High-strength v-glass and method of making and use thereof

Abstract

This application relates to the field of glass, specifically disclosing a high-strength aventurine glass, its preparation method, and its applications. The high-strength aventurine glass has a aventurine size of 10-350 μm, a transmittance of ≥ 6.5% at 550 nm, and a Vickers hardness of ≥ 700 MPa. This aventurine glass uses a high-alumina-silicon glass system as a matrix, and is formed by introducing metal oxides and employing a gradient reheat crystallization process. This effectively overcomes the technical bottleneck of difficult crystallization caused by the high viscosity of the high-alumina-silicon glass system, and solves the problems of insufficient strength and uneven flashing effect in existing aventurine glass technologies. It perfectly integrates optical aesthetics and mechanical properties, providing reliable impact protection for the screen without affecting the exquisite appearance of electronic products, thanks to its stable and uniform flashing effect and enhanced mechanical strength.

Description

Technical Field

[0001] This application relates to the field of glass materials, and more specifically, to a high-strength aventurine glass, its preparation method, and its application. Background Technology

[0002] Aventurine glass is a type of decorative glass with shimmering metallic crystals. Its aventurine effect originates from the precipitation of specific metal oxides (such as chromium, iron, and bismuth) into plate-like or star-shaped crystals within the glass matrix. This type of glass is increasingly sought after by smart electronic devices for display screens or back covers that combine high-end decorative effects with reliable protective performance.

[0003] Traditional glass manufacturing processes for achieving a glittering effect include the following: 1) Using gold mine tailings as the main raw material, combined with ordinary glass raw materials and a small amount of additives to form a glitter base, the mixture is melted, held at a constant temperature, and then annealed after molding. For example, CN1084834A uses gold mine tailings (Al2O3 0.1-1.0%) to prepare glitter glass, which can reduce production costs and achieve resource recycling and environmental protection. However, in the actual high-temperature melting process, the metal particles in the tailings are prone to agglomeration, resulting in uneven distribution of glitter in the glass and affecting the overall aesthetics of the product. At the same time, the glitter glass produced by this technology has certain limitations in terms of mechanical strength and other properties, limiting its application in fields with high strength requirements. 2) For ordinary soda-lime glass systems, CN113480176A proposes a scheme to prepare dry glitter glass particles using a soda-lime glass system as the matrix (Al2O3 0.1-10%). However, in practical applications, the low Al2O3 content results in poor mechanical properties of the glass matrix, making it prone to cracking in scenarios subject to high stress, such as floor decoration. Furthermore, its dry granule form limits its application primarily to ceramic tile surfaces, making it unsuitable for curved or complex glass products.

[0004] Therefore, traditional glass used to achieve the Venus sparkle effect suffers from insufficient intrinsic strength, poor strength performance, and uneven sparkle due to the difficulty in precisely controlling crystal size and distribution. This makes it difficult to meet the stringent impact resistance (such as drop height requirements) and wear resistance requirements of electronic devices. High-alumina-silica glass (Al2O3 content ≥15wt%), due to its excellent mechanical strength and chemical stability, has become the preferred material for high-end cover glass and holds promise as a base glass system for preparing high-strength Venus sparkle glass.

[0005] However, due to the high Al2O3 content in high-alumina silica glass, the viscosity of the glass melt is greater than 10 at 1350℃. 3Pa·s is approximately 100 times that of soda-lime glass. If a high-alumina-silica glass system is used as the base glass, metal particles are difficult to move and aggregate in such a viscous glass melt, seemingly "frozen" within the glass matrix. This leads to the following drawbacks: 1) Impaired metal ion diffusion: Reduced metal ion mobility results in extremely low crystal nucleation density, hindering growth; 2) Inhomogeneous crystallization due to phase separation: Al… 3+ The enriched region forms an [AlO4] network, which repels metal ions from entering, resulting in crystals being concentrated in the aluminum-poor region; 3) The stability of the glass matrix is ​​reduced: the addition of metal colorants weakens the stability of the glass matrix, which is not conducive to the strengthening of the glass surface.

[0006] Therefore, this application is hereby submitted. Summary of the Invention

[0007] To address the issues of insufficient strength and uneven flash effect in existing aventurine glass technologies, this application provides a high-strength aventurine glass, its preparation method, and its applications. This aventurine glass uses a high-alumina-silicon glass system as its matrix and is formed by introducing metal oxide crystals, perfectly blending optical aesthetics with mechanical properties. With its stable and uniform flash effect and enhanced mechanical strength, it provides reliable impact protection for the screen without compromising the aesthetic appeal of electronic products.

[0008] The technical solution adopted in this application is as follows: In the first aspect, this application proposes a high-strength asteroid glass, wherein the asteroid size is 10-350μm, the transmittance at 550nm is ≥ 6.5%, and the Vickers hardness is ≥ 700MPa.

[0009] Furthermore, this high-strength aventurine glass is composed of a basic high-alumina-silica glass component and metallic colorants and reducing agents; and meets the following conditions: 3.0 ≤ (SiO2+ Al2O3) / (metal colorant+ reducing agent+ Li2O) ≤ 12.0.

[0010] Furthermore, the basic high-alumina silica glass composition includes SiO2, Al2O3, Na2O, K2O and Li2O, wherein the content of SiO2 is 55-68 wt% and the content of Al2O3 is 15-24 wt%.

[0011] Furthermore, the content of the metallic colorant is 0.1 to 8 wt%, and the content of the reducing agent is 0.1 to 3 wt%.

[0012] Furthermore, the glass substrate of this high-strength aluminosilicate glass is obtained by mixing the raw materials of basic high-aluminosilicate glass with metal colorants and reducing agents, then melting and homogenizing the mixed raw materials using a gradient reheat crystallization process, followed by casting and annealing.

[0013] Preferably, the above-mentioned gradient retemperature crystallization process includes at least three heating-cooling stages, including: (1) Heat the mixed raw materials to the melting temperature T 熔 After the raw materials are completely melted, the temperature is lowered to T. 核 To promote the initial formation of crystal nuclei; (2) Then the temperature is raised to T x After holding at the temperature for X minutes, cool down to T. y The temperature is maintained for Y minutes, and the heating-cooling process is repeated 2-3 times to promote the slow precipitation and stable, uniform growth of Venus crystal nuclei. Among them, T 熔 1580-1620℃; T 核 1460-1500℃; T x 1460-1580℃; T y The temperature range is 1360-1450℃, and the following relationship is satisfied in each cycle: T 熔 > T x ≥T 核； X is 60-120 min; T 核 > T y Y is 90-210 min.

[0014] Preferably, in step (1), the mixed raw materials are heated to the melting temperature T. 熔 The heating rate is 8-10℃ / min; the temperature of the liquid is reduced to T. 核 The cooling rate is 5-7℃ / min, and no insulation is required.

[0015] Preferably, in step (2), the temperature of the liquid is raised to T. x The temperature rise rate is 2-5℃ / min; the temperature of the feed liquid is reduced to T. y The temperature drops at a rate of 1-4℃ / min.

[0016] Preferably, in step (2), the continuous heating-cooling cycle includes: a. Change the temperature of the feed liquid from T 核 The temperature is increased to T3 at a rate of V3 and held at t3 to promote the homogenization of the glass melt. b. Cool the liquid to temperature T4 at a rate of V4 and hold at that temperature for t4 to induce the formation of "Venus" crystal nuclei; c. Heat the liquid to temperature T5 at a rate of V5 and hold for t5 to promote crystal growth, while satisfying T3 > T5; d. Cool the liquid to temperature T6 at a rate of V6 and hold for t6 to adjust the crystal morphology and distribution, while satisfying T4 ≥ T6; e. Heat the liquid to temperature T7 at a rate of V7 and hold it at t7 to optimize the optical properties of Venus, while ensuring that T5 ≥ T7. f. Finally, the liquid is cooled to temperature T8 at a rate of V8 and held at that temperature for t8 to stabilize the star-shaped morphology and eliminate internal stress, while satisfying T6 > T8.

[0017] Preferably, the rate of temperature change in step (2) satisfies: V3>V4 ≥ V5 ≥ V6 ≥ V7 > V8, and the range of V3-V8 is 1~5℃ / min.

[0018] Furthermore, the above-mentioned basic high-alumina silica glass components, by weight percentage, are 55-68 wt% SiO2, 15-24 wt% Al2O3, 3-18 wt% Na2O, 0.5-5 wt% K2O and 0.1-5 wt% Li2O.

[0019] Furthermore, the aforementioned basic high-alumina-silica glass components also include MgO and ZrO2, as well as a clarifying agent; MgO is 0.1–8 wt%, ZrO2 is 0.1–3 wt%, and clarifying agent is 0.1–2 wt%.

[0020] Furthermore, the above-mentioned basic high-alumina-silicon glass composition satisfies: 2.5 ≤ (SiO2+ Al2O3) / (Na2O + K2O+ Li2O) ≤ 8.0.

[0021] Furthermore, the above-mentioned basic high-alumina-silicon glass composition satisfies: 0.2≤(MgO+2×Li2O) / Al2O3≤ 2.5.

[0022] Furthermore, the above-mentioned basic high-alumina-silicon glass composition satisfies: 3.0 ≤ (SiO2+ Al2O3+ ZrO2) / (Na2O+ K2O + Li2O) ≤ 8.0.

[0023] Furthermore, the aforementioned metal colorants include Fe3O4, Fe2O3, FeO, CuO, Cu2O, Cr2O3, CoO, dichromates, CrO3, MnO2, Co2O3, NiO, V2O5, TiO2, Nd2O3, Pr2O3, and Pr6O. 11 One or more of CeO2, Er2O3, MoO3, WO3, Au and Ag colloids.

[0024] Furthermore, the reducing agent mentioned above includes one or more of the following: carbon powder, coke powder, tartaric acid, aluminum powder, tin powder, silicon powder, glucose, ethanol, and citric acid.

[0025] Furthermore, the aforementioned clarifying agents include SO4. 2- NO3 - F - Cl - One or more of SnO2.

[0026] Furthermore, the base color of the aforementioned high-strength Venus glass includes any one of brown, black, green, blue, yellow, purple, and pink.

[0027] Furthermore, the Venus shape of the aforementioned high-strength Venus glass can be one or more of the following: dot-shaped, dendritic, triangular, quadrilateral, hexagonal, or elongated oblique square.

[0028] Furthermore, the Venus color of the aforementioned high-strength Venus glass is one or more of the following: turquoise, gold, reddish-brown, silver-white, sky blue, yellow, and pinkish-purple.

[0029] Furthermore, the aforementioned high-strength aventurine glass includes any one of the following: brown-based gold-flecked glass, black-based silver-flecked glass, green-based colored-color glass, blue-based colored-color glass, yellow-based colored-color glass, purple-based colored-color glass, and pink-based colored-color glass.

[0030] Furthermore, the above-mentioned high-strength aventurine glass has a four-point bending performance of 4PB, with a 4PB value ≥ 700 MPa; a drop height of 180-grit sandpaper ≥ 170 cm; and a glass thickness of 0.3–8.0 mm.

[0031] Secondly, this application provides a method for preparing high-strength aventurine glass, comprising: Step S1: Mix the raw materials of the basic high aluminosilicate glass component, metal colorant, and reducing agent according to the formula, and use high-pressure airflow pulverization combined with ultrasonic-assisted process to mix them evenly; Step S2: The mixed raw materials are melted and homogenized to crystallize using a gradient reheat crystallization process, then cast and annealed to obtain a glass substrate; Step S3: After cutting the glass substrate, polish it with polishing powder and finally perform chemical strengthening.

[0032] Furthermore, the parameters of the above-mentioned high-pressure airflow pulverization combined with ultrasonic assistance process include: high-pressure airflow pressure of 1.5-2.0MPa, ultrasonic power of 200-500W, frequency of 40-80kHz, and time of 20-40min.

[0033] Furthermore, in the process of preparing the glass substrate, the annealing temperature is 500-560℃, and after holding at that temperature for 120-180 minutes, it is cooled to room temperature in the furnace.

[0034] Furthermore, in the above polishing process, the polishing powder is one or more of alumina, silicon carbide, diamond, zirconium oxide, and cerium oxide.

[0035] Furthermore, the above polishing process includes rough polishing and fine polishing; Rough polishing includes using polishing powder with a particle size of 10-15μm, polishing pressure of 6-20kPa, polishing machine speed of 80-120rpm, and processing time of 10-15min; Fine polishing involves using polishing powder with a particle size of 0.5-1μm, a polishing pressure of 3-10kPa, a rotation speed of 60-80rpm, and a processing time of 20-30min.

[0036] Furthermore, the chemical tempering molten salt used in the above-mentioned chemical strengthening process includes one or more of KNO3, KNO2, KOH, K2CO3, K2SiO3, NaNO3, Na2CO3, Na2SiO3, Al2O3, Al(OH)3, and LiNO3.

[0037] Furthermore, the above chemical strengthening is a two-step chemical strengthening method, with a temperature of 200-450℃ and a strengthening time of 30-120min.

[0038] Furthermore, during the chemical strengthening process, a high-voltage electric field generation system is used to apply a high-voltage electric field to the chemically tempered molten salt.

[0039] Furthermore, in the chemical strengthening process, the applied electric field frequency is 0.1-1Hz, the electric field strength is 0.1-10kV / cm, and the electrode spacing is 5-50cm.

[0040] Thirdly, this application provides an application of the aforementioned high-strength aventurine glass in high-end consumer electronics products.

[0041] Furthermore, the aforementioned applications include one or more components in the manufacture of front display covers for consumer electronics products, rear covers assembled on the rear of electronic devices, and camera protection covers.

[0042] In summary, this application has the following beneficial effects: This application uses high-alumina-silica glass (Al2O3 content ≥15wt%) as the base system and introduces transition metals or rare earth elements as colorants. In order to promote the migration rate and crystallization uniformity of metal ions in high-viscosity glass melt, a gradient reheat crystallization process is used to melt, homogenize, and crystallize the mixed raw materials to form high-strength aventurine glass.

[0043] This aventurine glass, due to the excellent mechanical strength and chemical stability of its high-alumina-silica glass matrix, can further enhance its strength performance by achieving higher surface compressive stress and a deeper stress layer through chemical strengthening. The high-strength aventurine glass provided in this application has a Vickers hardness ≥ 700 MPa, a four-point bending performance (4PB value) ≥ 700 MPa, and a drop height of ≥ 170 cm with 180-grit sandpaper, demonstrating excellent mechanical strength. Simultaneously, by precisely controlling the crystallization process, aventurine sizes of 10-350 μm, diverse shapes, and rich colors are achieved, eliminating the defect of uneven flashing effects. Furthermore, the transmittance of this aventurine at 550 nm is ≥ 6.5%, and the glass thickness is 0.3–8.0 mm. It is suitable for high-end decorative applications such as display covers and back covers for consumer electronics products, combining high strength, aesthetics, and process compatibility, exhibiting significant technological advancement and market application value. Attached Figure Description

[0044] Figure 1 This is a gradient retemperature crystallization process curve provided in this application; Figure 2 This is a gradient retemperature crystallization process curve specifically used in the first set of embodiments of this application; Figure 3 This is a Venus morphology image of the high-strength Venus glass provided in Embodiment 3 of this application (taken using a red light background of a polarizing microscope). Figure 4 This is a Venus morphology image of the high-strength Venus glass provided in Embodiment 6 of this application (taken using a red-light background of a polarizing microscope). Detailed Implementation

[0045] The embodiments of the present invention will be described in detail below with reference to the examples. However, those skilled in the art will understand that the following examples are only for illustrating the present invention and should not be regarded as limiting the scope of the present invention. Specific conditions not specified in the examples shall be carried out according to conventional conditions or conditions recommended by the manufacturer. Reagents or instruments whose manufacturers are not specified are all conventional products that can be purchased commercially.

[0046] The technical solution of this invention is as follows: Firstly, this application proposes a high-strength aventurine glass with the following characteristics: Venus has a size of 10-350 μm; Transmittance at 550nm ≥ 6.5%; Vickers hardness ≥ 700 MPa; The four-point bending performance is 4PB, and the 4PB value is ≥700 MPa; Drop height of 180-grit sandpaper ≥ 170cm; The glass thickness is 0.3–8.0 mm; Glass density ≥ 2.49 g / cm³ 3 .

[0047] This high-strength aluminosilicate glass is composed of a basic high-aluminosilicate glass component and colorants and reducing agents. To maintain the glass's structural stability, crystallization performance, and coloring shimmer effect, and to avoid the negative impact of colorants and reducing agents on the basic high-aluminosilicate glass system, which could lead to insufficient glass stability and strength, the following conditions must be met: 3.0 ≤ (SiO2+ Al2O3) / (metal colorant+ reducing agent+ Li2O) ≤ 12.0.

[0048] Preferably, the content of the metallic colorant is 0.1-8 wt%, and the content of the reducing agent is 0.1-3 wt%.

[0049] To achieve diverse color representations, colorant components composed of transition metals or rare earth elements need to be added. The use of a single colorant can impart a simple and pure color to glass; the synergistic blending of multiple colorants can create rich and layered shimmering effects. However, because colorant ions possess a strong electric field, they can not only interfere with the crystallization process of the glass itself, but some may also penetrate the crystal structure, altering the mechanical properties of the glass. Therefore, this invention strictly controls the total amount of colorant added to no more than 8%.

[0050] To achieve a rich and varied amber effect, metallic colorants include Fe3O4, Fe2O3, FeO, CuO, Cu2O, Cr2O3, CoO, dichromates, CrO3, MnO2, Co2O3, NiO, V2O5, TiO2, Nd2O3, Pr2O3, and Pr6O. 11 One or more of CeO2, Er2O3, MoO3, WO3, Au and Ag colloids.

[0051] The reducing agent includes one or more of the following: carbon powder, coke powder, tartaric acid, aluminum powder, tin powder, silicon powder, glucose, ethanol, and citric acid.

[0052] Colorant oxides, together with basic components such as SiO2 and Al2O3, form a homogeneous melt, in which the colorant is dispersed in ionic or microparticle form. As the temperature decreases, the crystallization stage begins. Under the action of a reducing agent, the high-valence metal ions in the colorant are reduced to elemental metals or low-valence oxides, which precipitate due to decreased solubility, forming crystal particles of various sizes and shapes (i.e., "gold stars"). Different colorants correspond to specific gold star colors. At the same time, components such as Al2O3 and ZrO2 in the base glass are controlled by regulating melt viscosity and crystallization kinetics, combined with a gradient reheating crystallization process, to ensure uniform distribution of gold stars. The synergistic effect of the proportions of each component ultimately forms gold star glass with high strength and colorful sparkling effects.

[0053] In this application, the base color of the high-strength Venus glass includes any one of brown, black, green, blue, yellow, purple, and pink. The Venus shape is one or more of the following: dotted, dendritic, triangular, quadrilateral, hexagonal, and elongated rhomboid. The Venus color is one or more of the following: turquoise, gold, reddish-brown, silver-white, sky blue, yellow, and pinkish-purple.

[0054] In some preferred embodiments, the high-strength aventurine glass includes any one of brown-based gold-flashed glass, black-based silver-flashed glass, green-based colored-color glass, blue-based colored-color glass, yellow-based colored-color glass, purple-based colored-color glass, and pink-based colored-color glass.

[0055] In this application, the basic high-alumina-silica glass component, in oxide form and by mass percentage, includes: SiO2 55-68%, Al2O3 12-24%, Na2O 3-18%, K2O 0.5-5%, Li2O 0.1-5%, MgO 0.1-8%, ZrO2 0.1-3.0%, and clarifying agent 0.1-2%.

[0056] SiO2 forms the foundation of the network framework in high-alumina aventurine glass, providing the framework, chemical stability, and mechanical strength through its silicon-oxygen tetrahedral structure. Too low a content can lead to incomplete structure, deterioration of weather resistance, crystallization, and uneven aventurine formation; too high a content, on the other hand, affects melting due to high viscosity at high temperatures, hinders metal particle crystallization, and results in poor aventurine flashing effect. In the high-strength aventurine glass of this invention, the SiO2 content ranges from 55% to 68%, preferably 60% to 65%, and more preferably 61% to 63%.

[0057] Al2O3 is incorporated into the silicon-oxygen network of high-alumina aventurine glass as [AlO4] tetrahedra, enhancing mechanical properties such as hardness. It also acts as a viscosity modifier to control viscosity, inhibiting metal particle aggregation and ensuring uniform aventurine distribution. Excessive Al2O3 will lead to increased melting temperature, increased viscosity, uneven aventurine distribution, and difficulty in removing bubbles. In the high-strength aventurine glass of this invention, the Al2O3 content ranges from 15% to 24%, preferably 15% to 21%, and more preferably 17% to 20%.

[0058] Na₂O and K₂O act as strong fluxes, lowering the melting temperature and improving fluidity, thus aiding in the uniform dispersion of asteroides. They also strengthen the glass through ion exchange. However, excessively high content can reduce chemical stability and affect asteroid growth, requiring careful control. In the high-strength asteroid glass of this invention, the Na₂O content ranges from 3% to 18%, preferably 5% to 10%, and more preferably 5% to 8%; the K₂O content ranges from 0.5% to 5%, preferably 1% to 4%, and more preferably 2% to 4%.

[0059] Li2O due to Li + Small radius, in chemical strengthening, and surface K + / Na + The exchange of ions forms a compressive stress layer, improving the glass's impact resistance and abrasion resistance; however, excessive ion exchange increases the tendency for crystallization, interferes with the uniformity of ion exchange, and affects the strengthening adaptability. In the high-strength aventurine glass of this invention, the Li₂O content ranges from 0.1% to 5%, preferably 2% to 5%, and more preferably 3% to 5%.

[0060] MgO, as a network matrix, can reduce melt viscosity, promote uniform distribution of aventurines, and improve mechanical strength and thermal stability. However, excessive MgO can increase crystallization tendency, abnormally increase viscosity, and affect the flash effect and melting process. In the high-strength aventurine glass of this invention, the MgO content ranges from 0 to 8%, preferably 1 to 5%, and more preferably 2 to 4%.

[0061] ZrO2 acts as a nucleating agent, promoting uniform nucleation and refining the size of asteroid crystals, stabilizing the crystals, and strengthening their structure. Excessive ZrO2 will increase melt viscosity, raise melting temperature, and cause agglomeration, affecting uniformity and hindering asteroid growth. In the high-strength asteroid glass of this invention, the ZrO2 content ranges from 0 to 3%, preferably 1 to 3%, and more preferably 2 to 3%.

[0062] To further improve crystallization performance and the mechanical strength of the glass, the following variables also need to be controlled: 2.5 ≤ (SiO2 + Al2O3) / (Na2O + K2O + Li2O) ≤ 8.0.

[0063] 0.2≤ (MgO+2×Li2O) / Al2O3≤ 2.5 3.0 ≤ (SiO2 + Al2O3+ ZrO2) / (Na2O + K2O + Li2O)≤8.0 0.5≤ ZrO2 / (0.5+MgO)≤ 2.0.

[0064] Secondly, this application provides a method for preparing high-strength aventurine glass, comprising: Step S1, Mixing: Mix the raw materials of the basic high aluminosilicate glass component, as well as the metal colorant and reducing agent according to the formula, and use high-pressure airflow pulverization combined with ultrasonic assisted process to mix evenly; Preferably, the high-pressure gas flow pressure is 1.5-2.0 MPa, the ultrasonic power is 200-500 W, the frequency is 40-80 kHz, and the time is 20-40 min. Under these conditions, the basic component raw materials, colorant, and reducing component raw materials can be mixed uniformly, facilitating melting, molding, and uniform crystallization. In some embodiments of the present invention, the high-pressure gas flow pressure can be 1.5 MPa, 1.6 MPa, 1.7 MPa, 1.8 MPa, 1.9 MPa, or 2.0 MPa; the ultrasonic power can be 200 W, 300 W, 400 W, or 500 W; the frequency can be 40 kHz, 50 kHz, 60 kHz, 70 kHz, or 80 kHz; and the time can be 20 min, 25 min, 30 min, 35 min, or 40 min.

[0065] Step S2, Melting and Crystallization: The mixed raw materials are melted and homogenized and crystallized using a gradient reheat crystallization process, then cast and annealed to obtain a glass substrate; Furthermore, the gradient retemperature crystallization process includes at least three heating-cooling stages, and the temperature change curves are as follows: Figure 1 As shown, it includes: (1) Heat the mixed raw materials to the melting temperature T 熔 (Represented as T1 in the diagram), after the raw material is completely melted, the temperature is lowered to T. 核 (Represented as T2 in the diagram) to promote the initial formation of crystal nuclei; Among them, T 熔 1580-1620℃; T 核 The temperature ranges from 1460 to 1500℃. Further, the mixed raw materials are heated to the melting temperature T. 熔 The heating rate is 8-10℃ / min; the temperature of the liquid is reduced to T. 核 The cooling rate is 5-7℃ / min, and no insulation is required.

[0066] Preferably, the first heating is performed by raising the temperature of the high-temperature melting furnace to T at a heating rate of 8~10℃ / min. 熔The temperature is 1580~1620℃, and the holding time is 150~210min. High-alumina glass has a high melting point, requiring a higher melting temperature to achieve complete melting and initial clarification of the raw materials. In some embodiments of this invention, the heating rate can be 8℃ / min, 9℃ / min, or 10℃ / min; the furnace temperature can be 1580℃, 1590℃, 1600℃, 1610℃, or 1620℃; and the holding time can be 150min, 160min, 170min, 180min, 190min, 200min, or 210min.

[0067] Preferably, the first cooling step involves lowering the furnace temperature to 1460-1500°C at a rate of 5-8°C / min. Cooling to a suitable temperature increases the viscosity of the molten glass, promoting crystal nucleation, while a gentle cooling process avoids stress and compositional segregation, ensuring matrix uniformity. In some embodiments of the invention, the cooling rate can be 5°C / min, 6°C / min, 7°C / min, or 8°C / min; the furnace temperature can be 1460°C, 1470°C, 1480°C, 1490°C, or 1500°C.

[0068] (2) Then the temperature is raised to T x After holding at the temperature for X minutes, cool down to T. y The temperature is maintained for Y minutes, and the heating-cooling process is repeated 2-3 times to promote the slow precipitation and stable, uniform growth of Venus crystal nuclei. Among them, T x 1460-1580℃; T y The temperature is 1360-1450℃, and the following relationship is satisfied in each cycle: T 熔 > T x ≥T 核； X is 60-120 min; T 核 > T y Y is 90-210 min.

[0069] The "Venus" effect of aventurine glass originates from light scattering by colloidal particles of metals such as copper and chromium. However, the solubility of metal crystals in silicate melts exhibits a non-linear variation, and a single cooling process can easily lead to explosive nucleation, resulting in coarse or inhomogeneous crystals (losing the starburst effect). To resolve this supersaturation issue, this preferred process employs a continuous heating-cooling process, including a high-temperature stage (Tx ≥ T). 核 Slightly above the nucleation temperature (1460-1500℃), the metal supersaturation is controlled near the critical value to dissolve metastable nuclei, retaining only stable nuclei. In the low-temperature range (Ty=1360-1450℃, less than T...),... 核This region represents the peak of the metal diffusion rate. Increasing supersaturation drives crystal growth, but time must be limited (Y = 90-210 min) to prevent the dissolution of small crystals and the coarsening of large crystals. The heating-cooling process, in the first cycle, forms high-density crystal nuclei. In the subsequent 2-3 cycles, the temperature is repeatedly increased to Tx to dissolve metastable nuclei and screen for highly stable nuclei. Then, the temperature is reduced to Ty, allowing for epitaxial, directional growth on stable nuclei, gradually increasing the crystal size to the optimal light scattering range (10-350 μm). After more than 3 cycles, the improvement in crystal size distribution becomes limited.

[0070] During the heating-cooling process, in order to quickly pass through the phase transformation sensitive region and reduce impurities while avoiding thermal stress, the temperature of the feed liquid is further increased to T. x The temperature is increased at a rate of 2-5℃ / min to avoid overheating and dissolving the crystal nuclei; the temperature of the liquid is then reduced to T. y The temperature is reduced at a rate of 1-4℃ / min to control the stability of the crystal growth interface.

[0071] Furthermore, in step (2), the continuous heating-cooling cycle includes: a. Change the temperature of the feed liquid from T 核 The temperature is increased to T3 at a rate of V3 and held at t3 to promote the homogenization of the glass melt. Preferably, this step is a second heating: the furnace temperature is raised to 1540~1580℃ at a heating rate of 2-5℃ / min, and held for 90~150min. This second heating reduces the viscosity of the molten glass, promotes the diffusion of components after melting, eliminates local component differences, and achieves homogenization of the molten glass. In some embodiments of the present invention, the heating rate can be 2℃ / min, 3℃ / min, 4℃ / min, or 5℃ / min; the furnace temperature can be 1540℃, 1550℃, 1560℃, 1570℃, or 1580℃; and the holding time can be 90min, 100min, 110min, 120min, 130min, 140min, or 150min.

[0072] b. Cool the liquid to temperature T4 at a rate of V4 and hold at that temperature for t4 to induce the formation of "Venus" crystal nuclei; Preferably, this step is a second cooling: the furnace temperature is reduced to 1410~1450℃ at a cooling rate of 2-5℃ / min, and held for 90~120min. After cooling, the viscosity of the molten glass further increases, atomic movement is restricted, which is conducive to the stable formation of crystal nuclei and induces the formation of "Venus" crystal nuclei. In some embodiments of the present invention, the cooling rate can be 2℃ / min, 3℃ / min, 4℃ / min, or 5℃ / min; the furnace temperature can be 1410℃, 1420℃, 1430℃, 1440℃, or 1450℃; and the holding time can be 90min, 100min, 110min, or 120min.

[0073] c. Heat the liquid to temperature T5 at a rate of V5 and hold for t5 to promote crystal growth, while satisfying T3 > T5; Preferably, this step is a third heating: the furnace temperature is raised to 1480~1520℃ at a heating rate of 2-5℃ / min, and held for 90~120min. To accelerate the rate of atomic diffusion to the crystal nucleus and promote crystal growth, it is necessary to precisely control the temperature to be higher than the crystal nucleation temperature but lower than the crystal dissolution temperature. In some embodiments of the present invention, the heating rate can be 2℃ / min, 3℃ / min, 4℃ / min, or 5℃ / min; the furnace temperature can be 1480℃, 1490℃, 1500℃, 1510℃, or 1520℃; and the holding time can be 90min, 100min, 110min, or 120min.

[0074] d. Cool the liquid to temperature T6 at a rate of V6 and hold for t6 to adjust the crystal morphology and distribution, while satisfying T4 ≥ T6; Preferably, this step is a third cooling: the furnace temperature is reduced to 1410-1450℃ at a cooling rate of 2-5℃ / min, and held for 90-150min. To adjust the crystal morphology and enhance the uniformity of the "golden star" distribution, cooling is performed again. In some embodiments of the present invention, the cooling rate can be 2℃ / min, 3℃ / min, 4℃ / min, or 5℃ / min; the furnace temperature can be 1410℃, 1420℃, 1430℃, 1440℃, or 1450℃; and the holding time can be 90min, 100min, 110min, or 120min.

[0075] e. Heat the liquid to temperature T7 at a rate of V7 and hold it at t7 to optimize the optical properties of Venus, while ensuring that T5 ≥ T7. Preferably, this step is a fourth heating: the furnace temperature is raised to 1460-1500℃ at a heating rate of 2-5℃ / min, and held for 30-90min. This second heating balances crystal growth and matrix stability, optimizing the optical properties of the "Venus". In some embodiments of the present invention, the heating rate can be 2℃ / min, 3℃ / min, 4℃ / min, or 5℃ / min; the furnace temperature can be 1460℃, 1470℃, 1480℃, 1490℃, or 1500℃; and the holding time can be 30min, 50min, 70min, or 90min.

[0076] f. Finally, the liquid is cooled to temperature T8 at a rate of V8 and held at that temperature for t8 to stabilize the star-shaped morphology and eliminate internal stress, while satisfying T6 > T8.

[0077] Preferably, this step is the fourth cooling: the furnace temperature is reduced to 1360-1400℃ at a cooling rate of 1-3℃ / min, and held for 150-210min. While ensuring the stable formation of the asteroid pattern, cooling is necessary to eliminate internal stress and prepare for subsequent molding. In some embodiments of the present invention, the heating rate can be 1℃ / min, 3℃ / min, or 3℃ / min; the furnace temperature can be 1360℃, 1370℃, 1380℃, 1390℃, or 1400℃; and the holding time can be 150min, 160min, 170min, 180min, 190min, 200min, or 210min.

[0078] Furthermore, in step af above, the temperature change rate needs to be controlled to satisfy: V3>V4 ≥ V5 ≥ V6≥V7 > V8, and the value range of V3-V8 is 1~5℃ / min. V3 is the largest, corresponding to the first round of heating. At this time, the glass matrix is ​​still in a highly ductile state and can withstand relatively rapid heating. The subsequent rates decrease step by step, especially the last cooling V8, which is the slowest (1℃ / min). This is mainly for controlling the crystal coarsening stage. In the later stage of crystallization, the dissolution rate of small crystals is exponentially related to the growth rate of large crystals, which needs to be suppressed by ultra-low-speed cooling.

[0079] Step S3, Polishing and Strengthening: After cutting the glass substrate, polishing is performed using polishing powder, and finally chemical strengthening is carried out.

[0080] Preferably, the aventurine glass is cut into pieces, CNC machined, and side-scanned according to the required dimensions; Due to the hardness of metallic crystals, polishing powder and a special polishing process are required. Preferably, the main components of the polishing powder include one or more of alumina, silicon carbide, diamond, zirconium oxide, and cerium oxide. In some embodiments of the present invention, the polishing powder used for high-strength aventurine glass can be cerium oxide, zirconium oxide, or alumina.

[0081] Glass polishing includes the following steps: 1) Pretreatment: Ultrasonic cleaning of the glass with deionized water for 15-20 minutes to remove surface impurities and oil stains. In some embodiments of the present invention, the ultrasonic cleaning time with deionized water can be 15 minutes, 16 minutes, 17 minutes, 18 minutes, 19 minutes, or 20 minutes.

[0082] 2) Coarse polishing: Use polishing powder with a particle size of 10-15μm, polishing pressure of 6-20kPa, polishing machine speed of 80-120rpm, and processing time of 10-15min. In some embodiments of the present invention, the particle size of the coarse polishing powder can be 10μm, 11μm, 12μm, 13μm, 14μm, or 15μm; the polishing pressure can be 6kPa, 8kPa, 10kPa, 12kPa, 14kPa, 16kPa, 18kPa, or 20kPa; the polishing machine speed can be 80rpm, 90rpm, 100rpm, 110rpm, or 120rpm; and the processing time can be 10min, 11min, 12min, 13min, 14min, or 15min.

[0083] 3) Fine polishing: Using polishing powder with a particle size of 0.5-1.0 μm, a polishing pressure of 3-10 kPa, a rotation speed of 60-80 rpm, and a processing time of 20-30 min. In some embodiments of the present invention, the particle size of the fine polishing powder can be 0.5 μm, 0.6 μm, 0.7 μm, 0.8 μm, 0.9 μm, or 1.0 μm; the polishing pressure can be 3 kPa, 4 kPa, 5 kPa, 6 kPa, 7 kPa, 8 kPa, 9 kPa, or 10 kPa; the polishing machine rotation speed can be 60 rpm, 65 rpm, 70 rpm, 75 rpm, or 80 rpm; and the processing time can be 20 min, 22 min, 24 min, 26 min, 28 min, or 30 min.

[0084] 4) Cleaning: Ultrasonic cleaning with deionized water for 10-15 minutes. In some embodiments of the present invention, the ultrasonic cleaning time with deionized water can be 10 minutes, 11 minutes, 12 minutes, 13 minutes, 14 minutes, or 15 minutes.

[0085] Furthermore, in the chemical strengthening process, the chemical tempering salt used includes one or more of KNO3, KNO2, KOH, K2CO3, K2SiO3, NaNO3, Na2CO3, Na2SiO3, Al2O3, Al(OH)3, and LiNO3. In some embodiments of the present invention, the chemical tempering salt used for high-strength aventurine glass can be a single tempering salt or a composite tempering salt.

[0086] Furthermore, the two-step chemical strengthening temperature is 200-450℃, and the chemical strengthening time is 30-120 min. In some embodiments of the present invention, the chemical strengthening temperature can be 200℃, 250℃, 300℃, 350℃, 400℃, or 450℃, and the chemical strengthening time can be 30 min, 50 min, 70 min, 90 min, or 120 min.

[0087] Furthermore, during the chemical strengthening process, a high-voltage electric field generation system is used to apply a high-voltage electric field to the chemically tempered molten salt to drive alkali metal ions in the molten salt to migrate to the glass surface, while accelerating the dissolution of target ions in the glass, thereby increasing the ion exchange rate by ≥30% and the compression layer depth by ≥20%, significantly improving processing efficiency.

[0088] Preferably, during the chemical strengthening process, the applied electric field frequency is 0.1-1Hz, the electric field strength is 0.1-10kV / cm, and the electrode spacing is 5-50cm.

[0089] This invention also applies to the application of high-strength aventurine glass in high-end decorative fields, particularly in consumer electronics. The high-strength aventurine glass includes one or more components used in manufacturing front display screen covers for consumer electronics, rear covers assembled on the rear of electronic devices, and camera protective covers. The components are made of high-strength aventurine glass, and the electronic products incorporate all technical solutions related to high-strength aventurine glass.

[0090] The performance of the high-strength Venus glass obtained in the embodiments of this application was tested by the following method: (1) Vickers hardness: measured by a digital Vickers hardness tester HVS-1000AT2.1 in accordance with GB / T 37900-2019; (2) Four-point bending performance 4PB: measured by a universal testing machine according to GB / T 37781-2019; (3) Drop test of 180 grit sandpaper: The drop test of sandpaper was conducted using a drop tester of model XH-YF1000. The test conditions were: 180 grit sandpaper, the total weight of the test glass sample and fixture was 200 grams, the base height was 40 cm, the height was increased by 10 cm each time, and the test was conducted once per height until the glass broke. There were 20 test samples.

[0091] (4) Transmittance: Tested using a Shimadzu SolidSpce-3700i UV-NIR-Vis spectrophotometer, in accordance with standard GB / T 5433-1985.

[0092] The following provides a detailed description of specific embodiments of the present invention. It should be understood that the specific embodiments described herein are for illustrative and explanatory purposes only and are not intended to limit the scope of the invention.

[0093] First set of embodiments This set of embodiments provides a high-strength aventurine glass, the preparation method of which includes: (1) Calculate and weigh the raw materials corresponding to each component according to the distribution ratio of each group in Table 1; (2) The raw materials are thoroughly mixed by high-pressure airflow pulverization and ultrasonic-assisted mixing process and then sent to a high-temperature furnace; the high-pressure airflow pressure is 1.7MPa, the ultrasonic power is 300W, the ultrasonic frequency is 60kHz, and the ultrasonic time is 30min.

[0094] (3) The mixed raw materials are then melted at high temperature through a gradient reheat crystallization process. The temperature curve of the gradient reheat crystallization process is shown in the figure. Figure 2 As shown, the specific steps are as follows: a. Raise the temperature of the high-temperature melting furnace to 1620℃ at a heating rate of 10℃ / min and hold for 180min; b. Reduce the furnace temperature to 1500℃ at a cooling rate of 6℃ / min; c. Raise the furnace temperature to 1580℃ at a heating rate of 4℃ / min and hold for 120min; d. Reduce the furnace temperature to 1450℃ at a cooling rate of 3℃ / min and hold for 90min; e. Raise the furnace temperature to 1520℃ at a heating rate of 3℃ / min and hold for 90min; f. Reduce the furnace temperature to 1450℃ at a cooling rate of 3℃ / min and hold for 120min; g. Raise the furnace temperature to 1500℃ at a heating rate of 2℃ / min and hold for 60min; h. Reduce the furnace temperature to 1400℃ at a cooling rate of 1℃ / min and hold for 180min.

[0095] (4) The molten glass was then homogenized, shaped, annealed, and the basic aventurine glass was obtained. The annealing temperature was 550℃ and the holding time was 120min.

[0096] (5) The base asteroid glass is cut, CNC machined, side-scanned, and polished. The pre-polishing time is 15 min; rough polishing uses 15 μm zirconia with a particle size of 16 kPa and a speed of 100 rpm for 15 min; fine polishing uses 0.5 μm zirconia with a particle size of 8 kPa and a speed of 70 rpm for 30 min.

[0097] (6) The polished glass (0.6 mm) is subjected to two-step chemical strengthening in a chemical strengthening high-energy field auxiliary equipment, wherein the electric field strength is 5 kV / cm, the electric field frequency is 0.5 MHz, and the electrode spacing is 20 cm.

[0098] First chemical strengthening: molten salt NaNO3:KNO3=60%:40%, temperature 400℃, strengthening time 90min.

[0099] Second chemical strengthening: molten salt NaNO3:KNO3:KOH:K2SiO3=3%:97%:0.1%:0.2%, temperature 400℃, strengthening time 90min.

[0100] After completion, the product is placed in a muffle furnace for rapid cooling; the product is then washed with deionized water to obtain high-strength aventurine glass, and the performance of the obtained high-strength aventurine glass is tested.

[0101] Table 1. Composition of high-strength aventurine glass in Examples 1-7

[0102] Comparative Examples 1-7 The operation was carried out under the same conditions as in Examples 1-7, except that the composition of each raw material was as shown in Table 2.

[0103] Table 2. Composition of Venus Glass in Comparative Examples 1-7

[0104] As can be seen from Tables 1 and 2: Compared to Examples 1-5, the Al2O3 content in the glass frit of Comparative Examples 1-5 was relatively low (6-14%). Even with the same colorant, reducing agent, and chemical strengthening process, the Vickers hardness, 4PB, and 180-grit sandpaper drop of the resulting aventurine glass were all at lower levels. Furthermore, the aventurine glass effect was poor, exhibiting unevenness or the absence of aventurine particles. This was mainly due to an imbalance in the proportions of key components (such as an imbalance in the synergistic effect of ZrO2 and MgO), and excessive or insufficient content of core components (such as too low Al2O3 content or too high ZrO2 content). This resulted in excessively low melt viscosity, particle agglomeration, or phase separation, disrupting the uniform dispersion and crystallization conditions of metal ions. Ultimately, this led to the inability to precipitate aventurine particles (Comparative Examples 3-5) or uneven distribution of aventurine particles. Examples 1-5, however, ensured uniform aventurine particle precipitation through strict control of the proportions of each component. Compared to Example 6, Comparative Example 6 did not use a reducing agent to provide a reducing atmosphere, preventing the metal oxides from being reduced to elemental metals, thus resulting in no aventurine particle precipitation. Compared to Example 7, Comparative Example 7 increased the amount of colorant while keeping the amount of reducing agent constant, which prevented the colorant from being completely reduced to the metallic element and precipitated. As a result, the gold stars were smaller and unevenly distributed.

[0105] Second set of embodiments

[0106] The difference between this set of embodiments and Embodiment 3 lies in the gradient retemperature crystallization process in step (3), while other process parameters and raw material components are the same. The specific gradient retemperature crystallization process and performance test results are shown in Table 3.

[0107] Table 3. Gradient retemperature crystallization process and performance test results

[0108] Comparative Examples 8-14 The difference between this comparative example and Example 8 lies in the different gradient reheat crystallization process, as shown in Table 4: Table 4. Comparative results of gradient retemperature crystallization process and performance test.

[0109] As can be seen from Tables 3 and 4: Combining Example 8 and Comparative Examples 8-10, it can be seen that in the gradient reheat crystallization process, the number of heating-cooling cycles has a significant impact on the aventurine effect of the glass, and also affects the strength of the glass. Comparative Example 8 uses direct cooling after melting; Comparative Example 9 uses one heating-cooling cycle after initial nucleation; Comparative Example 10 uses one heating-cooling cycle after initial nucleation, and holds at the nucleation temperature for 90 minutes. The aventurine glasses obtained in these three cases have no aventurine precipitation or only a small amount of small aventurine particles. This is mainly because the multiple heating and cooling cycles control the melt viscosity and atomic diffusion in stages, meeting the requirements of the entire process of aventurine crystal nucleation, growth, and morphological stability. Reducing the number of heating and cooling cycles will disrupt this balance, resulting in difficulty in aventurine precipitation or a small amount of small aventurine particles.

[0110] As can be seen from Example 8 and Comparative Examples 11-12, in each heating-cooling cycle, Tx ≥ T 核 T 核 >T y This helps improve the nucleation and precipitation rate of Venus crystals, mainly because it accelerates the rate of atomic diffusion to the crystal nucleus, providing sufficient power for crystal nucleus growth and ensuring that the Venus crystals can grow fully. This avoids stagnation of crystal nucleus growth due to insufficient temperature, thereby ensuring the normal formation and appropriate size of Venus crystals. As can be seen from Example 8 and Comparative Examples 13-14, the heating rate has a significant impact on the Venus crystal formation effect in each heating-cooling cycle. This is because precise control of melt viscosity and atomic diffusion is required to ensure that the raw materials are fully melted, the composition is uniform, and the crystal nuclei form stably, avoiding difficulties in Venus crystal precipitation, uneven distribution, or abnormal size due to improper heating rates.

[0111] Third set of embodiments The difference between this set of embodiments and Embodiment 3 lies in the polishing process parameters in step (5), while other process parameters and raw material components are the same. Specific process parameters and performance test results are shown in Table 5.

[0112] Table 5. Polishing process parameters

[0113] Fourth set of embodiments The difference between this set of embodiments and Embodiment 3 lies in the chemical strengthening process parameters in step (6), while other process parameters and raw material components are the same. Specific process parameters and performance test results are shown in Table 6.

[0114] Table 6.

[0115] As shown in Tables 5 and 6, the aventurine glass prepared using the polishing and chemical strengthening processes described in this application exhibits excellent strength and mechanical properties after chemical strengthening. Furthermore, as demonstrated in Examples 27 and 28, applying a high-voltage electric field to the chemically tempered molten salt using a high-voltage electric field generation system during the chemical strengthening process helps improve the Vickers hardness, 4PB, and 180-grit sandpaper drop test of the glass.

[0116] This specific embodiment is merely an explanation of this application and is not intended to limit it. After reading this specification, those skilled in the art can make modifications to this embodiment without contributing any inventive step, but such modifications are protected by patent law as long as they fall within the scope of the claims of this application.

Claims

1. A high-strength aventurine glass, characterized in that, The high-strength aventurine glass has a aventurine size of 10-350μm, a light transmittance of ≥6.5% at 550nm, and a Vickers hardness of ≥700MPa.

2. The high-strength aventurine glass according to claim 1, characterized in that, The high-strength aluminosilicate glass is composed of basic high-aluminosilicate glass components and metallic colorants and reducing agents; and meets the following conditions: 3.0 ≤ (SiO2+ Al2O3) / (metal colorant+ reducing agent+ Li2O) ≤ 12.

0.

3. The high-strength aventurine glass according to claim 1, characterized in that, The basic high-alumina-silicon glass composition includes SiO2, Al2O3, Na2O, K2O and Li2O, wherein the content of SiO2 is 55-68 wt% and the content of Al2O3 is 15-24 wt%.

4. The high-strength aventurine glass according to any one of claims 1-3, characterized in that, The content of the metallic colorant is 0.1-8 wt%, and the content of the reducing agent is 0.1-3 wt%.

5. The high-strength aventurine glass according to any one of claims 1-3, characterized in that, The high-strength aluminosilicate glass substrate is obtained by mixing the raw materials of basic high-aluminosilicate glass, metal colorant, and reducing agent, then melting and homogenizing the mixed raw materials using a gradient reheat crystallization process, followed by casting and annealing.

6. The high-strength aventurine glass according to claim 5, characterized in that, The gradient retemperature crystallization process includes at least three heating-cooling stages, including: (1) Heat the mixed raw materials to the melting temperature T 熔 After the raw materials are completely melted, the temperature is lowered to T. 核 To promote the initial formation of crystal nuclei; (2) Then the temperature is raised to T x After holding at the temperature for X minutes, cool down to T. y The temperature is maintained for Y minutes, and the heating-cooling process is repeated 2-3 times to promote the slow precipitation and stable, uniform growth of Venus crystal nuclei. Among them, T 熔 1580-1620℃; T 核 1460-1500℃; T x 1460-1580℃; T y The temperature range is 1360-1450℃, and the following relationship is satisfied in each cycle: T 熔 > T x ≥T 核； X is 60-120 min; T 核 > T y Y is 90-210 min.

7. The high-strength aventurine glass according to claim 6, characterized in that, In step (1), the mixed raw materials are heated to the melting temperature T. 熔 The heating rate is 8-10℃ / min; the temperature of the liquid is reduced to T. 核 The cooling rate is 5-7℃ / min, and no insulation is required.

8. The high-strength aventurine glass according to claim 6, characterized in that, In step (2), the temperature of the liquid is raised to T. x The temperature rise rate is 2-5℃ / min; the temperature of the feed liquid is reduced to T. y The temperature drops at a rate of 1-4℃ / min.

9. The high-strength aventurine glass according to claim 8, characterized in that, In step (2), the continuous heating-cooling cycle includes: a. Change the temperature of the feed liquid from T 核 The temperature is increased to T3 at a rate of V3 and held at t3 to promote the homogenization of the glass melt. b. Cool the liquid to temperature T4 at a rate of V4 and hold at that temperature for t4 to induce the formation of "Venus" crystal nuclei; c. Heat the liquid to temperature T5 at a rate of V5 and hold for t5 to promote crystal growth, while satisfying T3 > T5; d. Cool the liquid to temperature T6 at a rate of V6 and hold for t6 to adjust the crystal morphology and distribution, while satisfying T4 ≥ T6; e. Heat the liquid to temperature T7 at a rate of V7 and hold it at t7 to optimize the optical properties of Venus, while ensuring that T5 ≥ T7. f. Finally, the liquid is cooled to temperature T8 at a rate of V8 and held at that temperature for t8 to stabilize the star-shaped morphology and eliminate internal stress, while satisfying T6 > T8.

10. The high-strength aventurine glass according to claim 9, characterized in that, In step (2), the rate of temperature change satisfies: V3>V4 ≥ V5 ≥ V6 ≥ V7 > V8, and the range of V3-V8 is 1-5℃ / min.

11. The high-strength aventurine glass according to claim 3, characterized in that, The basic high-alumina-silicon glass components, by weight percentage, are: SiO2 55-68 wt%, Al2O3 15-24 wt%, Na2O 3-18 wt%, K2O 0.5-5 wt%, and Li2O 0.1-5 wt%.

12. The high-strength aventurine glass according to claim 11, characterized in that, The basic high-alumina-silicon glass component also includes MgO and ZrO2, as well as a clarifying agent; The MgO content is 0.1–8 wt%, the ZrO2 content is 0.1–3 wt%, and the clarifying agent content is 0.1–2 wt%.

13. The high-strength aventurine glass according to claim 12, characterized in that, The basic high-alumina-silicon glass composition satisfies: 2.5 ≤ (SiO2+ Al2O3) / (Na2O + K2O + Li2O) ≤ 8.

0.

14. The high-strength aventurine glass according to claim 12, characterized in that, The basic high-alumina-silicon glass component satisfies: 0.2≤(MgO+2×Li2O) / Al2O3≤ 2.

5.

15. The high-strength aventurine glass according to claim 12, characterized in that, The basic high-alumina-silicon glass composition satisfies: 3.0 ≤ (SiO2+ Al2O3+ ZrO2) / (Na2O + K2O + Li2O) ≤ 8.

0.

16. The high-strength aventurine glass according to claim 5, characterized in that, The metallic colorants include Fe3O4, Fe2O3, FeO, CuO, Cu2O, Cr2O3, CoO, dichromate, CrO3, MnO2, Co2O3, NiO, V2O5, TiO2, Nd2O3, Pr2O3, and Pr6O. 11 One or more of CeO2, Er2O3, MoO3, WO3, Au and Ag colloids.

17. The high-strength aventurine glass according to claim 5, characterized in that, The reducing agent includes one or more of the following: carbon powder, coke powder, tartaric acid, aluminum powder, tin powder, silicon powder, glucose, ethanol, and citric acid.

18. The high-strength aventurine glass according to claim 12, characterized in that, The clarifying agent includes SO4. 2- NO3 - F - Cl - One or more of SnO2.

19. The high-strength aventurine glass according to claim 1, characterized in that, The base color of the high-strength Venus glass includes any one of brown, black, green, blue, yellow, purple, and pink.

20. The high-strength aventurine glass according to claim 1, characterized in that, The high-strength Venus glass has a Venus shape that is one or more of the following: dot-shaped, dendritic, triangular, quadrilateral, hexagonal, and elongated oblique square.

21. The high-strength aventurine glass according to claim 19, characterized in that, The high-strength aventurine glass has a aventurine color that is one or more of the following: turquoise, gold, reddish-brown, silver-white, sky blue, yellow, and pinkish-purple.

22. The high-strength aventurine glass according to claim 21, characterized in that, The high-strength aventurine glass includes any one of the following: brown base gold-flashed glass, black base silver-flashed glass, green base colored-color glass, blue base colored-color glass, yellow base colored-color glass, purple base colored-color glass, and pink base colored-color glass.

23. The high-strength aventurine glass according to claim 1, characterized in that, The high-strength aventurine glass has a four-point bending performance of 4PB, with a 4PB value ≥ 700 MPa; a drop height of ≥ 170 cm with 180-grit sandpaper; and a glass thickness of 0.3–8.0 mm.

24. A method for preparing high-strength aventurine glass as described in any one of claims 1-23, characterized in that, It includes: The raw materials of the basic high aluminosilicate glass component, along with the metal colorant and reducing agent, are mixed according to the formula and then mixed evenly using a high-pressure airflow pulverization combined with ultrasonic-assisted process. A gradient reheat crystallization process is used to melt and homogenize the mixed raw materials, followed by casting and annealing to obtain a glass substrate; After the glass substrate is cut, it is polished with polishing powder and finally chemically strengthened.

25. The method for preparing high-strength aventurine glass according to claim 24, characterized in that, The parameters of the high-pressure airflow pulverization combined with ultrasonic assistance process include: high-pressure airflow pressure of 1.5-2.0 MPa, ultrasonic power of 200-500 W, frequency of 40-80 kHz, and time of 20-40 min.

26. The method for preparing high-strength aventurine glass according to claim 24, characterized in that, During the preparation of glass substrates, the annealing temperature is 500-560℃, and the temperature is maintained for 120-180 minutes before being cooled to room temperature in the furnace.

27. The method for preparing high-strength aventurine glass according to claim 24, characterized in that, During the polishing process, the polishing powder is one or more of alumina, silicon carbide, diamond, zirconium oxide, and cerium oxide.

28. The method for preparing the glass substrate of high-strength aventurine glass according to claim 24, characterized in that, The polishing process includes rough polishing and fine polishing; The coarse polishing includes using polishing powder with a particle size of 10-15μm, a polishing pressure of 6-20kPa, a polishing machine speed of 80-120rpm, and a processing time of 10-15min; The fine polishing process involves using polishing powder with a particle size of 0.5-1μm, a polishing pressure of 3-10kPa, a rotation speed of 60-80rpm, and a processing time of 20-30min.

29. The method for preparing high-strength aventurine glass according to claim 24, characterized in that, In the chemical strengthening process, the chemical tempering molten salt used includes one or more of KNO3, KNO2, KOH, K2CO3, K2SiO3, NaNO3, Na2CO3, Na2SiO3, Al2O3, Al(OH)3, and LiNO3.

30. The method for preparing high-strength aventurine glass according to claim 24, characterized in that, The chemical strengthening is a two-step chemical strengthening method, with a temperature of 200-450℃ and a strengthening time of 30-120min.

31. The method for preparing high-strength aventurine glass according to claim 24, characterized in that, In the chemical strengthening process, a high-voltage electric field generation system is used to apply a high-voltage electric field to the chemically hardened molten salt.

32. The method for preparing high-strength aventurine glass according to claim 31, characterized in that, In the chemical strengthening process, the applied electric field frequency is 0.1-1 Hz, the electric field strength is 0.1-10 kV / cm, and the electrode spacing is 5-50 cm.

33. The application of high-strength aventurine glass as described in any one of claims 1-23 in high-end consumer electronics products.

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