Bright ceramic tile with anti-skid and anti-fouling properties and preparation method thereof

Abstract

The present application relates to the technical field of building ceramics, and particularly relates to a bright ceramic tile with antiskid and antifouling properties and a preparation method thereof, comprising the following steps: A. applying a base glaze to the surface of a body layer to form a base glaze layer; B. spraying engraved dry particles to the surface of the base glaze layer to obtain an engraved dry particle layer; C. applying a protective glaze to the surface of the engraved dry particle layer to obtain a protective glaze layer; D. drying and then entering a kiln for calcination, and polishing to obtain the bright ceramic tile with antiskid and antifouling properties; wherein the bright ceramic tile with antiskid and antifouling properties has holes, and the holes are formed by the inner core particles and the bridging layer of the engraved dry particles falling off. The bright ceramic tile with antiskid and antifouling properties and the preparation method thereof are beneficial to ensuring the bright effect and also having good antiskid and antifouling properties, so as to overcome the shortcomings in the prior art.

Description

Technical Field

[0001] This invention relates to the field of building ceramics technology, and in particular to a glossy ceramic tile with anti-slip and anti-fouling properties and its preparation method. Background Technology

[0002] Glossy ceramic tiles, as an important decorative material for everyday homes, are highly favored by consumers for their mirror-like gloss, luxurious and grand visual appeal, high-temperature resistance, and rich glaze colors. They are widely used in home decoration, commercial spaces, and cultural tourism scenic areas. With the development of technology and the improvement of people's living standards, people have increasingly higher requirements for the quality of life, which means that in addition to stain resistance, glossy ceramic tiles also need to have a certain degree of slip resistance.

[0003] To achieve both slip resistance and stain resistance in glossy ceramic tiles, a typical approach in existing technologies involves applying a protective glaze to the surface of the tile and then adding a high-temperature dry granule anti-slip and stain-resistant glaze (wherein the ball-milled high-temperature dry granules have a smooth surface). Specifically, this method involves mixing high-temperature dry granules with a protective glaze and ball-milling with water to obtain the anti-slip and stain-resistant glaze. After firing, the dry granules protrude from the glaze surface, utilizing their slight undulations to achieve slip resistance through mechanical interlocking with the sole of a shoe. Simultaneously, the formation principle of the high-temperature dry granules with a smooth surface is similar to the mechanism by which pebbles in flowing water form a smooth surface, making it difficult for stains to accumulate on the surface of the high-temperature dry granules, thus obtaining a glossy ceramic tile that simultaneously possesses anti-slip and stain-resistant properties.

[0004] However, the above process has the following drawbacks: During the overall ball milling of the anti-slip and anti-fouling glaze, the high-temperature dry particles are prone to breakage. These broken high-temperature dry particles (high-melting-point components) mix into the protective glaze (low-melting-point matrix). Furthermore, as a high-melting-point heterogeneous component, the broken high-temperature dry particles easily increase the initial melting temperature and firing temperature of the overall anti-slip and anti-fouling glaze. This prevents the glaze from fully melting and vitrifying at the original firing temperature, resulting in incomplete firing (i.e., underfiring). Consequently, the glaze surface fails to form a dense, non-porous glassy structure, resulting in numerous micropores and defects. Ultimately, stains (such as ink, soy sauce, and tea stains) can easily penetrate into the glaze layer through these pores and cannot be removed by conventional cleaning, producing permanent stains and reducing its anti-fouling performance. In addition, the large microscopic undulations on the surface caused by the anti-slip dry particles also cause diffuse reflection of light, resulting in a decrease in the glaze's gloss and making it difficult to achieve the expected high-gloss effect. It should be noted that the protective glaze (low-melting-point matrix) constitutes the majority of the volume of the glaze layer obtained from firing the anti-slip and anti-fouling glaze, and is the main component forming the continuous glassy phase. High-temperature dry granules, on the other hand, are a functional additive designed to maintain their granular shape or not fully melt at the firing temperature of the protective glaze to provide the micro-protrusion structure required for anti-slip properties. Therefore, the original firing temperature mainly refers to the firing temperature of the "protective glaze (low-melting-point matrix)" in the anti-slip and anti-fouling glaze.

[0005] In summary, existing technologies cannot produce glossy ceramic tiles that also possess good anti-slip and anti-fouling properties while ensuring a glossy finish. Summary of the Invention

[0006] The purpose of this invention is to propose a glossy ceramic tile with anti-slip and anti-fouling properties and its preparation method, which is beneficial to have good anti-slip and anti-fouling properties while ensuring the glossy effect, so as to overcome the shortcomings of the prior art.

[0007] To achieve this objective, the present invention adopts the following technical solution:

[0008] A method for preparing a glossy ceramic tile with anti-slip and anti-fouling properties includes the following steps:

[0009] A. Apply the base glaze to the surface of the body layer to form the base glaze layer;

[0010] B. Spray the engraved dry granules onto the surface of the base glaze layer to obtain the engraved dry granule layer;

[0011] The method for preparing the engraved dry granules is as follows:

[0012] B1. The core glaze is dried and granulated sequentially to obtain core particles; wherein, according to the mass parts, the raw materials of the core glaze include 30-40 parts of periclase, 15-20 parts of spodumene, 20-25 parts of barium carbonate, 10-20 parts of quartz, 8-12 parts of magnesite and 35-50 parts of water.

[0013] B2. The bridging material is sprayed onto the surface of the core particles in a fluidized state to form a bridging layer on the surface of the core particles, thereby obtaining the first intermediate particles; wherein the raw materials of the bridging material include glass frit powder, anhydrous ethanol and a binder, and the softening point of the glass frit powder is 750-850°C.

[0014] B3. Spray the coating glaze onto the surface of the first intermediate particles in a fluidized state to form a coating layer on the surface of the bridging layer, thereby obtaining the second intermediate particles; wherein, according to the mass fraction, the raw materials of the coating glaze include 40-50 parts of α-alumina, 20-30 parts of zircon sand, 15-20 parts of corundum, 3-8 parts of aluminum magnesium spinel and 3-8 parts of kaolin.

[0015] B4. The second intermediate particles are successively calcined and vibrated and screened to obtain carved dry particles; wherein the calcination temperature of the carved dry particles is 600-700℃;

[0016] C. Apply a protective glaze to the surface of the carved dry granule layer to obtain a protective glaze layer; wherein, calculated by mass parts, the raw materials of the protective glaze include 20-25 parts of quartz powder, 15-18 parts of spodumene, 10-12 parts of calcined alumina, 8-10 parts of washed kaolin, 3-5 parts of nano titanium dioxide, 10-15 parts of potassium feldspar, 5-8 parts of calcite, 2-4 parts of zinc oxide, 3-5 parts of nepheline, and 3-5 parts of cerium oxide;

[0017] D. After drying, the ceramic tile is fired in a kiln and polished to obtain a glossy ceramic tile with anti-slip and anti-fouling properties; wherein, the glossy ceramic tile with anti-slip and anti-fouling properties has pores, and the pores are formed by the detachment of the core particles and bridging layer of the carved dry granules.

[0018] Further, in step B2, the raw materials of the glass frit powder, calculated by mass parts, include 45-55 parts of borax, 15-20 parts of quartz powder, 8-12 parts of zinc oxide, 20-25 parts of sodium carbonate, 2-5 parts of spodumene, and 0-3 parts of aluminum hydroxide.

[0019] Furthermore, in step B2, the raw materials for the bridging material also include glycerin and a dispersant;

[0020] The bridging material comprises, by weight, 40-50 parts glass frit powder, 3-8 parts binder, 1-3 parts glycerol, 0.1-0.5 parts dispersant, and 30-50 parts anhydrous ethanol.

[0021] Further, in step B2, the amount of bridging material sprayed is 50-80% of the mass of the core glaze, calculated as a percentage by mass.

[0022] Further, step B3 includes:

[0023] B31. The coating glaze is continuously sprayed onto the surface of the first intermediate particles, and after drying, a coating base layer is formed on the surface of the bridging layer;

[0024] B32. Repeat step B31 4 to 10 times to form a wrapping layer on the surface of the bridging layer.

[0025] Furthermore, in step B2, the particle size of the core particles is 80–150 μm, and the thickness of the bridging layer is 10–20 μm.

[0026] Further, step B involves spraying engraved dry granules onto the surface of the base glaze layer using digital inkjet printing or screen printing to obtain an engraved dry granule layer, wherein the spraying amount of the engraved dry granules is 50–200 granules / cm². 2 .

[0027] Furthermore, in step C, the thickness of the protective glaze layer is 1.1 to 1.2 times the particle size of the engraved dry particles.

[0028] Furthermore, in step D, the calcination temperature is 1180–1220°C, and the calcination time is 20–25 min.

[0029] A glossy ceramic tile with anti-slip and anti-fouling properties is prepared using the above-mentioned preparation method for glossy ceramic tiles with anti-slip and anti-fouling properties. The glossy ceramic tile with anti-slip and anti-fouling properties has a gloss level >90°, a stain resistance level of 5, a dry static friction coefficient >0.70, and a wet static friction coefficient >0.60.

[0030] The technical solution provided by this invention may include the following beneficial effects:

[0031] 1. After pre-firing and glazing, the sculpted dry particles obtained by this technical solution actually consist of a core particle, a bridging layer, and an encapsulating layer from the inside out, and the coefficient of thermal expansion of the core particle is greater than 10 × 10⁻⁶. -6 / ℃, the coefficient of thermal expansion of the coating layer is less than 5.5×10. -6 / ℃, the expansion coefficients of the two are vastly different.

[0032] 2. When the bridging layer is in a viscoelastic state, it becomes the weakest link in the system. Under the stress generated by the huge thermal expansion difference between the core particles and the coating layer, the bridging layer first undergoes plastic deformation through viscous flow, leading to the breakdown of the interfacial bond between it and the coating layer, forming annular microcracks. Simultaneously, the core particles break under internal stress, significantly weakening the bond strength between them and the bridging layer. Furthermore, as the temperature continues to drop below the softening point, although the bridging layer eventually solidifies into a glassy state, this solidification is completed on the basis of damaged interfaces and internal plastic rheology. This results in the following structure of the cooled ceramic tile: fragments of broken core particles are loosely adhered together by a small amount of re-solidified, fragile bridging layer residue. This core-bridging layer composite has undergone macroscopic mechanical detachment from the coating layer through annular microcracks, maintaining only a very weak residual connection. The entire system is in a quasi-stable state of "pre-separation." In the subsequent polishing process, the protective glaze layer is partially polished, and the outer coating layer at the top of the carved dry particles is cut away, exposing the bridging layer of the carved dry particles. Furthermore, the horizontal shear force and vibration generated during polishing easily overcome the weak adhesion between the core fragments and the bridging layer residue, and act on the pre-formed annular microcracks between the coating layer and the bridging layer, inducing resonance and eventual interface peeling. This causes the core fragment-attached bridging layer composite to be completely removed from the inner surface of the coating layer and detached. Essentially all the core fragment-attached bridging layer composites detach, ultimately forming a microporous structure on the glaze surface. The inner wall of this microporous structure is the coating layer, and the edges are uncut protective glaze layers firmly bonded to the coating layer. This microporous structure increases the friction between the shoe sole and the brick surface, thus achieving an anti-slip effect. Detailed Implementation

[0033] This technical solution provides a method for preparing glossy ceramic tiles with anti-slip and anti-fouling properties, including the following steps:

[0034] A. Apply the base glaze to the surface of the body layer to form the base glaze layer;

[0035] B. Spray the engraved dry granules onto the surface of the base glaze layer to obtain the engraved dry granule layer;

[0036] The method for preparing the engraved dry granules is as follows:

[0037] B1. The core glaze is dried and granulated sequentially to obtain core particles; wherein, according to the mass parts, the raw materials of the core glaze include 30-40 parts of periclase, 15-20 parts of spodumene, 20-25 parts of barium carbonate, 10-20 parts of quartz, 8-12 parts of magnesite and 35-50 parts of water.

[0038] B2. The bridging material is sprayed onto the surface of the core particles in a fluidized state to form a bridging layer on the surface of the core particles, thereby obtaining the first intermediate particles; wherein the raw materials of the bridging material include glass frit powder, anhydrous ethanol and a binder, and the softening point of the glass frit powder is 750-850°C.

[0039] B3. Spray the coating glaze onto the surface of the first intermediate particles in a fluidized state to form a coating layer on the surface of the bridging layer, thereby obtaining the second intermediate particles; wherein, according to the mass fraction, the raw materials of the coating glaze include 40-50 parts of α-alumina, 20-30 parts of zircon sand, 15-20 parts of corundum, 3-8 parts of aluminum magnesium spinel and 3-8 parts of kaolin.

[0040] B4. The second intermediate particles are successively calcined and vibrated and screened to obtain carved dry particles; wherein the calcination temperature of the carved dry particles is 600-700℃;

[0041] C. Apply a protective glaze to the surface of the carved dry granule layer to obtain a protective glaze layer; wherein, calculated by mass parts, the raw materials of the protective glaze include 20-25 parts of quartz powder, 15-18 parts of spodumene, 10-12 parts of calcined alumina, 8-10 parts of washed kaolin, 3-5 parts of nano titanium dioxide, 10-15 parts of potassium feldspar, 5-8 parts of calcite, 2-4 parts of zinc oxide, 3-5 parts of nepheline, and 3-5 parts of cerium oxide;

[0042] D. After drying, the ceramic tile is fired in a kiln and polished to obtain a glossy ceramic tile with anti-slip and anti-fouling properties; wherein, the glossy ceramic tile with anti-slip and anti-fouling properties has pores, and the pores are formed by the detachment of the core particles and bridging layer of the carved dry granules.

[0043] To address the technical challenge of existing glossy ceramic tiles simultaneously achieving a glossy finish, slip resistance, and stain resistance, this technical solution proposes a method for preparing glossy ceramic tiles with slip and stain resistance. The method comprises four steps: A (applying a base glaze), B (spraying etched dry granules), C (applying a protective glaze), and D (firing and polishing). Through innovative preparation methods, raw material formulations for the etched dry granules, and protective glaze formulations, this method achieves both excellent slip and stain resistance while ensuring a glossy finish. It should be noted that the body layer in this technical solution is formed by pressing and drying conventional ceramic blanks, and the base glaze layer is formed by applying conventional base glazes. Further description of the ceramic blanks and base glazes is omitted here.

[0044] Specifically, the raw materials for the core glaze include periclase, spodumene, barium carbonate, quartz, magnesite, and water. Among these, periclase has a high coefficient of thermal expansion (approximately 13.5 × 10⁻⁶). -6Peregrine (at / ℃) provides a high intrinsic physical expansion basis. Simultaneously, spodumene (LiAlSi2O5) decomposes at high temperatures to produce Li2O, SiO2, and A2O3, while quartz introduces SiO2. Furthermore, the aforementioned active components, such as Li2O, SiO2, and A2O3, react further, promoting the formation of β-lithium nepheline (LiAlSiO4) or related high-lithium silicate phases. During the cooling process after calcination (i.e., glazing) in subsequent step D, these lithium-containing crystalline phases undergo drastic lattice contraction or structural transformation as they pass through their specific phase transition temperature range. This contraction process, macroscopically, acts as a strong, reverse expansion stress source relative to the continuously thermally contracting matrix—i.e., chemical expansion—significantly increasing the apparent average thermal expansion coefficient of the multiphase ceramic structure formed after calcination of the core glaze, making the expansion coefficient of the core particles greater than 10 × 10⁻⁶. -6 / ℃.

[0045] Furthermore, the raw materials for the coating glaze include α-alumina, zircon sand, corundum, aluminum-magnesium spinel, and kaolin. Zircon sand decomposes at high temperatures to generate active SiO2 and ZrO2, which react with SiO2 and A2O3 produced by the decomposition of kaolin in the system, forming a continuous aluminosilicate glass phase between the α-alumina grains. This glass phase itself has an extremely low coefficient of thermal expansion (as low as 4–6 × 10⁻⁶). -6 / ℃), and through encapsulation and bonding, it provides strong mechanical constraint on the highly expandable crystalline phase. Simultaneously, the main phases α-alumina and corundum provide skeletal strength and wear resistance, but their intrinsic high expansion (approximately 8.0 × 10⁻⁶ °C) results in significant mechanical constraint on the highly expandable crystalline phase. -6 The aluminum-magnesium spinel (α-alumina) is physically restrained by the surrounding continuous low-expansion glass phase when heated, preventing it from expanding freely and thus significantly reducing its effective contribution to the macroscopic expansion coefficient. Furthermore, the aluminum-magnesium spinel introduced into the formulation has a lower expansion coefficient than α-alumina. It can partially replace the higher-expansion α-alumina as the crystal phase framework, thereby reducing the overall average thermal expansion coefficient of the rigid crystal phase network. Based on this, combined with the strong constraint of the low-expansion glass phase, the two work synergistically to ultimately achieve an expansion coefficient of less than 5.5 × 10⁻⁶. -6 / ℃.

[0046] Meanwhile, the raw materials for the bridging material include glass frit powder, anhydrous ethanol, and a binder. The fluidized core particles refer to core particles placed in a fluidized bed reactor, through which an inert gas such as nitrogen is introduced, causing the core particles to be in a "boiling" fluidized state under the action of the gas flow. This ensures that each core particle has an equal opportunity to be exposed to the bridging material. The bridging material is then sprayed onto the surface of the fluidized core particles, allowing the solvent (anhydrous ethanol) in the bridging material to evaporate rapidly after spraying. Simultaneously, the binder firmly bonds the glass frit powder to the surface of the core particles.

[0047] Furthermore, the core function of the binder in this technical solution is to act as a temporary bonding medium, ensuring that the glass frit powder adheres to the surface of the core particles during the low-temperature preparation stage. After entering step B4, the calcination (i.e., pre-firing) and glazing processes, as the temperature rises, the glass frit powder melts first to form a liquid phase. At this point, although the binder begins to decompose, its bonding function is taken over by the molten glaze. Ultimately, the binder completely decomposes, carbonizes, and volatilizes during the pre-firing process, leaving no residue and detaching from the system. This ensures that the bridging layer formed by the glass frit powder fully melts, densifies, and forms a glass phase structure at high temperatures, which adheres to the surface of the core particles. In other words, the bridging layer ultimately obtained in this application is essentially a glass phase formed by the calcination of the glass frit powder.

[0048] In summary, after pre-firing and glazing, the sculpted dry particles obtained by this technical solution actually consist of a core particle, a bridging layer, and an encapsulating layer from the inside out, and the coefficient of thermal expansion of the core particle is greater than 10 × 10⁻⁶. -6 / ℃, the coefficient of thermal expansion of the coating layer is less than 5.5×10. -6 / ℃, the expansion coefficients of the two are vastly different.

[0049] Secondly, during the high-temperature calcination stage in step B4, the magnesite (MgCO3) and barium carbonate (BaCO3) in the core glaze formulation can be thermally decomposed to release CO2 gas and form multi-scale pores inside the core particles. However, during the cooling process after calcination in step D, the significant thermal expansion mismatch between the core particles and the coating layer generates extremely high tensile stress within the core particles. The pre-existing pores act as stress concentration points, inducing and propagating numerous dispersed microcracks. The irreversible opening of these microcracks during cooling is recorded as an additional, nonlinear structural expansion increment in macroscopic thermal expansion measurements, thereby causing the core particles to crack and generate microcracks.

[0050] Furthermore, during the glaze firing cooling process, when the kiln temperature drops from a high temperature to the softening point range (750–850℃) of the bridging layer material, a physical transformation occurs: the viscosity of the bridging layer, previously in a high-temperature, low-viscosity state, increases sharply with decreasing temperature, entering a critical viscoelastic state. At this point, the enormous thermal stress generated by the difference in thermal expansion between the core particles and the encapsulation layer is concentrated on the bridging layer. Due to the stress relaxation characteristics of the bridging layer in the viscoelastic state, it can locally dissipate shear stress through viscous flow (irreversible plastic deformation), thus becoming a pre-designed weak zone for stress release in the entire system. At the same time, due to its extremely low strength, the bridging layer loses its ability to effectively transfer stress between the encapsulation layer and the core, allowing the constraint force of the encapsulation layer to be transferred more directly to the core particles. The residual stress that cannot be released is highly concentrated at pre-existing defects such as pores and grain boundaries within the core particles, thereby directionally driving the initiation and propagation of cracks, and exacerbating the crack propagation and fragmentation within the core particles.

[0051] Furthermore, a relatively strong bonding interface is achieved between the coating layer and the protective glaze layer through the synergistic effect of highly active interfacial reaction, deep melt penetration, and gradient transition of expansion coefficient. The specific principle is as follows: (1) The protective glaze adopts a formulation system with relatively low flux content and high alumina content, so that its chemical potential is highly matched with the chemical potential of the coating glaze surface. At the glaze firing temperature, the glaze melt and the coating layer surface have extremely high chemical compatibility. This not only promotes significant Al2O3 exchange at the interface between the two, but also... 3+ With Si 4+ Interdiffusion and solid-state reaction enable the glaze melt to penetrate deep into the grain boundaries and micropores of the coating layer. During the cooling process, the penetrated glaze melt crystallizes or vitrifies synchronously with the coating layer matrix, forming a mechanical-chemical composite locking structure in which the coating layer particles and the protective glaze layer intertwine and micro-interlock. In addition, the Li2O introduced by spodumene in the protective glaze formula promotes low-temperature eutectic melting and participates in the generation of lithium aluminum silicate crystal phase that is thermodynamically compatible with α-alumina, thereby achieving gradient connection and firm anchoring from phase to structure at the interface; (2) This technical solution limits the calcination temperature curve in step B4, so that the coating glaze material is only initially sintered in this pre-firing stage and forms a coating layer with a certain porosity. The porosity of the coating layer not only provides capillary channels and microscopic anchoring points for the glaze melt, which is conducive to the glaze melt penetrating into the coating layer, but also provides more contact opportunities for the active components in the glaze melt (such as flux ions and network oxides) and the crystal surfaces in the coating layer (such as corundum and mullite), accelerating the interdiffusion of ions and solid-phase reaction at high temperatures, which is conducive to further improving the bonding strength between the coating layer and the protective glaze layer; (3) The protective glaze, through the synergy of raw materials such as quartz, calcined alumina, spodumene and nepheline in its formula, controls its thermal expansion coefficient to a gradient range between the core particles and the coating layer. This gradient makes the shrinkage of the protective glaze layer greater than that of the coating layer during the cooling process after glaze firing, but less than that of the core particles. As a result, the protective glaze layer generates a weak compressive stress relative to the coating layer. This compressive stress can enhance the tight contact and closure of the interface, effectively offsetting the tendency of interface separation that may be caused by the violent expansion of the core, thereby ensuring the integrity of the integrated structure of the composite interface between the coating layer and the protective glaze layer under complex thermal stress.

[0052] Furthermore, when the bridging layer is in a viscoelastic state, it becomes the weakest link in the system. Under the stress generated by the huge thermal expansion difference between the core particles and the coating layer, the bridging layer first undergoes plastic deformation through viscous flow, leading to the breakdown of the interfacial bond between it and the coating layer, forming annular microcracks. Simultaneously, the core particles break under internal stress, significantly weakening the bond strength between them and the bridging layer. Additionally, as the temperature continues to drop below the softening point, although the bridging layer eventually solidifies into a glassy state, this solidification is completed on the basis of damaged interfaces and internal plastic rheology. This results in the following structure of the cooled ceramic tile: fragments of broken core particles are loosely adhered together by a small amount of re-solidified, fragile bridging layer residue. This core-bridging layer composite has undergone macroscopic mechanical detachment from the coating layer through annular microcracks, maintaining only a very weak residual connection. The entire system is in a quasi-stable state of "pre-separation." In the subsequent polishing process, the protective glaze layer is partially polished, and the outer coating layer at the top of the carved dry particles is cut away, exposing the bridging layer of the carved dry particles. Furthermore, the horizontal shear force and vibration generated during polishing easily overcome the weak adhesion between the core fragments and the bridging layer residue, and act on the pre-formed annular microcracks between the coating layer and the bridging layer, inducing resonance and eventual interface peeling. This causes the core fragment-attached bridging layer composite to be completely removed from the inner surface of the coating layer and detached. Essentially all the core fragment-attached bridging layer composites detach, ultimately forming a microporous structure on the glaze surface. The inner wall of this microporous structure is the coating layer, and the edges are uncut protective glaze layers firmly bonded to the coating layer. This microporous structure increases the friction between the shoe sole and the brick surface, thus achieving an anti-slip effect.

[0053] Finally, as mentioned above, in this technical solution, the inner wall of the pores is a coating layer formed by the glaze, while the surface of the tile is a protective glaze layer, making the tile surface essentially a composite structure of the coating layer and the protective glaze layer. The coating glaze, composed mainly of high-temperature stable crystalline phases such as α-alumina, corundum, and aluminum-magnesium spinel, combined with an aluminosilicate glass phase, forms a highly dense, extremely low-porosity rigid structure after glazing, fundamentally blocking the penetration path of contaminants (such as pigments and liquids) into the interior. Meanwhile, the protective glaze, fully melted during firing, also forms a continuous, uniform, pore-free glassy surface layer, fundamentally blocking the penetration path of contaminants (such as pigments and liquids) into the interior. The combination of these two elements results in a glossy tile with excellent stain resistance.

[0054] Furthermore, if the carved dry particles are directly added to the protective glaze before overall ball milling, instead of being physically mixed uniformly, the carved dry particles will be further broken down during the overall ball milling process. These broken carved dry particles, as a high-melting-point heterogeneous component, increase the overall initial melting temperature and firing temperature of the anti-slip protective glaze, increasing the risk of under-firing and easily affecting its anti-fouling performance. Therefore, this solution adopts a technical approach of applying the protective glaze and carved dry particles separately, fundamentally eliminating their interference with the sintering temperature of the protective glaze and ensuring stable and reliable anti-fouling performance.

[0055] This technical solution achieves high gloss, and the specific principle is as follows: The main crystalline phase of the coating layer is α-alumina (corundum), which itself has a high refractive index (approximately 1.76). After glazing, these high-refractive-index grains are tightly wrapped and bonded by an aluminosilicate glass phase with an equally high refractive index, forming an extremely dense, low-porosity microstructure. This densification reduces diffuse reflection (scattering) losses at the interface. The protective glaze layer, after melting, forms a uniform, defect-free glassy surface with a smooth surface and a high refractive index (approximately 1.5–1.6). As a surface layer, the protective glaze layer provides initial, highly efficient specular reflection. When light entering the interior reaches the inner wall of the pores, due to the extremely high density and relatively high average refractive index of the coating layer itself, the reflection efficiency of the light on its inner wall surface is also very high. Simultaneously, through formulation design, the refractive index of the protective glaze is optimally matched with the refractive index of the continuous glass phase in the coating layer, which helps to reduce scattering losses at the interface between the two. Therefore, the mirror reflection of the protective glaze and the efficient reflection of the inner wall of the pores work together to produce a strong and uniform mirror gloss, giving the brick surface a bright effect.

[0056] It should be noted that vibrating screening refers to placing the calcined dry granules obtained after calcining the second intermediate particles on a 200-300 mesh screen and applying vibration at a frequency of 100-200Hz, so that the agglomerated calcined dry granules roll and collide on the screen, naturally deagglomerate and pass through the screen to obtain carved dry granules.

[0057] To further explain, in step B2, the raw materials of the glass frit powder, calculated by mass parts, include 45-55 parts of borax, 15-20 parts of quartz powder, 8-12 parts of zinc oxide, 20-25 parts of sodium carbonate, 2-5 parts of spodumene, and 0-3 parts of aluminum hydroxide.

[0058] This technical solution limits the formulation of glass frit powder, utilizes a high proportion of borax and sodium carbonate to synergistically provide a strong flux and network formation basis, and introduces spodumene as a highly efficient fluxing agent, which can significantly reduce the melting temperature and high-temperature viscosity of the glass frit powder system. At the same time, it greatly limits the amount of high-viscosity component aluminum hydroxide and controls the quartz powder content to optimize the network structure, thereby adjusting the softening point of the glass frit powder to the target range of 750-850℃, which is beneficial to ensuring the performance of the glass frit powder.

[0059] To further explain, in step B2, the raw materials for the bridging material also include glycerin and a dispersant;

[0060] The bridging material comprises, by weight, 40-50 parts glass frit powder, 3-8 parts binder, 1-3 parts glycerol, 0.1-0.5 parts dispersant, and 30-50 parts anhydrous ethanol.

[0061] This technical solution, by adding glycerin and a dispersant to the bridging material and limiting the amount of each raw material added, helps to ensure that the bridging layer performs its key functions of stress relaxation, interface separation, and guided controlled peeling, thereby ensuring the performance of the sculpted dry particles. It should be noted that the dispersant can be sodium polyacrylate or sodium hexametaphosphate.

[0062] Preferably, the adhesive is either a polyvinyl butyral aqueous solution or a polyvinyl alcohol aqueous solution, and the polyvinyl butyral content in the polyvinyl butyral aqueous solution is 10-20% by mass percentage, and the polyvinyl alcohol content in the polyvinyl alcohol aqueous solution is 10-20%.

[0063] To further explain, in step B2, the amount of bridging material sprayed is 50-80% of the mass of the core glaze, calculated as a percentage by mass.

[0064] If the mass of the bridging material is less than 50% of the mass of the core glaze, the amount of bridging material used is too low. During spraying, this trace amount of bridging material results in an excessively thin bridging layer. An excessively thin bridging layer has limited stress relaxation (viscous flow) capacity and cannot easily dissipate interfacial shear stress. Residual stress may directly cause the core to excessively break down or even pulverize during cooling, losing its structural integrity as a "pre-separated composite" and easily affecting the final pore morphology. If the mass of the bridging material is more than 80% of the mass of the core glaze, the amount of bridging material used is too high, resulting in an excessively thick bridging layer. An excessively thick bridging layer may undergo excessive deformation, flow, or bulging due to its own weight or internal and external stresses at the softening point temperature, easily damaging the geometry and interface smoothness of the sculpted dry particles.

[0065] To further explain, step B3 includes:

[0066] B31. The coating glaze is continuously sprayed onto the surface of the first intermediate particles, and after drying, a coating base layer is formed on the surface of the bridging layer;

[0067] B32. Repeat step B31 4 to 10 times to form a wrapping layer on the surface of the bridging layer.

[0068] This technical solution uses 4 to 10 spray coatings to construct the coating layer, which helps to avoid the problems of glaze dripping, uneven thickness, or drying cracking caused by a single thick coating. It ensures that the uniformity, density, and thickness of the coating layer are precisely controllable, providing reliable thermodynamic protection and stable low expansion performance for subsequent firing.

[0069] To further explain, in step B2, the particle size of the core particles is 80–150 μm, and the thickness of the bridging layer is 10–20 μm.

[0070] If the core particles are too small, they are easily carried away by the airflow, which is not conducive to the spraying of bridging material; if the core particles are too large, the fluidization state is unstable, which is also not conducive to the spraying of bridging material.

[0071] Furthermore, if the particle size of the core particles and the thickness of the bridging layer are too large, the resulting holes after the core particles and bridging layer detach will be too large, affecting the decorative effect. Conversely, if the particle size of the core particles and the thickness of the bridging layer are too small, the resulting holes after the core particles and bridging layer detach will be too small, resulting in limited effect in increasing the friction between the shoe sole and the brick surface, which may affect the anti-slip function. Therefore, this technical solution limits the particle size of the core particles and the thickness of the bridging layer to ensure that the size of the holes formed after the core particles and bridging layer detach is appropriate, which helps to ensure both the anti-slip effect and the decorative effect.

[0072] Further explanation: Step B involves spraying engraved dry granules onto the surface of the base glaze layer using digital inkjet printing or screen printing to obtain an engraved dry granule layer, wherein the spraying amount of the engraved dry granules is 50–200 granules / cm². 2 .

[0073] Using digital inkjet printing or screen printing instead of traditional mixed spraying or random spraying can achieve patterning of engraved dry granules, thereby improving the decorative effect.

[0074] Furthermore, if the spraying amount of sculpted dry granules is too low, there will be too few effective friction points per unit area, making it difficult to form a continuous and reliable water film disruption zone on the tile surface (especially in a wet state). This results in a small actual contact area between the shoe sole and the tile surface, leading to insufficient mechanical interlocking and low friction, significantly increasing the risk of slipping. If the spraying amount of sculpted dry granules is too high, the high-density pores will give the tile surface a sandy or frosted feel, deviating from the smooth, mirror-like texture that high-end tiles should have, thus affecting the product's grade.

[0075] To further explain, in step C, the thickness of the protective glaze layer is 1.1 to 1.2 times the particle size of the engraved dry particles.

[0076] By limiting the thickness of the protective oil layer, it is beneficial to ensure that the carved dry particles are completely immersed in the protective glaze layer while reducing the amount of protective glaze applied and saving costs. This allows for a uniform temperature field and stable atmosphere during glaze firing, and provides sufficient medium for the formation of a strong interface between the coating layer of the carved dry particles and the protective glaze layer.

[0077] To further explain, in step D, the calcination temperature is 1180–1220°C, and the calcination time is 20–25 min.

[0078] This technical solution, by limiting the calcination temperature and calcination time in step D, helps to ensure the gloss effect, anti-slip performance, and stain resistance of the final calcined ceramic tile.

[0079] A glossy ceramic tile with anti-slip and anti-fouling properties is prepared using the above-mentioned preparation method for glossy ceramic tiles with anti-slip and anti-fouling properties. The glossy ceramic tile with anti-slip and anti-fouling properties has a gloss level >90°, a stain resistance level of 5, a dry static friction coefficient >0.70, and a wet static friction coefficient >0.60.

[0080] This technical solution also proposes a glossy ceramic tile with anti-slip and anti-fouling properties prepared by the above-mentioned method for preparing glossy ceramic tiles with anti-slip and anti-fouling properties. The gloss is >90°, the stain resistance is level 5, the dry static friction coefficient is >0.70, and the wet static friction coefficient is >0.60. This is beneficial to ensure good anti-slip and anti-fouling properties while maintaining the glossy effect.

[0081] The technical solution of the present invention will be further illustrated below through specific embodiments.

[0082] Example 1

[0083] A. Apply the base glaze to the surface of the body layer to form the base glaze layer;

[0084] B. Using digital inkjet printing, engraved dry granules are sprayed onto the surface of the base glaze layer to obtain an engraved dry granule layer, with a spraying density of 100 granules / cm². 2 ;

[0085] The preparation method of carved dry granules is as follows:

[0086] B1. The core glaze is dried and granulated in sequence to obtain core particles with a particle size of 100μm; wherein, according to the mass parts, the raw materials of the core glaze include 35 parts of periclase, 18 parts of spodumene, 23 parts of barium carbonate, 15 parts of quartz, 10 parts of magnesite and 40 parts of water.

[0087] B2. A bridging material is sprayed onto the surface of the fluidized core particles to form a bridging layer with a thickness of 10 μm, resulting in the first intermediate particles. The amount of bridging material sprayed is 60% of the mass of the core glaze. The raw materials of the bridging material include 45 parts glass frit powder, 5 parts binder, 2 parts glycerol, 0.1 parts sodium polyacrylate, and 40 parts anhydrous ethanol. The raw materials of the glass frit powder include 50 parts borax, 16 parts quartz powder, 10 parts zinc oxide, 23 parts sodium carbonate, 3 parts spodumene, and 1 part aluminum hydroxide, with a softening point of 780℃. The binder is a polyvinyl butyral aqueous solution, and the polyvinyl butyral content in the polyvinyl butyral aqueous solution is 15% by mass.

[0088] B3. The coating glaze is continuously sprayed onto the surface of the first intermediate particle. After drying, a coating base layer is formed on the surface of the bridging layer. The step of forming the coating base layer is repeated 5 times to form a coating layer on the surface of the bridging layer, thus obtaining the second intermediate particle. The raw materials of the coating glaze, calculated by mass, include 45 parts of α-alumina, 25 parts of zircon sand, 18 parts of corundum, 5 parts of aluminum magnesium spinel, and 5 parts of kaolin.

[0089] B4. The second intermediate particles are calcined and vibrating sieved sequentially to obtain carved dry particles; wherein, the calcination temperature of the carved dry particles is 650℃.

[0090] C. Apply the protective glaze to the surface of the sculpted dry granule layer to obtain a protective glaze layer with a thickness of 135μm; wherein, according to the mass parts, the raw materials of the protective glaze include 23 parts of quartz powder, 16 parts of spodumene, 11 parts of calcined alumina, 9 parts of washed kaolin, 4 parts of nano titanium dioxide, 13 parts of potassium feldspar, 6 parts of calcite, 3 parts of zinc oxide, 4 parts of nepheline and 4 parts of cerium oxide;

[0091] D. After drying, the ceramic tile is fired in a kiln and polished to obtain a glossy ceramic tile with anti-slip and anti-fouling properties; the firing temperature is 1200℃ and the firing time is 25min; the glossy ceramic tile with anti-slip and anti-fouling properties has pores, and the pores are formed by the core particles of the carved dry granules and the detachment of the bridging layer.

[0092] Example 2

[0093] A. Apply the base glaze to the surface of the body layer to form the base glaze layer;

[0094] B. Using screen printing, the sculpted dry granules are sprayed onto the surface of the base glaze layer to obtain a sculpted dry granule layer, with a spraying density of 80 granules / cm². 2 ;

[0095] The preparation method of carved dry granules is as follows:

[0096] B1. The core glaze is dried and granulated in sequence to obtain core particles with a particle size of 120μm; wherein, according to the mass parts, the raw materials of the core glaze include 30 parts of periclase, 20 parts of spodumene, 20 parts of barium carbonate, 18 parts of quartz, 12 parts of magnesite and 50 parts of water.

[0097] B2. A bridging material is sprayed onto the surface of the fluidized core particles to form a bridging layer with a thickness of 20 μm, resulting in the first intermediate particles. The amount of bridging material sprayed is 70% of the mass of the core glaze. The raw materials of the bridging material include 40 parts glass frit powder, 8 parts binder, 3 parts glycerol, 0.3 parts sodium hexametaphosphate, and 45 parts anhydrous ethanol. The raw materials of the glass frit powder include 55 parts borax, 15 parts quartz powder, 8 parts zinc oxide, 20 parts sodium carbonate, 2 parts spodumene, and 2 parts aluminum hydroxide, and the softening point of the glass frit powder is 750℃. The binder is a polyvinyl alcohol aqueous solution, and the polyvinyl alcohol content in the polyvinyl alcohol aqueous solution is 10% by mass.

[0098] B3. The coating glaze is continuously sprayed onto the surface of the first intermediate particle. After drying, a coating base layer is formed on the surface of the bridging layer. The step of forming the coating base layer is repeated 8 times to form a coating layer on the surface of the bridging layer, thus obtaining the second intermediate particle. The raw materials of the coating glaze, calculated by mass, include 40 parts of α-alumina, 30 parts of zircon sand, 15 parts of corundum, 8 parts of aluminum magnesium spinel, and 3 parts of kaolin.

[0099] B4. The second intermediate particles are calcined and vibrating sieved sequentially to obtain carved dry particles; wherein, the calcination temperature of the carved dry particles is 700℃;

[0100] C. Apply a protective glaze to the surface of the sculpted dry granule layer to obtain a protective glaze layer with a thickness of 180 μm; wherein, according to the mass parts, the raw materials of the protective glaze include 20 parts of quartz powder, 18 parts of spodumene, 12 parts of calcined alumina, 10 parts of washed kaolin, 5 parts of nano titanium dioxide, 15 parts of potassium feldspar, 5 parts of calcite, 2 parts of zinc oxide, 5 parts of nepheline, and 3 parts of cerium oxide.

[0101] D. After drying, the ceramic tile is fired in a kiln and polished to obtain a glossy ceramic tile with anti-slip and anti-fouling properties; the firing temperature is 1180℃ and the firing time is 25min; the glossy ceramic tile with anti-slip and anti-fouling properties has pores, and the pores are formed by the core particles of the carved dry granules and the detachment of the bridging layer.

[0102] Example 3

[0103] A. Apply the base glaze to the surface of the body layer to form the base glaze layer;

[0104] B. Using digital inkjet printing, engraved dry granules are sprayed onto the surface of the base glaze layer to obtain an engraved dry granule layer, with a spraying density of 100 granules / cm². 2 ;

[0105] The preparation method of carved dry granules is as follows:

[0106] B1. The core glaze is dried and granulated in sequence to obtain core particles with a particle size of 140μm; wherein, according to the mass parts, the raw materials of the core glaze include 40 parts of periclase, 15 parts of spodumene, 25 parts of barium carbonate, 10 parts of quartz, 8 parts of magnesite and 40 parts of water.

[0107] B2. A bridging material is sprayed onto the surface of the fluidized core particles to form a bridging layer with a thickness of 10 μm, resulting in the first intermediate particles. The amount of bridging material sprayed is 70% of the mass of the core glaze. The raw materials of the bridging material include 50 parts glass frit powder, 3 parts binder, 1 part glycerin, 0.5 parts sodium polyacrylate, and 50 parts anhydrous ethanol. The raw materials of the glass frit powder include 45 parts borax, 18 parts quartz powder, 12 parts zinc oxide, 20 parts sodium carbonate, 5 parts spodumene, and 3 parts aluminum hydroxide, and the softening point of the glass frit powder is 800℃. The binder is a polyvinyl butyral aqueous solution, and the polyvinyl butyral content in the polyvinyl butyral aqueous solution is 10% by mass.

[0108] B3. The coating glaze is continuously sprayed onto the surface of the first intermediate particle. After drying, a coating base layer is formed on the surface of the bridging layer. The step of forming the coating base layer is repeated 10 times to form a coating layer on the surface of the bridging layer, thus obtaining the second intermediate particle. The raw materials of the coating glaze, calculated by mass, include 50 parts of α-alumina, 20 parts of zircon sand, 20 parts of corundum, 3 parts of aluminum magnesium spinel, and 8 parts of kaolin.

[0109] B4. The second intermediate particles are calcined and vibrating sieved sequentially to obtain carved dry particles; wherein, the calcination temperature of the carved dry particles is 700℃;

[0110] C. Apply the protective glaze to the surface of the sculpted dry granule layer to obtain a protective glaze layer with a thickness of 195μm; wherein, according to the mass parts, the raw materials of the protective glaze include 25 parts of quartz powder, 15 parts of spodumene, 10 parts of calcined alumina, 8 parts of washed kaolin, 3 parts of nano titanium dioxide, 10 parts of potassium feldspar, 8 parts of calcite, 4 parts of zinc oxide, 3 parts of nepheline and 5 parts of cerium oxide.

[0111] D. After drying, the ceramic tile is fired in a kiln and polished to obtain a glossy ceramic tile with anti-slip and anti-fouling properties; the firing temperature is 1180℃ and the firing time is 25min; the glossy ceramic tile with anti-slip and anti-fouling properties has pores, and the pores are formed by the core particles of the carved dry granules and the detachment of the bridging layer.

[0112] Comparative Example 1

[0113] Comparative Example 1 uses existing technology to prepare glossy ceramic tiles with anti-slip and anti-fouling properties. The specific preparation method is as follows:

[0114] A. Preparation of high-temperature dry granules; wherein, according to mass parts, the chemical composition of the high-temperature dry granules includes: SiO2 62.0 parts, Al2O3 13.0 parts, Fe2O3 0.03 parts, TiO2 0.1 parts, CaO 5.5 parts, MgO 0.8 parts, K2O 2.2 parts, Na2O 1.2 parts and loss on ignition 0.05 parts, and the melting temperature of the high-temperature dry granules is 1700~1800℃;

[0115] B. After crushing the high-temperature dry granules to 100 mesh, mix them with the remaining raw materials of the anti-slip protective glaze, add water, and ball mill. After ball milling, add water to obtain an anti-slip protective glaze with a flow rate of 15s, a specific gravity of 1.35, a fineness of passing through a 350-mesh sieve, and a sieve residue of 0.3-1.0%. The raw materials of the anti-slip protective glaze, by mass percentage, include: 10 parts potassium feldspar, 5 parts sodium feldspar, 6 parts kaolin, 2 parts zinc oxide, 2 parts corundum, 3 parts wollastonite, 3 parts barium carbonate, and 50 parts high-temperature dry granules. The chemical composition of the above anti-slip protective glaze, by mass percentage, includes: 66.5 parts SiO2, 13.2 parts Al2O3, 0.2 parts Fe2O3, 0.15 parts TiO2, 6.5 parts CaO, 1.2 parts MgO, 2.6 parts K2O, 1.5 parts Na2O, and 1 part BaO. 0.5 parts, ZnO 3.2 parts and loss on ignition 3.5 parts;

[0116] C. Apply the anti-slip protective glaze with a specific gravity of 1.35 and a spraying amount of 300g / m³. 2 The coating is applied to the top of the tile blank after the base glaze has been applied and inkjet printed. After drying, it is fired to obtain a glossy ceramic tile with anti-slip and anti-fouling properties.

[0117] The glossy ceramic tiles prepared in the examples and comparative examples were subjected to conventional tests in the field of architectural ceramics, including anti-slip, anti-fouling, and gloss performance. The results are shown in Table 1 below:

[0118] Table 1. Performance test results of glossy ceramic tiles in the examples and comparative examples.

[0119]

[0120] As can be seen from the test data in Table 1, the glossy ceramic tiles obtained by this technical solution have a gloss level >90°, a stain resistance level of 5, a dry static friction coefficient >0.70, and a wet static friction coefficient >0.60. This is beneficial to ensure good anti-slip and anti-stain properties while maintaining a glossy effect, so as to meet the actual use needs.

[0121] The technical principles of the present invention have been described above with reference to specific embodiments. These descriptions are merely for explaining the principles of the invention and should not be construed as limiting the scope of protection of the invention in any way. Based on this explanation, those skilled in the art can readily conceive of other specific embodiments of the invention without inventive effort, and these embodiments will all fall within the scope of protection of the present invention.

Claims

1. A method for preparing a glossy ceramic tile with anti-slip and anti-fouling properties, characterized in that, Includes the following steps: A. Apply the base glaze to the surface of the body layer to form the base glaze layer; B. Spray the engraved dry granules onto the surface of the base glaze layer to obtain the engraved dry granule layer; The method for preparing the engraved dry granules is as follows: B1. The core glaze is dried and granulated sequentially to obtain core particles; wherein, according to the mass parts, the raw materials of the core glaze include 30-40 parts of periclase, 15-20 parts of spodumene, 20-25 parts of barium carbonate, 10-20 parts of quartz, 8-12 parts of magnesite and 35-50 parts of water. B2. The bridging material is sprayed onto the surface of the fluidized core particles to form a bridging layer on the surface of the core particles, thus obtaining the first intermediate particles; wherein, by mass parts, the raw materials of the bridging material include 40-50 parts of glass frit powder, 3-8 parts of binder, 1-3 parts of glycerol, 0.1-0.5 parts of dispersant, and 30-50 parts of anhydrous ethanol, and the softening point of the glass frit powder is 750-850℃; by mass parts, the raw materials of the glass frit powder include 45-55 parts of borax, 15-20 parts of quartz powder, 8-12 parts of zinc oxide, 20-25 parts of sodium carbonate, 2-5 parts of spodumene, and 0-3 parts of aluminum hydroxide; B3. Spray the coating glaze onto the surface of the first intermediate particles in a fluidized state to form a coating layer on the surface of the bridging layer, thereby obtaining the second intermediate particles; wherein, according to the mass fraction, the raw materials of the coating glaze include 40-50 parts of α-alumina, 20-30 parts of zircon sand, 15-20 parts of corundum, 3-8 parts of aluminum magnesium spinel and 3-8 parts of kaolin. B4. The second intermediate particles are successively calcined and vibrated and screened to obtain carved dry particles; wherein the calcination temperature of the carved dry particles is 600-700℃; C. Apply a protective glaze to the surface of the carved dry granule layer to obtain a protective glaze layer; wherein, calculated by mass parts, the raw materials of the protective glaze include 20-25 parts of quartz powder, 15-18 parts of spodumene, 10-12 parts of calcined alumina, 8-10 parts of washed kaolin, 3-5 parts of nano titanium dioxide, 10-15 parts of potassium feldspar, 5-8 parts of calcite, 2-4 parts of zinc oxide, 3-5 parts of nepheline, and 3-5 parts of cerium oxide; D. After drying, the ceramic tile is fired in a kiln and polished to obtain a glossy ceramic tile with anti-slip and anti-fouling properties; wherein, the glossy ceramic tile with anti-slip and anti-fouling properties has pores, and the pores are formed by the detachment of the core particles and bridging layer of the carved dry granules.

2. The method for preparing a glossy ceramic tile with anti-slip and anti-fouling properties according to claim 1, characterized in that, In step B2, the amount of bridging material sprayed is 50-80% of the mass of the core glaze, calculated as a percentage by mass.

3. The method for preparing a glossy ceramic tile with anti-slip and anti-fouling properties according to claim 1, characterized in that, Step B3 includes: B31. The coating glaze is continuously sprayed onto the surface of the first intermediate particles, and after drying, a coating base layer is formed on the surface of the bridging layer; B32. Repeat step B31 4 to 10 times to form a wrapping layer on the surface of the bridging layer.

4. The method for preparing a glossy ceramic tile with anti-slip and anti-fouling properties according to claim 1, characterized in that, In step B2, the particle size of the core particles is 80–150 μm, and the thickness of the bridging layer is 10–20 μm.

5. The method for preparing a glossy ceramic tile with anti-slip and anti-fouling properties according to claim 1, characterized in that, Step B involves spraying etched dry granules onto the surface of the base glaze layer using digital inkjet printing or screen printing to obtain an etched dry granule layer, wherein the spraying amount of the etched dry granules is 50–200 granules / cm². 2 .

6. The method for preparing a glossy ceramic tile with anti-slip and anti-fouling properties according to claim 1, characterized in that, In step C, the thickness of the protective glaze layer is 1.1 to 1.2 times the particle size of the engraved dry particles.

7. The method for preparing a glossy ceramic tile with anti-slip and anti-fouling properties according to claim 1, characterized in that, In step D, the calcination temperature is 1180–1220°C, and the calcination time is 20–25 min.

8. A glossy ceramic tile with anti-slip and anti-fouling properties, characterized in that: The glossy ceramic tile with anti-slip and anti-fouling properties is prepared using the preparation method of any one of claims 1 to 7. The glossy ceramic tile with anti-slip and anti-fouling properties has a gloss level > 90°, a stain resistance level of 5, a dry static friction coefficient > 0.70, and a wet static friction coefficient > 0.60.

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