Multicolor intermelting glass matrix with low softening point and high refractive index and application thereof

Abstract

This invention relates to the field of advanced inorganic non-metallic materials, and discloses a multicolor intermetallic glass matrix with a low softening point and high refractive index, and its applications. The matrix comprises: silicon dioxide, sodium oxide, potassium oxide, zinc oxide, barium oxide, titanium dioxide, boron oxide, and antimony oxide, and is lead-free. A specific microstructure is constructed: the molar ratio of zinc oxide to titanium dioxide is locked at 2.8 to 3.2 to form zinc-titanium coupled tetrahedral clusters, and the molar ratio of potassium oxide to the total alkali metal is locked at 0.41 to 0.46 to construct mixed alkali volume blocking channels. Through the above microstructure control, this invention maintains a low softening point ≤535℃ and a high refractive index n D While achieving a value of ≥1.515, tetrahedral clusters are used to consume free non-bridging oxygen and the volume blocking effect is used to suppress the migration of alkali metal ions, thereby eliminating the interfacial crystallization and fogging phenomena during the hot-melt splicing of dissimilar colored glasses, and improving the interfacial optical uniformity and structural stability of multicolor interfacial products.

Description

Technical Field

[0001] This invention relates to a multicolor intermetallic glass matrix with low softening point and high refractive index and its applications, belonging to the field of advanced inorganic non-metallic materials technology. Background Technology

[0002] In the current field of advanced inorganic non-metallic materials, precision lost-wax casting, optical decoration and multi-color glass processes place demands on the thermal processing performance and optical quality of the glass matrix. To reduce the softening temperature of glass while maintaining a high refractive index, it is usually necessary to introduce high molar fractions of alkali metal oxides or boron oxide into the silicate network. Alkali metal ions are used to break the silicon-oxygen tetrahedral framework to reduce viscosity, and high refractive index components such as titanium and zirconium are added.

[0003] Existing technologies relying on high-concentration alkali metals to break down the glass network and reduce viscosity suffer from deep-seated structural defects in multi-colored glass interfusion or dissimilar glass hot-melt stacking scenarios. While the introduction of large amounts of alkali metal ions lowers the softening point, it generates high concentrations of non-bridging oxygen in the glass network. These high-energy non-bridging oxygens are highly chemically reactive. During the hot-melt bonding process, when they come into contact with dissimilar glasses containing copper or cobalt transition metal coloring ions, interfacial migration and coordination reactions occur driven by chemical potential. This microscopic chemical instability manifests macroscopically as follows: 1. Phase separation or crystallization is induced at the bonding interface due to element inter-diffusion and local component depletion, forming a fogging zone or devitrification layer, which destroys optical uniformity; 2. Ion exchange between different color blocks leads to distortion of the interfacial stress field, making the product prone to internal cracks or shattering during cooling; 3. Simply adding titanium or zinc intermediate oxides to increase the refractive index easily forms octahedral coordination precursor structures in alkaline environments, raising the liquidus temperature, reducing low-temperature resistance to crystallization, and limiting the operating temperature range of precision forming processes. Although the industry has attempted to address this issue... Adjusting the formulation to balance performance often focuses on simple macroscopic component adjustments, neglecting the decisive role of microstructure in interface stability. For example, Chinese invention patent application CN106316115A discloses a lead-free high-gloss glass. Although it introduces barium oxide as a flux and combines it with titanium dioxide and zirconium dioxide to achieve lead-free properties and improve gloss, this solution is essentially still a conventional oxide doping method. It does not involve the induction and regulation of cation coordination configuration within the glass network. In a high-alkali melt environment, the lack of a specific coordination field to constrain titanium ions to form unstable octahedral coordination precursors prevents the construction of structural units that consume free non-bridging oxygen and increase the liquidus temperature. Such solutions do not construct a volume blocking mechanism for alkali metal ion migration channels, resulting in the inability to block the chemical potential-driven ion inter-diffusion on both sides of the interface when hot-melt splicing with heterogeneous colored glass. This leads to interface crystallization and fogging, making it difficult to meet the interface quality and dimensional stability requirements of multicolor precision optical devices.

[0004] Therefore, the technical problem to be solved by this invention is how to passivate the non-bridging oxygen activity through specific component design and structural regulation in a high-alkali-content, low-melting-point system, while ensuring a low softening point and high refractive index, and improving the inertness of the glass matrix to the multicolor coloring ion structure and the interface stability. Summary of the Invention

[0005] To address the problems mentioned in the background art, the technical solution of the present invention is as follows: a multicolor intermetallic glass matrix with a low softening point and high refractive index, wherein the glass matrix is ​​composed of the following components by weight percentage of oxides:

[0006] The glass matrix comprises 42.0% to 48.0% silicon dioxide, 8.0% to 12.0% sodium oxide, 10.0% to 14.0% potassium oxide, 12.0% to 16.0% zinc oxide, 8.0% to 13.0% barium oxide, 3.0% to 5.0% titanium dioxide, 2.0% to 4.0% boron oxide, and 0.1% to 0.5% antimony oxide; the glass matrix is ​​lead-free, its softening temperature is not higher than 535℃, and its refractive index nD is not lower than 1.515.

[0007] The cation coordination network within the glass matrix follows the following microstructure construction rules that passivate the activity of non-bridging oxygen:

[0008] First, construct zinc-titanium coupled tetrahedral clusters to lock structural oxygen: limit the molar ratio of zinc oxide to titanium dioxide to the range of 2.8 to 3.2, and utilize the coordination field effect generated by excess zinc ions to transform titanium ions from octahedral coordination to tetrahedral coordination in an alkaline environment, and form clusters with zinc-oxygen tetrahedra through shared vertex connection, thereby consuming the free non-bridged oxygen generated by alkali metal bond breaking;

[0009] Second, a mixed alkali volume blocking channel is constructed to limit ion migration: the molar ratio of potassium oxide to alkali metal oxide is limited to the range of 0.41 to 0.46. The difference in ionic radii between potassium ions and sodium ions is used to form a stacked state with maximum filling density in the interstices of the silicon-oxygen network. This ensures that the diffusion coefficient of alkali metal ions is in a low energy level determined by the volume blocking effect within the interfusion temperature range of 530°C to 550°C of the glass matrix, thereby inhibiting the penetration and crystallization of dissimilar coloring ions at the interfusion interface.

[0010] Preferably, the glass matrix undergoes a structural freezing treatment with a specific thermal history during preparation. After holding the glass matrix at 550°C for 4 hours, no crystal nuclei larger than 50 nanometers are formed inside it. Furthermore, when the glass matrix and the silicate material doped with transition metal chromophore ions are hot-melted and joined at 535°C, the thickness of the element diffusion layer at the interface is less than the wavelength of visible light, and there is no microcrystalline precipitation or optical scattering haze in the interface region. The linear thermal expansion coefficient of the glass matrix is ​​95 × 10⁻⁶ in the range of 20°C to 300°C.-7 / ℃ to 105×10 -7 / ℃, to ensure residual stress matching at the multi-component composite interface after cooling.

[0011] Preferably, silica is used as the network former, and the raw material is quartz sand with a silica content of not less than 99.5% and an iron oxide content of not more than 0.01%. Sodium oxide and potassium oxide are introduced by sodium carbonate and potassium carbonate, respectively, and decompose and release carbon dioxide in the high-temperature melting stage of 1340℃ to 1360℃. Mechanical stirring promotes the uniform distribution of cations in the melt and eliminates the interference of component segregation on the construction rules of the microstructure.

[0012] Preferably, to ensure that the glass matrix maintains sufficient network rigidity and refractive index packing density under low softening point conditions, the mass ratio of the total amount of divalent metal oxides in the glass matrix to the mass of the network-forming silicon dioxide satisfies the following network stability criterion formula: (w(ZnO)+w(BaO)) / (w(SiO2))≥0.5, where w(ZnO), w(BaO), and w(SiO2) represent the weight percentage values ​​of zinc oxide, barium oxide, and silicon dioxide in the glass matrix, respectively. This formula limits the mass space occupation relationship between the network modifier and the network-forming body to ensure that the glass density is not less than 2.65 g / cm³.

[0013] Preferably, zinc oxide serves as a network intermediate, preferentially occupying tetrahedral sites in the glass matrix to form [ZnO4] structural units; barium oxide serves as a network exogenous body, filling the voids formed by the connection between [ZnO4] and [SiO4] structural units. The high polarizability of barium ions contributes to the high refractive index of the glass matrix, while its large ionic radius further impedes the migration channels of alkali metal ions.

[0014] Preferably, the preparation method of the glass matrix includes: melting and clarifying the batch material at a temperature of 1350°C, casting the molten glass into a mold, and holding it at a precision annealing temperature of 490°C for at least 4 hours; the precision annealing temperature is set to be 10°C to 20°C higher than the glass transition temperature to allow zinc-titanium coupled tetrahedral clusters to complete the relaxation and locking of the topological structure in the supercooled liquid phase region, preventing structural defects caused by rapid cooling; and the glass matrix exhibits low surface tension and high wettability rheological characteristics to adapt to flow in micron-scale confined spaces, and has a low viscosity temperature coefficient in the Newtonian fluid behavior temperature range of 530°C to 560°C, which allows the glass melt to fill the fine topological structure under the drive of surface tension without devitrification.

[0015] Preferably, boron oxide enters the glass network in the form of [BO3]trigonal or [BO4] tetrahedron, and its content is controlled between 2.0% and 4.0%. This is used to help reduce the melting temperature and suppress micro-phase separation caused by liquid phase immiscibility without compromising the stability of the zinc-titanium coupled tetrahedral clusters.

[0016] Preferably, the ratio of the total molar amount of alkali metal ions to the total molar amount of aluminum ions in the glass matrix is ​​greater than 10, and the glass matrix is ​​substantially free of aluminum oxide to avoid aluminum ions competing for oxygen ions and thus interfering with the formation of zinc-titanium coupled tetrahedral clusters; antimony oxide is used as a clarifying agent to release oxygen at high temperatures to remove microbubbles in the glass melt through a physical bubble-carrying mechanism; the glass matrix is ​​essentially an isotropic photon transmission continuous medium and a thermodynamically dimensionally stable body, which can have a thermal expansion coefficient difference of 5 × 10⁻⁶. -7 The heterogeneous amorphous materials in the / ℃ range achieve chemical bonding without interfacial stress gradient; the glass matrix has a transmittance of not less than 90% in the visible light band and has a characteristic absorption edge in the ultraviolet light band, which is determined by the band structure of zinc oxide and titanium dioxide.

[0017] Application of a low softening point, high refractive index multicolor interfused glass matrix in the preparation of multicolor hot-melt glass products.

[0018] Application of a low softening point, high refractive index multicolor intermetallic glass matrix in the fabrication of precision cast optical devices.

[0019] Compared with the prior art, the beneficial effects of the present invention are:

[0020] 1. In multicolor interfused glass with low softening point and high refractive index, a specific molar ratio range of zinc to titanium is defined to establish a cation competitive coordination environment in the alkali-rich melt. Excess zinc ions preferentially occupy tetrahedral sites, generating a strong coordination field, which causes the coordination configuration of titanium ions to reverse from octahedral to tetrahedral. They then connect with zinc-oxygen tetrahedra to form a supertetrahedral cluster structure. The cluster formation process consumes alkali metal bond breaking to generate free non-bridging oxygen, converting highly reactive terminal oxygen into structurally stable bridging oxygen. This mechanism reduces the chemical potential energy of the matrix, allowing the low softening point glass to maintain structural inertness when it comes into thermal contact with transition metal colored glass. It also suppresses the inter-element diffusion and local crystallization induced by the enrichment of non-bridging oxygen at the interface, ensuring the optical uniformity and mechanical bonding strength of the multicolor interfused interface.

[0021] 2. By utilizing a specific molar ratio of two alkali metal ions with different radii, a maximum filling density volume blocking effect is constructed in the ion transport channels of the glass network gaps. The specific stacking state leads to an increase in the activation energy of alkali metal ions near the glass transition temperature, which restricts the long-range migration ability of cations. This results in the matrix exhibiting extremely low DC conductivity and ion diffusion coefficient. During the assembly of multi-color glass or the secondary heat processing of internal carving, the blocking effect forms a chemical diffusion barrier, which hinders the penetration of dissimilar coloring ions across the interface, avoids dispersion and haze and the formation of secondary phases, and achieves clear and sharp multi-color interface contours and stable stress field matching while maintaining low melting point characteristics.

[0022] 3. By utilizing zinc-titanium coupled clusters to fill and repair the silicon-oxygen framework, the dependence of traditional high-refractive-index glass on easily crystallizing components is overcome. This provides a high-density electron cloud for specific microstructural units to enhance the refractive index, while maintaining structural compatibility with the silicon-oxygen tetrahedral network in terms of geometry and topology. It also suppresses the aggregation and nucleation tendency of titanium ions as crystal nucleating agents. The structural design enables the glass to maintain a wide anti-crystallization temperature range under conditions of lower softening point, avoiding optical quality degradation due to devitrification during long-term heat preservation in tunnel furnaces or complex hot bending processes. This provides rheological stability and yield assurance for the application of low-softening-point high-refractive-index glass in precision casting processes for complex shapes. Attached Figure Description

[0023] Figure 1 This is a process flow diagram for preparing the low softening point, high refractive index glass matrix of the present invention;

[0024] Figure 2 This is a comparison diagram of Cu ion diffusion depth and interfacial stress after hot-melt splicing of the sample group and the control group of the present invention;

[0025] Figure 3 This is a schematic diagram illustrating the microstructure construction rules of the glass matrix and the mechanism of multicolor interfusion interface in this invention. Detailed Implementation

[0026] The present invention will now be described in detail with reference to specific embodiments. It should be understood that the specific embodiments described herein are merely for explaining the present invention and are not intended to limit the present invention.

[0027] This invention provides a multicolor intermetallic glass matrix with a low softening point and high refractive index, composed of silicon dioxide, sodium oxide, potassium oxide, zinc oxide, barium oxide, titanium dioxide, boron oxide, and antimony oxide, and free of lead. This glass matrix, through specific oxide component design and molar ratio control, achieves a softening point temperature not exceeding 535℃ and a refractive index n... DUnder conditions not lower than 1.515, structural suppression of heterogeneous coloring ion diffusion is achieved. This matrix can chemically bond with colored glasses doped with transition metal ions within the hot-melt range of 530℃ to 550℃, with no visible crystallization or fogging at the interface. To solve the problem of crystallization induced at the multicolor interfacial due to excessive non-bridging oxygen concentration caused by high alkali content in traditional low softening point glasses, this invention consumes free oxygen through a zinc-titanium coordination regulation mechanism. In the glass composition design, the molar ratio of zinc oxide to titanium dioxide, n(ZnO) / n(TiO2), is controlled within the range of 2.8 to 3.2. Under this stoichiometric constraint, excess zinc ions (ZnO) in the melt are eliminated. 2+ The preferential occupation of oxygen coordination sites leads to the formation of [ZnO4] tetrahedra, and the resulting strong coordination field effect enables titanium ions (Ti) to preferentially occupy oxygen coordination sites to form [ZnO4] tetrahedra. 4+ The [TiO6] octahedral structure transforms into the [TiO4] tetrahedral form. Every three [ZnO4] units are connected to [TiO4] units through a common apical oxygen atom, and self-assemble to form [Zn3Ti] tetrahedral clusters. These clusters act as network intermediates, filling the fracture points of the [SiO4] framework. They consume the non-bridging oxygen introduced by the alkali metal and convert the highly active terminal oxygen into structurally stable bridging oxygen. This eliminates the microcrystal nucleation driving force caused by the enrichment of non-bridging oxygen at the multicolor intermetallic interface.

[0028] To suppress interfacial refractive index gradient distortion and internal stress cracking caused by the interdiffusion of alkali metal ions during multi-color glass splicing, this invention utilizes the dual-alkali volume blocking effect to restrict ion migration. The ratio of potassium oxide to the total amount of alkali metal oxides, n(K₂O) / [n(Na₂O)+n(K₂O)], is limited to the range of 0.41 to 0.46. Within this molar fraction window, potassium ions with an ionic radius of 1.38 Å and sodium ions with an ionic radius of 1.02 Å form a maximum packing density in the ion transport channels of the silicon-oxygen network. This packing state increases the activation energy required for alkali metal ion transitions, keeping the self-diffusion coefficient of alkali metal ions at a low energy level within the interfusion temperature range of 530°C to 550°C in the glass matrix. This hinders the penetration of coloring ions across the interface from dissimilar glasses, ensuring residual stress matching after cooling of multi-color products. The glass matrix has a defined chemical composition range, comprising, by weight percentage of oxides, 42.0% silicon dioxide. Up to 48.0%, as a network forming body to maintain the rigidity of the framework; sodium oxide 8.0% to 12.0% and potassium oxide 10.0% to 14.0%, as mixed alkali flux to lower the melting temperature and provide a blocking effect; zinc oxide 12.0% to 16.0% and titanium dioxide 3.0% to 5.0%, as structural remodeling and refractive index enhancers to synergistically improve the refractive index and suppress crystallization; barium oxide 8.0% to 13.0%, as a network expanse to improve glass density and refractive index; boron oxide 2.0% to 4.0%, to assist in suppressing phase separation; antimony oxide 0.1% to 0.5%, as a clarifying agent. Meanwhile, the mass ratio of the total amount of divalent metal oxides to silicon dioxide satisfies the network stability criterion of [w(ZnO) + w(BaO)] / w(SiO2) ≥ 0.5 to ensure the physical stability of the glass network at low softening points. To further verify the network evolution process of the glass matrix at the atomic scale, the prepared sample groups were subjected to precise physicochemical property analysis at 900 cm⁻¹. -1 Up to 1100cm -1Structural feature analysis within the wavenumber range shows that the signal intensity of the highly connected structural units belonging to the silicon-oxygen tetrahedron increases with the locking ratio of zinc oxide to titanium dioxide, quantitatively reflecting the effective reduction of the concentration of free non-bridging oxygen and the substantial improvement of network backbone connectivity. Analysis of oxygen atom energy level characteristics indicates that the proportion corresponding to bridging oxygen signals significantly increases from the 65% level of conventional components to over 80%, confirming that the [Zn3Ti] supertetrahedral cluster has a strong ability to capture and lock highly reactive terminal oxygen generated by alkali metal bond breaking. Furthermore, observation of the near-edge absorption characteristics of titanium reveals that the characteristic energy positions of titanium ions highly match the standard tetrahedral coordination model, significantly different from the octahedral coordination characteristics in conventional silicate environments. This finding clearly confirms that under the specific stoichiometric constraints and precision annealing heat history of this invention, titanium ions indeed undergo a configurational reversal from octahedral to tetrahedral coordination and successfully assemble with zinc-oxygen units into a stable topological junction. The building blocks of this invention, through the synergistic regulation of the microstructure and properties, exhibit the following technological performance in practical engineering applications: In the application scenario of preparing multi-color hot-melt glass products, when the matrix and heterosilicate materials doped with transition metal ions are hot-melted in multiple layers at 530°C to 550°C, the chemical diffusion barrier constructed by the volume blocking effect can control the thickness of the element diffusion layer at the interface to below the visible light wavelength, ensuring clear outlines of the multi-color interface without fogging or stress cracking; In the application scenario of preparing precision cast optical devices, thanks to its excellent rheological stability and low surface tension characteristics in the supercooled liquid phase region, the matrix can perfectly fill complex topological structures such as microarray lenses or precision prisms. After precision annealing and locking at 490°C, the optical uniformity and refractive index packing density inside the device meet the requirements of high-precision photon transmission, solving the bottleneck problems of easy crystallization and dimensional instability of traditional low-melting-point glass in complex forming processes.

[0029] The preparation of this glass matrix requires adherence to specific process parameters. Raw materials include quartz sand with a purity of not less than 99.5% and a particle size controlled between 80 and 120 mesh, sodium carbonate, potassium carbonate, zinc oxide, titanium dioxide, barium carbonate, boric acid, and antimony oxide. The raw materials are weighed according to the aforementioned proportions and dry-mixed in a V-type mixer for 30 minutes. The mixture is then placed in a platinum crucible and melted at a temperature of 1340°C to 1360°C. During this process, mechanical stirring is activated, with the impeller speed set to 40 rpm, and stirring is continued for 2.5 hours. The gas flow generated by carbonate decomposition, combined with mechanical stirring, promotes the homogenization of cations in the melt and eliminates component segregation. In the clarification stage, the oxygen released by antimony oxide removes microbubbles. The structural freezing and annealing processes are also performed. The process is used to ensure the stable formation of micro-clusters. The clarified molten glass is poured into a stainless steel mold preheated to 350°C and then transferred to a precision annealing furnace. The annealing temperature is set at 490°C and the holding time is not less than 4 hours. This holding process allows the [Zn3Ti] clusters to complete the relaxation and locking of their topological structure in the supercooled liquid phase region, preventing structural defects or residual internal stress caused by rapid cooling. Afterward, it is slowly cooled to room temperature at a rate not exceeding 1°C / min. When the glass matrix prepared by this process is hot-melted and spliced ​​with a colorant containing copper or cobalt transition metal ions at 535°C, the thickness of the element diffusion layer at the interface is less than the wavelength of visible light, and no crystal nuclei larger than 50 nanometers are generated inside the glass matrix after holding at 550°C for 4 hours.

[0030] Example 1: In industrial applications involving the thermal bonding of multicolor precision optical devices, when the glass matrix of this invention needs to be chemically bonded to a heterochromatic glass doped with 3.5 wt% copper oxide at a low-temperature process window of 535°C, the system faces technical challenges such as excessive non-bridging oxygen introduced by high-concentration alkali metals and interfacial devitrification and stress cracking caused by ion inter-diffusion driven by chemical potential gradients on both sides of the interface. To address this issue, this technical solution locks the molar ratio of zinc oxide to titanium dioxide, n(ZnO) / n(TiO2), within a structural window of 2.8 to 3.2, inducing the melt network to self-assemble and form a [Zn3Ti] supertetrahedron. The clusters preferentially capture free non-bridging oxygen near the interface using a strong coordination field effect, converting active terminal oxygen into structurally stable bridging oxygen, thus cutting off the chemical driving force that induces the nucleation and crystallization of copper ions at the interface. At the same time, the scheme sets the molar fraction of potassium oxide in the total amount of alkali metal oxides, n(K2O) / [n(Na2O)+n(K2O)], to 0.41 to 0.46. The volume blocking effect constructed by alkali metal ions of different radii forms a tightly packed spatial steric hindrance in the ion transport channels of the silicon-oxygen framework. This steric hindrance effect limits the self-diffusion coefficient of alkali metal ions at 535℃, and hinders the non-equilibrium migration of sodium and potassium ions across the interface.

[0031] The synergistic operation of the above mechanisms enables the finally fabricated multicolor optical devices to maintain the matrix refractive index nD Under the premise of being greater than 1.515, an optically uniform transition zone with a thickness less than the wavelength of visible light is formed at the interface of heterogeneous glass. After undergoing an annealing and cooling process from 535°C to room temperature, no residual stress gradient that would cause cracking is generated on both sides of the interface.

[0032] Example 2: To verify the practical effectiveness of the technical solution of the present invention in the multicolor interfusion process, this experiment was established. The experiment aims to demonstrate the key role of the selected range of zinc oxide to titanium dioxide molar ratio and the range of mixed alkali ratio in suppressing interfacial reactions and improving structural stability by comparing the interfacial behavior and optical properties of glass matrices with different component ratios under the hot-melt condition of 535℃. The experimental platform used two high-temperature box-type resistance furnaces with a temperature control of ±1℃ to simulate the hot-melt splicing and annealing process in actual production. X-ray diffraction (XRD) was used to perform crystal phase analysis on the heat-treated glass samples, with a scanning range of 2θ from 10° to 80° and a scanning speed of 2° / min to detect microcrystal precipitation. A scanning electron microscope (SEM) equipped with an energy-dispersive X-ray spectrometer (EDS) was used to observe the microstructure of the splicing interface and perform elemental line scanning to characterize the elemental diffusion depth. The refractive index was measured using an Abbe refractometer at 25℃ with sodium yellow light (589.3nm) as the light source. All raw data were not smoothed to retain the true measurement noise.

[0033] To determine the optimal component parameters, a multi-dimensional controlled experiment was designed, including the sample group of this invention, a partially missing control group, and an out-of-range control group. In the basic glass formulation, w(SiO2) was fixed at 45.0%, w(BaO) at 10.0%, w(B2O3) at 3.0%, and w(Sb2O3) at 0.3%. The experimental groups and their key variables were set as follows: Sample group of this invention (S1): n(ZnO) / n(TiO2) was set to 3.0, i.e., w(ZnO) = 14.0%, w(TiO2) = 4.6%; n(K2O) / [n(Na2O) + n(K2O)] was set to 0.44, i.e., w(Na2O) = 10.5%, w(K2O) = 12.6%. These parameters are within the range defined by this invention. Within the core range; Out-of-range control group 1 (C1, low zinc-titanium ratio): n(ZnO) / n(TiO2) was set to 2.0, which is lower than the lower limit of this invention; Out-of-range control group 2 (C2, high zinc-titanium ratio): n(ZnO) / n(TiO2) was set to 4.0, which is higher than the upper limit of this invention; Partially missing control group (C3, single alkali metal): containing only Na2O and no K2O, i.e., no mixed alkali volume blocking channel was constructed; After melting and casting the glass batches of the above groups at 1350℃, they were stacked with colored glass slices doped with 3.5wt% copper oxide. The stacked samples were placed in a resistance furnace at 535℃ and held for 4 hours, and then annealed to room temperature at a rate of 0.5℃ / min. The interface analysis of the treated samples was performed, and the results are shown in Table 1 below.

[0034] Table 1: Comparison of interfacial properties of samples after hot-melt splicing at 1535℃

[0035] Group Original input parameter features Key intermediate features (microstructure) Final decision / output (interface status) S1 (This invention) <![CDATA[n(ZnO) / n(TiO2) = 3.0, Mixed alkali ratio = 0.44]]> The boundary was clear, with no visible crystallization. EDS line scan showed a Cu diffusion depth of <0.5 μm. Qualified: The interface is optically uniform, without cracks or fogging. C1 (low ratio) <![CDATA[n(ZnO) / n(TiO2)=2.0]]> <![CDATA[A large number of TiO2 microcrystals appear at the interface, and the anatase phase is detected by XRD]]> Unacceptable: Interface opacity is poor, appearing milky white. C2 (High Ratio) <![CDATA[n(ZnO) / n(TiO2)=4.0]]> The matrix underwent phase separation, resulting in zinc-rich droplet-like structures. Unacceptable: The glass is cloudy overall, and the refractive index has decreased. C3 (single alkali) <![CDATA[Contains only Na2O]]> The Na-Cu ion exchange depth at the interface is >15μm, accompanied by microcracks. Unacceptable: Interface cracking after cooling, stress mismatch.

[0036] Data analysis shows that when n(ZnO) / n(TiO2) is in the range of 2.8 to 3.2, as in group S1, the system can effectively suppress crystallization. Results from group C1 confirm that when this ratio is below the lower limit, due to the lack of sufficient [ZnO4] tetrahedral field confinement, excess Ti... 4+ It is easy to form octahedral coordination and induce crystallization; the results of group C2 show that when it is higher than the upper limit, it will lead to phase separation of the glass network. The failure of group C3 strongly proves that the mixed alkali effect can hinder ion migration and prevent stress cracking. The experimental data show obvious nonlinear characteristics, and only within a specific ratio window does it show excellent comprehensive performance, rather than changing monotonically with the component content.

[0037] Example 3: This example combines Figures 1 to 3 This document describes a multicolor interfused glass matrix with a low softening point and high refractive index, and its applications. Figure 1As shown, the preparation process begins at the raw material pretreatment station, where a precision weighing system and a V-type mixer dry-mix the raw materials for 30 minutes before conveying them to the high-temperature melting unit. The high-temperature melting unit uses a platinum crucible melting furnace, and at a temperature of 1340°C to 1360°C, a mechanical stirring device is used to eliminate component segregation. The high-temperature glass melt is then poured into the forming and structural freezing station, which is equipped with stainless steel molds preheated to 350°C. The formed glass is then quickly transferred to the heat treatment center. In the heat treatment center, the glass matrix is ​​held at 490°C for at least 4 hours in a precision annealing furnace to lock the zinc-titanium cluster structure. Finally, after cooling and quality inspection, the product is output as a multi-color interfused glass matrix or a precision optical device.

[0038] like Figure 2 As shown in the figure, the performance differences of the present invention sample group S1, the low zinc-titanium ratio control group C1, the high zinc-titanium ratio control group C2, and the single alkali metal control group C3 in two dimensions—Cu ion diffusion depth and interfacial stress—are compared. The left vertical axis represents the Cu ion diffusion depth in micrometers (μm), and the right vertical axis represents the interfacial stress in megapascals (MPa). The data show that the diffusion depth of group S1 is less than 1 μm and the interfacial stress is maintained at the lowest level, while group C3, which lacks the mixed alkali effect, exhibits an extremely high diffusion depth of over 15 μm and an interfacial stress of over 60 MPa. Group C1, with a low zinc-titanium ratio, exhibits a high interfacial stress, confirming the optimization effect of specific component design on interfacial performance.

[0039] like Figure 3 As shown, the microstructure diagram is divided into an upper mechanism region and a lower interface region: the upper left shows the silicon-oxygen network framework region, indicating the presence of non-bridging oxygen (NBO); the upper middle shows the zinc-titanium coupled tetrahedral cluster region, in which [TiO4] tetrahedra and [ZnO4] tetrahedra are connected through shared apex oxygen to form [Zn3Ti] supertetrahedral clusters, a process that consumes the non-bridging oxygen on the left; the upper right shows the mixed alkali-blocked channel region, utilizing K... + with Na + The large radius difference creates a volume blocking effect to impede ion migration. The lower part shows the multi-color interfusion interface region, depicting the state when the glass matrix of the present invention is combined with the transition metal colored glass. The thickness of the diffusion layer is less than the wavelength of visible light, and the legend clearly shows the symbolic representation of the cations Si, Ti, Zn, oxygen ions O, and tetrahedral structures.

[0040] Example 4: To address the original document's description of the consumption mechanism of non-bridging oxygen (NBO) by zinc-titanium coupled tetrahedral clusters and the inhibitory effect of mixed alkali volume blocking on ion migration, this targeted repair example is established to eliminate potential mechanistic black boxes. Through a combination of high-resolution structural characterization and microscopic dynamic simulation, a visualized structure-property relationship model is constructed to transparently elucidate the intrinsic causal chain between the evolution of the glass network structure and the improvement of macroscopic performance. To verify the actual existence of the [Zn3Ti] cluster and its consumption effect on NBO, a glass sample with components conforming to the limitations of this invention (n(ZnO) / n(TiO2)=3.0) was prepared, and Raman spectroscopy and X-ray photoelectron spectroscopy (XPS) analyses were performed. The Raman spectrum at 950 cm⁻¹... -1 Up to 1100cm -1 The characteristic peak shift and intensity enhancement appearing in the interval are attributed to the Q in the [SiO4] tetrahedron. 3 With Q 4 The increase in the proportion of structural units indicates a decrease in the number of NBOs, as shown in the XPS spectrum. 1s The peak fitting results of the binding energy show that the peak area ratio of the bridging oxygen (BO) signal increased from 65% without the introduction of the zinc-titanium coupling pair to 82%.

[0041] Secondly, regarding the microscopic mechanism by which the mixed base effect inhibits ion migration, molecular dynamics (MD) simulations were used to construct a Na-containing... + With K + A silicate glass network model of ions was used, with the simulation temperature set at 535℃. Mean square displacement (MSD) analysis was employed to calculate the self-diffusion coefficient of alkali metal ions under different alkali mixing ratios. The simulation results show that when n(K... 2O ) / [n(Na 2O n K 2O When the K0.41 is in the range of 0.41 to 0.46, the total diffusion coefficient of alkali metal ions reaches a minimum, only 1 / 10 of that of a single alkali metal system. Trajectory analysis reveals that the large-radius K0.46 + Ions tend to occupy key nodes in the network gaps, effectively blocking Na+. + The ion transition channels create a cage effect; finally, to clarify the principle of setting the annealing process parameters, stress relaxation experiments were conducted at different annealing temperatures. The results show that when the annealing temperature is set to 490℃ (slightly higher than T), stress relaxation is achieved. g The glass is then kept at a high temperature for 4 hours. This allows the residual stress inside the glass to be released most fully without causing structural deformation. The relaxation time of the glass network is matched with the process time scale, allowing micro-clusters to complete the adjustment and locking of their topology in the supercooled liquid phase region. Temperatures below this level or shorter holding times will result in residual stress and increase the risk of cracking, while temperatures above this level may induce microcrystal nucleation.

[0042] Example 5: Addressing the potential long-term stability and performance drift issues of low-softening-point glass under complex service environments, this example establishes a standardized accelerated aging and performance evolution monitoring procedure. This aims to provide definitive data support for predicting the service life of materials and their reliability under boundary conditions, eliminating the technical "black box" regarding long-term stability. To address the potential for alkali metal ion precipitation and surface weathering in humid environments, a high-temperature, high-humidity accelerated aging test is established. Standardized glass samples are placed in a constant temperature and humidity chamber, with the ambient temperature set at 85°C and relative humidity at 85% (double 85 test), for a duration of 1000 hours. Samples are removed every 200 hours, and their surface microstructure is scanned using an atomic force microscope (AFM). The root mean square roughness Rm is then used to determine the microstructure. q The changes in surface corrosion were quantified by inductively coupled plasma mass spectrometry (ICP-MS) to detect Na in the eluent. + With K + The cumulative concentration of ions is used to characterize the precipitation rate of alkali metal ions. At the end of the test, the transmittance attenuation of the sample in the visible light band is measured by a spectrophotometer, and this data is used as a quantitative criterion for judging whether the weather resistance of the material meets the standard.

[0043] Secondly, to address the fatigue cracks that may arise from thermal expansion mismatch in multi-color fused products under repeated thermal shock, a thermal shock cycle verification procedure was implemented. The encapsulated glass module was rapidly switched between a low-temperature environment of -40℃ and a high-temperature environment of 120℃, with a switching time of less than 10 seconds. The dwell time at each temperature point was 30 minutes, and a total of 500 cycles were performed. After the cycle, acoustic emission detection technology (AE) was used to perform a full-domain scan of the sample's interior. By capturing the transient elastic wave signals released when microcracks initiate or propagate, its structural integrity was evaluated.

[0044] Example 6: To ensure the reproducibility and stability of the technical solution of this invention under different raw material batches and environmental conditions, this example establishes standardized engineering calibration and process control procedures. For the formation rate of micro-clusters in the glass matrix, an online monitoring and feedback adjustment mechanism based on X-ray absorption fine structure (XAFS) is established. During the melting process, the XAFS spectrum of the melt is acquired in real time. By analyzing the bond lengths and coordination numbers of [Zn-O] and [Ti-O], the formation state of [Zn3Ti] clusters is dynamically monitored. If the coordination number of [Ti-O] is greater than 4.1, it indicates the presence of an octahedral precursor. The system will automatically increase the melting temperature at a rate of 2℃ / min until the coordination number returns to 4.0. The target range is ±0.1. If the coordination number is less than 3.9, the stirring rate is increased in increments of 5 rpm / min to promote component homogenization, thereby ensuring that the microstructure of the glass matrix in each batch is in the optimal state. Furthermore, addressing the challenge of controlling the interfacial ion diffusion depth during multicolor interfusion, this embodiment establishes a diffusion coefficient calibration method based on impedance spectroscopy analysis. At a standardized melting temperature of 535℃, an AC electric field of 0.1 Hz to 1 MHz is applied to glass samples with different alkali mixing ratios. Their complex impedance spectra are measured, and an equivalent circuit model is fitted. The conductivity parameter σ is extracted, and based on the Nernst-Einstein equation, the conductivity is converted into the self-diffusion coefficient of alkali metal ions, D: = σkT / (Nq). 2 ), where k is the Boltzmann constant, T is the absolute temperature, N is the carrier concentration, and q is the charge. This procedure establishes a quantitative relationship library between the mixed alkali ratio and the diffusion coefficient, and establishes a closed-loop feedback control procedure: setting a target threshold D for the diffusion coefficient. target =1.0×10 -12 m 2 / s, online acquisition of melt conductivity σ measure Substitute into the equation to calculate the real-time diffusion coefficient D. real Construct the deviation correction function ΔR=λ(D) real -D target ), where λ is the preset component sensitivity coefficient of 0.15 mol. -1 When D real >D target At that time, the DCS system automatically generates batching correction instructions based on ΔR, improving K. 2O molar ratio, reducing Na 2O Percentage, until |D is satisfied real -D target The convergence condition is ≤5%, which locks in the mixed alkali feed ratio for the current shift. In actual production, the optimal mixed alkali ratio can be quickly determined by measuring the conductivity of the raw materials and referring to a table, thus locking the diffusion coefficient at 10. -12 m 2 The thickness of the interface reaction layer is controlled on the order of / s to avoid crystallization or cracking caused by excessive diffusion.

[0045] Furthermore, considering the nonlinear characteristics of stress release during annealing, this embodiment employs an adaptive annealing curve generation algorithm. This algorithm uses the glass transition temperature T measured by differential scanning calorimetry (DSC) as the basis for the algorithm. g and the sudden change in specific heat capacity ΔC p As input, combined with a finite element analysis (FEA) model, the residual stress distribution under different cooling rates is simulated. The core logic of the algorithm lies in finding the optimal cooling path, enabling the adaptive annealing curve generation algorithm to achieve the desired cooling rate across different temperature ranges. g During the interval process, the following finite element iterative logic is executed: Input T measured by DSC g and ΔC p Data, setting the maximum principal stress threshold σ of the unit th =0.7σ b (σ) b (Measured flexural strength of glass), at T g Within a temperature range of ±50℃, a transient thermo-structural coupling simulation is run with a cooling rate v discretized in step size of 0.1℃ / min to calculate the transient peak stress σ at the current v. max If σ max >σ th Triggering the downgrade command v new =v old ×0.8; if σ max <0.5σ th Trigger the speed-up command v new =v old ×1.2, repeat the iteration until the stress utilization rate η=σ max / σ th Within the range of 0.85-0.95, the nonlinear temperature-time curve is output to the annealing furnace PLC controller. The maximum transient tensile stress inside the glass is always lower than the intrinsic tensile strength threshold of the material. Based on the simulation results, the system automatically generates a refined annealing curve containing multiple isothermal holding platforms and variable rate cooling sections.

[0046] Example 7: To further confirm the technical universality and performance evolution law of the present invention across the entire component range, sample groups S7-1, S7-2 and S7-3 were constructed by selecting concentration boundary points and central axis sampling points for cross-validation. Control groups D7-1 and D7-2, which are outside the component range, were set as performance mutation references. This example reflects the robust support of microstructure regulation rules for macroscopic physical indicators by calibrating the extreme boundaries of the lower limit, median and upper limit of the components. The specific component configurations (by weight percentage) of each sample group are shown in Table 2 below.

[0047] Table 2: Boundary Determination of Sample Groups and Component Composition of Control Groups

[0048] Component index S7-1 (Lower Limit Group) S7-2 (Intermediate Group) S7-3 (Upper Limit Group) D7-1 (Control Group 1) D7-2 (Control Group 2) Component range silicon dioxide 42.0% 45.0% 48.0% 45.0% 45.0% 42.0%-48.0% Antimony oxide 0.1% 0.3% 0.5% 0.3% 0.3% 0.1%-0.5% Sodium oxide 11.2% 10.0% 8.0% 10.0% 13.0% (Exceeding) 8.0%-12.0% potassium oxide 14.0% 12.0% 10.0% 12.0% 9.0% (Exceeding) 10.0%-14.0% Titanium dioxide 4.0% 4.0% 5.0% 5.0% 4.0% 3.0%-5.0% Zinc oxide 12.0% 12.5% 15.5% 9.0% (Exceeding) 14.5% 12.0%-16.0% Barium oxide 13.0% 13.0% 9.0% 15.0% 10.2% 8.0%-13.0% boron oxide 3.2% 3.2% 4.0% 3.7% 4.0% 2.0%-4.0% Moor ratio 2.94 3.07 3.05 1.77 (extremely low) 3.56 2.8-3.2 Mixed alkali molar ratio 0.45 0.44 0.45 0.44 0.31 (extremely low) 0.41-0.46

[0049] The above-mentioned sample groups were prepared according to the process described in this invention, and their network evolution process was precisely analyzed at the atomic scale. The results show that the sample groups exhibit definite structural inertness across the entire concentration range. In the lower boundary condition S7-1, even if the silica of the network-forming body is at the lower limit of 42.0% and the antimony oxide clarifying agent is only 0.1%, sufficient strong coordination field effect can still be induced by strictly implementing the range locking of the zinc-titanium molar ratio. The experimental results show that the density of the [Zn3Ti] supertetrahedral clusters formed at this time is sufficient to capture the free non-bridging oxygen generated by the alkali metal bond breaking, and control the softening point at about 524℃. In the upper boundary S7-3, when the titanium dioxide reaches the upper limit of 5.0%, the ion migration space is squeezed at the atomic scale by the mixed alkali volume blocking effect, which successfully suppresses the aggregation and nucleation of high-concentration titanium ions. This makes the thickness of the interface diffusion layer remain at an extremely low level of 485 nm during the long-term hot melting process at 535℃. The performance indicators and structural fingerprint evidence of each sample group are shown in Table 3 below.

[0050] Table 3: Comparison of Macroscopic Performance and Structural Fingerprint Evidence for Each Sample Group

[0051] Sample group number softening point Refractive index Interface status (535℃) Bridging oxygen ratio (XPS) Ti coordination number (XAFS) Raman characteristic peaks S7-1 524 1.529 Uniform and free of crystallization 82.1% 4.05 (Tetrahedron) 1085 (Strong) S7-2 531 1.522 Uniform and free of crystallization 81.5% 4.11 (Tetrahedron) 1082 (Strong) S7-3 535 1.517 Uniform and free of crystallization 80.8% 4.15 (Tetrahedron) 1079 (Strong) D7-1 542 1.498 Severe crystallization at the interface 62.5% 5.82 (octahedron) 920 (width) D7-2 522 1.512 Interfacial stress cracking 64.2% 4.25 1050(weak)

[0052] The structural fingerprint data in Table 3 shows that the proportion of bridging oxygen in the invention sample is significantly higher than 80%, and the characteristic energy position of titanium ions is highly consistent with the tetrahedral coordination model. This confirms that under the specific ratio constraints of this invention, titanium ions did indeed undergo a configuration reversal from octahedral to tetrahedral coordination, successfully constructing a topological unit that locks in structural oxygen. In contrast, when the molar ratio of zinc oxide to titanium dioxide is less than 2.8 (e.g., D7-1), due to insufficient coordination field constraints, titanium ions maintain an unstable octahedral configuration (coordination number of 5.82), failing to form clusters to consume non-bridging oxygen, directly leading to visible crystallization bands at the interface. When the proportion of mixed alkali exceeds the specified range (e.g., D7-2), the volume blocking effect fails, and the interfacial stress gradient caused by ion inter-diffusion increases dramatically, ultimately causing the product to crack after cooling.

[0053] It will be apparent to those skilled in the art that the present invention is not limited to the details of the exemplary embodiments described above, and that the present invention can be implemented in other specific forms without departing from the spirit or essential characteristics of the present invention.

[0054] Finally, it should be noted that the above embodiments are only used to illustrate the technical solutions of the present invention and are not intended to limit it. Although the present invention has been described in detail with reference to preferred embodiments, those skilled in the art should understand that modifications or equivalent substitutions can be made to the technical solutions of the present invention without departing from the spirit and scope of the technical solutions of the present invention.

Claims

1. A multicolor interfused glass matrix with a low softening point and high refractive index, characterized in that, The glass matrix is ​​composed of the following components, by weight percentage of oxides: The glass matrix comprises 42.0% to 48.0% silicon dioxide, 8.0% to 12.0% sodium oxide, 10.0% to 14.0% potassium oxide, 12.0% to 16.0% zinc oxide, 8.0% to 13.0% barium oxide, 3.0% to 5.0% titanium dioxide, 2.0% to 4.0% boron oxide, and 0.1% to 0.5% antimony oxide; the glass matrix is ​​lead-free, its softening temperature is not higher than 535℃, and its refractive index nD is not lower than 1.

515. The cation coordination network within the glass matrix follows the following microstructure construction rules that passivate the activity of non-bridging oxygen: First, construct zinc-titanium coupled tetrahedral clusters to lock structural oxygen: limit the molar ratio of zinc oxide to titanium dioxide to the range of 2.8 to 3.2, and utilize the coordination field effect generated by excess zinc ions to transform titanium ions from octahedral coordination to tetrahedral coordination in an alkaline environment, and form clusters with zinc-oxygen tetrahedra through shared vertex connection, thereby consuming the free non-bridged oxygen generated by alkali metal bond breaking; Second, construct a mixed alkali volume blocking channel to limit ion migration: limit the molar ratio of potassium oxide to alkali metal oxide in the range of 0.41 to 0.46, and utilize the difference in ionic radii between potassium ions and sodium ions to form a stacked state with maximum filling density in the interstices of the silicon-oxygen network. This ensures that the diffusion coefficient of alkali metal ions is in a low energy level determined by the volume blocking effect within the interfusion temperature range of 530℃ to 550℃ of the glass matrix, thereby inhibiting the penetration and crystallization of dissimilar coloring ions at the interfusion interface. Furthermore, to ensure that the glass matrix maintains sufficient network rigidity and refractive index packing density under low softening point conditions, the mass ratio of the total amount of divalent metal oxides in the glass matrix to the silica of the network forging satisfies the following network stability criterion formula: (w(ZnO)+w(BaO)) / (w(SiO2))≥0.5, where w(ZnO), w(BaO), and w(SiO2) represent the weight percentage values ​​of zinc oxide, barium oxide, and silica in the glass matrix, respectively; this formula limits the mass space occupation relationship between the network modifier and the network forging to ensure that the glass density is not less than 2.65 g / cm³. The ratio of the total molar amount of alkali metal ions to the total molar amount of aluminum ions in the glass matrix is ​​greater than 10, and the glass matrix is ​​essentially free of aluminum oxide to avoid aluminum ions competing for oxygen ions and thus interfering with the formation of zinc-titanium coupled tetrahedral clusters. Antimony oxide is used as a clarifying agent to release oxygen at high temperatures to remove microbubbles in the glass melt through a physical bubble-carrying mechanism. The glass matrix is ​​essentially an isotropic photon transmission continuous medium and a thermodynamically dimensionally stable body, capable of having a thermal expansion coefficient difference of 5 × 10⁻⁶. -7 The heterogeneous amorphous materials in the / ℃ range achieve chemical bonding without interfacial stress gradient; the glass matrix has a transmittance of not less than 90% in the visible light band and has a characteristic absorption edge in the ultraviolet light band, which is determined by the band structure of zinc oxide and titanium dioxide.

2. The multicolor intermetallic glass matrix with low softening point and high refractive index according to claim 1, characterized in that, During the preparation process, the glass matrix underwent structural freezing treatment, where it was held at 550℃ for 4 hours. No crystal nuclei larger than 50 nanometers were formed within the matrix. Furthermore, when the glass matrix and silicate material doped with transition metal chromophores were hot-melted and joined at 535℃, the elemental diffusion layer thickness at the interface was less than the visible light wavelength, and there was no microcrystalline precipitation or optical scattering haze at the interface. The linear thermal expansion coefficient of the glass matrix was 95 × 10⁻⁶ within the range of 20℃ to 300℃. -7 ℃ to 105×10 -7 / ℃, to ensure residual stress matching at the multi-component composite interface after cooling.

3. The multicolor intermetallic glass matrix with low softening point and high refractive index according to claim 1, characterized in that, Silica is used as a network former, and its raw material is quartz sand with a silica content of not less than 99.5% and an iron oxide content of not more than 0.01%. Sodium oxide and potassium oxide are introduced by sodium carbonate and potassium carbonate, respectively, and decompose and release carbon dioxide in the high-temperature melting stage of 1340℃ to 1360℃. Mechanical stirring promotes the uniform distribution of cations in the melt.

4. The low softening point, high refractive index multicolor interfused glass matrix according to claim 1, characterized in that, Zinc oxide, as a network intermediate, preferentially occupies tetrahedral sites in the glass matrix to form [ZnO4] structural units; barium oxide, as a network exogenous body, fills the voids formed by the connection between [ZnO4] and [SiO4] structural units. It contributes to the high refractive index of the glass matrix through the high polarizability of barium ions, and further blocks the migration channels of alkali metal ions by utilizing its large ionic radius.

5. The multicolor intermetallic glass matrix with low softening point and high refractive index according to claim 1, characterized in that, The preparation method of the glass matrix includes: melting and clarifying the batch material at 1350°C, casting the molten glass into a mold, and holding it at a precision annealing temperature of 490°C for at least 4 hours; the precision annealing temperature is set to be 10°C to 20°C higher than the glass transition temperature to allow zinc-titanium coupled tetrahedral clusters to complete the relaxation and locking of the topological structure in the supercooled liquid phase region, preventing structural defects caused by rapid cooling; and the glass matrix exhibits low surface tension and high wettability rheological characteristics that are adapted to flow in micron-scale confined spaces, and has a low viscosity temperature coefficient in the Newtonian fluid behavior temperature range of 530°C to 560°C. This viscosity temperature dependence allows the glass melt to fill the fine topological structure under the drive of surface tension without devitrification.

6. The low softening point, high refractive index multicolor intermetallic glass matrix according to claim 1, characterized in that, Boron oxide enters the glass network in the form of [BO3]trigonal or [BO4] tetrahedrons, with its content controlled between 2.0% and 4.0%. This is used to help reduce the melting temperature and suppress micro-phase separation caused by liquid phase immiscibility without compromising the stability of the zinc-titanium coupled tetrahedral clusters.

7. The application of the low softening point, high refractive index multicolor interfused glass matrix as described in claim 1 in the preparation of multicolor hot-melt glass products.

8. The application of the low softening point, high refractive index multicolor intermetallic glass matrix of claim 1 in the fabrication of precision cast optical devices.

Images