive index functional ink to be stacked in small amounts at the edges of simulated crystal lines and cloud patterns to form micro-undulations; S6. Application of high-transparency protective glaze: A high-transparency protective glaze is prepared according to the raw material ratio of the high-transparency protective glaze layer, ball-milled to a fineness of 0.04% residue on a 10,000-pore sieve, and adjusted to a specific gravity of 1.85 g / cm³. 3 The glaze slurry is then evenly applied to the surface of the printed blank at a rate of 220g / m². 2 A high-transparency protective glaze layer is formed; the raw material ratio of the high-transparency protective glaze layer (by total weight percentage of raw materials): 22% borosilicate glass powder containing barium oxide and titanium oxide, 10% nano-alumina, 20% quartz, 25% potassium feldspar, 8% kaolin, and 5% calcium carbonate. In the borosilicate glass powder containing barium oxide and titanium oxide, the content of barium oxide is 10wt% and the content of titanium oxide is 5wt%; S7. Dynamic response gradient firing: The glazed body is placed in a roller kiln and the following staged temperature-controlled firing process is executed: a) Dehydration and pre-oxidation stage: Starting from room temperature, the temperature is increased to 450℃ at a rate of 70℃ / h; b) Vitrification-interface reaction stage: The temperature is increased from 450℃ to the initial melting temperature T1 (1020℃) of the high-transparency protective glaze at a rate of 1350℃ / h. This temperature value was determined experimentally. c) Melting-Densification Main Reaction Stage: The temperature is raised from the initial melting temperature T1 (1020℃) of the high-transparency protective glaze to the maximum firing temperature Tmax at a rate of 90℃ / h. The maximum firing temperature Tmax is 1240℃, and the holding time is 48 minutes, so that the glaze is completely melted, the body is highly densified, and an interface strengthening-optical adaptation transition layer is generated in situ between the multimodal digital texture layer and the high-transparency protective glaze layer. The holding time t at the maximum firing temperature Tmax and the thickness d of the body after the tile is formed satisfy the following relationship: t=k×d, where the unit of the holding time t is minutes, the unit of the body thickness d is millimeters, and k is a proportionality coefficient with a value range of 3-5 minutes / mm. In this embodiment, the body thickness d=12, k=4, and the holding time t=4×12=48 minutes.

[0030] d) Controlled cooling stage: After firing, the green body is rapidly cooled at a rate of 110℃ / h in a temperature zone above 700℃, and then slowly cooled in a temperature zone below 700℃ until it is removed from the kiln.

[0031] S8. Post-processing: After firing, the tiles undergo edge grinding and chamfering to obtain the finished product. Finished product testing parameters are shown in the table below:

[0032] Test results show that the product of this invention can not only accurately replicate the unique depth and luster of natural stone with extremely high simulation, but also outperform existing technology products in terms of strength, hardness, and thermal shock stability.

[0033] Although embodiments of the invention have been shown and described, it will be understood by those skilled in the art that various changes, modifications, substitutions and alterations can be made to these embodiments without departing from the principles and spirit of the invention, the scope of which is defined by the appended claims and their equivalents.

Claims

1. A high-simulation, high-performance stone-look glossy ceramic tile, characterized in that, From bottom to top, the layers consist of a high-strength body layer, a functional base glaze layer, a multimodal digital texture layer, an interface-strengthening-optical adaptation transition layer, and a high-transparency protective glaze layer. The high-strength body layer contains spodumene tailings powder and a composite of zirconium silicate and zinc oxide as a sintering aid. After firing, it has a water absorption rate ≤0.2% and a rupture modulus ≥42MPa. The functional base glaze layer covers the high-strength body layer and contains a pore-forming agent and active components that react with subsequent inks. The surface of the functional base glaze layer has a microporous structure with an average pore size of 0.5-5μm and a porosity of 5-15%. The multimodal digital texture layer is printed on the functional base glaze layer. Above the glaze layer, there is color information and microscopic topology reconstructed based on the fusion of three-dimensional morphology and spectral data of natural stone. The microscopic topology is formed by the local stacking of high refractive index functional inks, with a surface roughness Ra of 0.5-10μm. The interface strengthening-optical adaptation transition layer is located above the multimodal digital texture layer. It is an intermediate layer formed in situ during the firing process, with a continuous gradient change in composition and structure. The high-transparency protective glaze layer is located on the outermost layer of the ceramic tile. Its raw materials include low-melting-point high-refractive-index glass powder. The glass powder is borosilicate glass containing barium oxide and titanium oxide. After firing, the visible light transmittance is not less than 90%, and the glaze surface has a Mohs hardness of ≥7.

2. The high-simulation, high-performance stone-look ceramic tile according to claim 1, characterized in that, The high-strength blank layer comprises, by weight percentage of the total raw materials: 20-28% high-plasticity clay, 25-35% quartz, 12-20% calcined bauxite, 5-10% spodumene tailings powder, and 3-6% nano-zirconium silicate-zinc oxide composite powder. The weight ratio of zirconium silicate to zinc oxide in the nano-zirconium silicate-zinc oxide composite powder is (1.5-4):1, and the average particle size D50 of the nano-zirconium silicate-zinc oxide composite powder is less than 100 nanometers.

3. The high-simulation, high-performance imitation stone glossy ceramic tile according to claim 1, characterized in that, The functional base glaze layer, by weight percentage of the total raw materials, comprises: 40-55% potassium feldspar, 15-25% quartz, 10-20% kaolin, 3-8% pore-forming agent, and 2-6% active component. The pore-forming agent is at least one of calcium carbonate, magnesium carbonate, or polymethyl methacrylate microspheres, and the active component is at least one of nano zinc oxide or nano cerium oxide.

4. The high-simulation, high-performance stone-look ceramic tile according to claim 1, characterized in that, The refractive index of the high refractive index functional ink is not less than 1.

70.

5. A high-simulation, high-performance imitation stone glossy ceramic tile according to claim 1, characterized in that, The high-transparency protective glaze layer comprises, by weight percentage of the total raw materials: 15-30% borosilicate glass powder containing barium oxide and titanium oxide, 5-15% nano-alumina, 10-25% quartz, 20-30% potassium feldspar, 5-10% kaolin, and 3-8% calcium carbonate. Among these, the barium oxide content in the borosilicate glass powder containing barium oxide and titanium oxide is 5-15 wt%, and the titanium oxide content is 2-8 wt%.

6. A method for preparing a high-simulation, high-performance imitation stone glossy ceramic tile as described in any one of claims 1-5, characterized in that, Includes the following steps: S1. Multimodal Digital Model Generation: Microscopic three-dimensional morphology data and multispectral data of natural stone samples are collected and fused using algorithms to generate a multimodal digital model containing independent color channel and morphology channel print files. S2. Green Body Preparation: Green body powder is prepared according to the raw material ratio of the high-strength green body layer. After wet ball milling to a fineness of ≤0.3% on a 10,000-pore sieve, it is spray-granulated and pressed into shape using a mold under a pressure of 35-45 MPa to obtain the green body, i.e., the high-strength green body layer. S3. Functional Base Glaze Slurry Preparation: The components are weighed according to the raw material ratio of the functional base glaze layer, mixed, and then water and electrolyte are added for wet ball milling until the fineness reaches ≤0.5% on a 10,000-pore sieve, resulting in a specific gravity of 1.65-1.75 g / cm³. 3 S4. Functional base glaze slurry; Application and pre-firing of functional base glaze: Apply functional base glaze slurry to the surface of the body, with an application amount of 80-120 g / m². 2 Then, it is pre-fired at 300-450℃ to form a functional base glaze layer with a microporous structure; S5. Multi-channel digital inkjet printing: The color channel file and the morphology channel file generated in step S1 are simultaneously input into an industrial inkjet printer, and a multi-channel ink system containing at least C, M, Y, K, W and a high refractive index functional ink is used to print on the pre-fired functional base glaze layer to form a multimodal digital texture layer, wherein the morphology channel file controls the stacking of ink droplets of high refractive index functional ink in a preset area to form micro-undulations; S6. Application of High-Transparency Protective Glaze: Prepare a high-transparency protective glaze according to the raw material ratio of the high-transparency protective glaze layer, ball mill it until the residue on a 10,000-mesh sieve is ≤0.05%, and adjust it to a specific gravity of 1.82-1.88 g / cm³. 3 The glaze slurry is then evenly applied to the surface of the printed blank, with an application rate of 200-250 g / m². 2 To form a high-transparency protective glaze layer; S7. Dynamic response gradient firing: Place the glazed body in a roller kiln and execute the following staged temperature-controlled firing process: a) Dehydration and pre-oxidation stage: Starting from room temperature, raise the temperature to 450℃ at a rate of 60-80℃ / h; b) Vitrification-interface reaction stage: Raise the temperature from 450℃ to the initial melting temperature T1 of the high-transparency protective glaze at a rate of 120-150℃ / h; c) Melting-leveling-densification main reaction stage: At a rate of 8 The temperature is increased from the initial melting temperature T1 of the high-transparency protective glaze to the maximum firing temperature Tmax at a rate of 0-100℃ / h, where the maximum firing temperature Tmax is 1220-1260℃, and the holding time is t, so that the glaze is completely melted, the body is highly densified, and an interface strengthening-optical adaptation transition layer is generated in situ between the multimodal digital texture layer and the high-transparency protective glaze layer; d) Controlled cooling stage: After firing, the body is rapidly cooled at a rate of 100-120℃ / h in a temperature range above 700℃, and then slowly cooled in a temperature range below 700℃ until it is removed from the kiln; S8. Post-processing: After firing, the ceramic tile is cold-processed to obtain the finished product.

7. The preparation method according to claim 6, characterized in that, In step S5, the inkjet printing resolution is not less than 1200 dpi.

8. The preparation method according to claim 6, characterized in that, In step S7, the heat preservation time t and the thickness d of the ceramic tile body after molding satisfy the following relationship: t=k×d, where the heat preservation time t is in minutes, the thickness d is in millimeters, and k is a proportionality coefficient with a value range of 3-5 minutes / millimeter.

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