Test method for controlling forming production of lithium aluminum silicon glass

Abstract

According to the present invention, the relationship expression between the crystallization degree value Ai and the cross section size Si capable of being produced by the crystallization degree value Ai is established during the lithium aluminum silicon glass generation process through the overflow method, and the introduction of the relationship expression means that the key parameters during the production process can be optimized by precisely regulating the crystallization degree value of the glass; therefore, the quality defect caused by crystallization is avoided.

Description

Technical Field

[0001] This application relates to the technical field of glass, and particularly to a test method for controlling the forming production of lithium aluminosilicate glass. Background Art

[0002] Lithium aluminosilicate glass is widely used in the field of electronic displays due to its excellent mechanical properties and chemical stability. By introducing two kinds of alkali metal ions, sodium and lithium, this kind of glass can achieve sodium-lithium and potassium-sodium binary ion exchange, forming a composite compressive stress layer, endowing it with characteristics such as high hardness and high strength. However, when using the overflow method to produce this high-performance glass, there are indeed some technical challenges, especially the problems related to the viscosity-temperature properties and crystallization properties of the glass.

[0003] When using the overflow method to produce glass, two aspects of the glass itself need to be considered, namely the viscosity-temperature properties of the glass and the crystallization properties of the glass. In terms of viscosity-temperature properties, during the production process by the overflow method, the viscosity of the glass melt at the bottom of the overflow tank is crucial for the operation of the forming section. The viscosity of the glass melt not only determines the working temperature of the overflow tank, but also directly affects the temperature control ability and energy consumption efficiency of the production line. If the viscosity of the glass melt is too high or too low, it will affect the uniformity and quality of the glass ribbon. For example, too high viscosity may lead to poor flow of the glass melt, increasing the risk of glass ribbon breakage; while too low viscosity may cause excessive flow of the glass melt, resulting in difficult control of the forming size. In terms of crystallization properties, a key issue in the production by the overflow method is the influence of the residence time and temperature of the glass melt at the bottom of the overflow tank on crystallization. When the glass melt stays at the bottom of the overflow tank for a long time, especially when the temperature is close to or lower than the upper limit temperature of crystallization, crystallization is likely to occur. Crystallization will cause problems such as stones and devitrification inside the glass, seriously affecting the product quality. In addition, in the production of large-width or relatively thick glass, due to the slow flow rate of the glass melt, it is easier to form accumulations at the bottom of the overflow tank, further increasing the risk of crystallization. Summary of the Invention

[0004] In view of the above deficiencies in the prior art, the purpose of the present application is to provide a test method for controlling the forming production of lithium aluminosilicate glass, aiming to correspondingly characterize the crystallization state by testing the energy and mass changes generated during the exothermic process of the glass material through TG-DSC (Thermogravimetry-Differential Scanning Calorimetry). During the overflow method production process, the bottom of the overflow tank is often one of the areas with the lowest temperature in the forming component. Then, the product of the width and thickness of the glass ribbon determines the residence time of the glass liquid at the bottom of the overflow tank when the temperature of the glass liquid is lower than its crystallization temperature. The present application relates the energy change generated after the glass has a crystallization tendency when the temperature at the bottom of the overflow tank is lower than the crystallization temperature to the size of the glass substrate in actual production, and thus can regulate the crystallization degree of lithium aluminosilicate glass in actual mass production through this relationship, thereby solving the problem that the prior art lacks an intuitive and quantitative characterization of the relationship between the forming size of the glass in production and its crystallization degree and cannot effectively control the crystallization degree to ensure the product quality in glass production.

[0005] To solve the above technical problems, in the first aspect, the present application proposes a test method for controlling the forming production of lithium aluminosilicate glass, including the following steps:

[0006] Step 1: Use a synchronous thermal analyzer to obtain the heat flow Q-temperature T curve of the lithium aluminosilicate glass, and determine T pbmin 、T pbmax according to the crystallization peak region of the glass in the figure; where T pbmin is the lowest temperature at the start of crystallization in the crystallization peak region of the glass; T pbmax is the temperature at the end of heat release in the crystallization peak region of the glass;

[0007] Step 2: Calculate the crystallization degree value through the following formula;

[0008]

[0009] y = f(T);

[0010] In the formula, y = f(T) is the heat flow Q-temperature T curve of the lithium aluminosilicate glass obtained by the synchronous thermal analyzer, and A i is the integral value corresponding to the crystallization peak region, used to represent the crystallization degree value, with the unit of W·℃·g -1 ;

[0011] Step 3: Calculate the cross-sectional size of the lithium aluminosilicate glass that can be produced through the following formula:

[0012] S i = K÷A i ;

[0013] In the formula, S i is the cross-sectional size of the lithium aluminosilicate glass actually produced, with the unit of dm2 ; K = S max ×A max ; S i ≥ S max ; where S max is the maximum cross-sectional size that the production line can produce lithium aluminosilicate glass by itself; A max is the maximum devitrification degree value that the production line can accept when producing lithium aluminosilicate glass plates with the maximum cross-sectional size and the product yield is 80%; the unit of K is dm 2 ·W·℃·g -1 .

[0014] Furthermore, in the test method, the range of the test temperature is 30 - 1000 °C.

[0015] Furthermore, in the test method, the heating rate is 1 - 15 °C / min, preferably 10 °C / min.

[0016] Furthermore, the A max is obtained through the following steps:

[0017] S1: Use a certain production line to produce N glass formulas, and calculate the devitrification degree value A corresponding to each glass formula through the above step 2 i ; where N ≥ 1000;

[0018] S2: Statistically analyze the relationship between the production yield (i.e., the yield) and the devitrification degree value A i , and record the devitrification degree value A corresponding to the production yield of 80% i as the maximum devitrification degree value A max .

[0019] Furthermore, when producing lithium aluminosilicate glass by the overflow method, the maximum cross-sectional size S max is 0.59 dm 2 .

[0020] Furthermore, the devitrification degree value A i is 0.00 - 5.73 W·℃·g -1 , preferably 0.10 - 5.73 W·℃·g -1 .

[0021] In a second aspect, the present application provides a method for preparing lithium aluminosilicate glass, controlling the devitrification degree value A of the lithium aluminosilicate glass i to be 0.00 - 5.73, and A i is obtained through the following calculation formula:

[0022]

[0023] Wherein, y = f(T) is the heat flow Q - temperature T curve of the lithium aluminosilicate glass obtained by a synchronous thermal analyzer, and A i is the integral value corresponding to the crystallization peak region, with the unit of W·℃·g -1 ;

[0024] Meanwhile, the cross-sectional size of the lithium aluminosilicate glass during forming satisfies the following relational expression:

[0025] S i = K ÷ A i ;

[0026] Wherein, S i is the cross-sectional size of the actually produced lithium aluminosilicate glass, with the unit of dm 2 ;

[0027] K = S max × A max ; S i ≥ S max ; wherein, S max is the maximum cross-sectional size that the production line itself can produce lithium aluminosilicate glass; A max is the maximum crystallization degree value that the production line can accept when producing lithium aluminosilicate glass plates with the maximum cross-sectional size and the product yield is 80%; the unit of K is dm 2 ·W·℃·g -1 ;

[0028] The composition of the lithium aluminosilicate glass, in terms of mole percentage of oxides, includes the following components:

[0029] SiO2: 50.00 mol% - 75.00 mol%;

[0030] Al2O3: 5.00 mol% - 20.00 mol%;

[0031] Li2O: 0.01 mol% - 15.00 mol%;

[0032] Na2O: 2.00 mol% - 12.00 mol%.

[0033] Furthermore, the composition of the lithium aluminosilicate glass, in terms of mole percentage of oxides, further includes the following components:

[0034] P2O5: 0.00 mol% - 10.00 mol%;

[0035] K2O: 0.00 mol% - 2.00 mol%;

[0036] MgO: 0.00 mol% - 10.00 mol%;

[0037] CaO: 0.00 mol% to 5.00 mol%;

[0038] SrO: 0.00 mol% to 2.00 mol%;

[0039] ZnO: 0.00 mol% to 1.00 mol%;

[0040] ZrO2: 0.00 mol% to 3.00 mol%;

[0041] B2O3: 0.00 mol% to 5.00 mol%;

[0042] La2O3: 0.00 mol% to 3.00 mol%;

[0043] Y2O3: 0.00 mol% to 3.00 mol%.

[0044] Furthermore, the thickness of the glass is 0.1 - 2.0 mm.

[0045] Compared with the prior art, the present application has the following beneficial effects:

[0046] 1. The present application for the first time establishes a relationship formula between the crystallization degree value A and the cross-sectional size S that can be produced during the production of lithium aluminosilicate glass by the overflow method. The introduction of this relationship formula means that the present application can optimize the key parameters in the production process by precisely controlling the crystallization degree of the glass, thereby avoiding quality defects caused by crystallization. Because the present application discovers that the energy and mass changes generated during the exothermic process of the glass material are measured by TG-DSC (Thermogravimetry-Differential Scanning Calorimetry) to correspondingly characterize its crystallization state, ensuring that the residence time of the glass melt at the bottom of the overflow tank does not exceed the critical value, thus preventing the crystallization degree from being too severe to cause mass production to fail. i with the cross-sectional size S that it can produce i The connection relationship. The introduction of this relationship means that the present application can optimize the key parameters in the production process by precisely controlling the crystallization degree of the glass, thereby avoiding quality defects caused by crystallization. Because the present application discovers that the energy and mass changes generated during the exothermic process of the glass material are measured by TG-DSC (Thermogravimetry-Differential Scanning Calorimetry) to correspondingly characterize its crystallization state, ensuring that the residence time of the glass melt at the bottom of the overflow tank does not exceed the critical value, thus preventing the crystallization degree from being too severe to cause mass production to fail.

[0047] 2. By controlling the specific crystallization degree value A of the lithium aluminosilicate glass i and making it satisfy a specific relationship formula, it is possible to achieve large-scale stable mass production of lithium aluminosilicate glass by the overflow method under the condition that the production cross-sectional size does not exceed S i and the yield remains above 80%.

[0048] 3. The actual application of the test method for controlling the forming production of lithium aluminosilicate glass in the present application can significantly reduce the cost of producing lithium aluminosilicate glass by the overflow method and reduce the trial-and-error cost. BRIEF DESCRIPTION OF THE DRAWINGS

[0049] Figure 1 It is a polarized light microscope image of the crystallization situation of Example 3 in the forming stage.

[0050] Figure 2 Polarized light microscope image of the crystallization situation of Example 9 in the forming stage.

[0051] Figure 3 Polarized light microscope image of the crystallization situation of Comparative Example 2 in the forming stage.

[0052] Figure 4 Polarized light microscope image of the crystallization situation of Comparative Example 4 in the forming stage.

[0053] Figure 5 Standard curve graph of the production yield - crystallization degree value A in the present application i

[0054] Figure 6 Graph of DSC heat flow Q - temperature T for Examples and Comparative Examples used to calculate the crystallization degree value A i Detailed implementation manners

[0055] The present invention will clearly and completely describe the technical solutions in the embodiments of the present invention in conjunction with the accompanying drawings in the embodiments of the present invention. Obviously, the described embodiments are only a part of the embodiments of the present invention, rather than all the embodiments. All other embodiments obtained by those of ordinary skill in the art based on the present invention belong to the scope of protection of the present invention.

[0056] Unless otherwise specified in specific circumstances in the present invention, the numerical ranges listed herein include the upper and lower limit values, as well as all integers and fractions within that range, rather than the specific values listed when defining the range. As used herein, "and / or" is inclusive. For example, "A and / or B" means only A, or only B, or both A and B at the same time.

[0057] The corresponding test methods and explanations of related measurement methods involved in the present application are as follows:

[0058] 1. TG - DSC test:

[0059] The instrument used is Mettler - Toledo TGA / DSC 3 +, and the test is carried out in accordance with JY / T 0589.5 - 202. The standard substance used for the test is α - Al2O3 powder. The container for placing the sample is a platinum crucible. The ambient temperature of the instrument placement is 24°C, and the air humidity is 40%. After grinding the glass and passing it through a 200 - mesh sieve, the sample to be tested is obtained. Weigh about 20 mg of the sample and heat it from room temperature to 900°C at a heating rate of 10°C / min under the protection of nitrogen atmosphere to obtain the DSC curve of the sample.

[0060] 2. The test method for the glass production yield (yield) includes:

[0061] ​​(1) After preparing the powder materials corresponding to the recipe, put them into the kiln pool for melting;

[0062] (2) Let the melted glass liquid flow into the platinum channel for high-temperature clarification and stirring homogenization;

[0063] (3) Inject the glass liquid with appropriate viscosity and temperature into the overflow brick, and form it through the limit roller and the edge puller;

[0064] (4) Anneal the formed glass quickly;

[0065] (5) Conduct on-line quality inspection on the annealed glass ribbon. Consider the glass ribbon as a good product when the number of crystals with a particle size greater than 10 μm is less than or equal to 10 in every 1 m 2 of the glass ribbon, and calculate the glass production yield.

[0066] 3. Crystallization test method for glass:

[0067] (1) Break the glass into small pieces with a size of 2 mm - 5 mm, and then put them into a long platinum-yellow boat and spread them evenly;

[0068] (2) Set the temperature range of the gradient furnace of model GTF-1612SLW-G. Set the upper limit temperature point of the crystallization of the glass material recipe as the highest temperature point of the temperature range of the platinum-yellow boat in the gradient furnace. For example, if the upper limit of crystallization is 1130 °C, then set the highest test temperature as 1130 °C;

[0069] (3) After the gradient furnace reaches the preset temperature range, put the platinum-yellow boat containing the sample to be tested into the gradient furnace. After keeping it at a constant temperature for 10, 20, and 30 minutes, take out the platinum-yellow boat;

[0070] (4) Observe the glass sample using a polarized light microscope or an optical microscope.

[0071] In actual production, it is found in this application that lithium aluminosilicate glass, due to the introduction of two kinds of alkali metal ions, sodium and lithium, can simultaneously perform binary ion exchange of sodium-lithium and potassium-sodium to form a composite compressive stress layer, thus possessing excellent properties such as high hardness and high strength. However, the realization of these properties depends on strict production process control, especially the viscosity-temperature property and crystallization property of the glass during the overflow method production process. As an efficient and low-cost production process, the overflow method is widely used in the consumer electronics field. Its advantages lie in high uniformity on both sides of the glass, low production cost, good glass quality, and no need for reverse polishing. However, this process also has problems. The glass needs to maintain an appropriate viscosity in the forming section (mainly at the bottom of the overflow tank), which not only affects the temperature corresponding to the overflow tank when producing glass by overflow, but also poses strict requirements on the crystallization property of the glass. Specifically, the longer the residence time of the glass liquid at the bottom of the overflow tank, the easier it is to crystallize, resulting in the fracture of the glass ribbon or other defects. Based on this, this application discovers two key problems, the influence of the viscosity-temperature property and the control of the crystallization property. The viscosity-temperature property of the glass directly affects the temperature setting of the overflow tank, and further affects the energy consumption and the crystallization property of the glass. If the temperature is too high, the glass liquid may crystallize; if the temperature is too low, it may lead to poor fluidity of the glass and difficulty in forming. During the overflow method production process, the residence time of the glass liquid at the bottom of the overflow tank determines whether it will crystallize. Glass with a large plate width or a relatively large thickness is prone to accumulation and stacking at the bottom of the overflow tank due to its slow flow rate, increasing the risk of crystallization. Therefore, how to minimize the crystallization phenomenon on the premise of ensuring glass forming has become the basic concept of this application.

[0072] Based on the above ideas, this application proposes, based on the thermodynamic theory of crystallization in materials science, to correspondingly characterize the crystallization state of glass materials by testing the energy and mass changes generated during the exothermic process of the glass materials through TG-DSC (thermogravimetry-differential scanning calorimetry). According to the thermodynamic principle, amorphous substances usually have higher internal energy than the corresponding crystalline substances of the same composition. When amorphous substances transform into crystalline substances, they will release excess energy and there will be a mass change, which can be detected by a TG-DSC instrument; and the crystallization state of the glass under different conditions can be evaluated.

[0073] This application provides a test method for controlling the forming production of lithium aluminosilicate glass, and the specific steps are as follows:

[0074] Step 1: Use a synchronous thermal analyzer to obtain the heat flow Q-temperature T curve of the lithium aluminosilicate glass, and determine T pbmin 、T pbmax according to the crystallization peak region of the glass in the figure; where T pbmin is the lowest temperature at which crystallization starts in the crystallization peak region of the glass; T pbmax is the temperature at the end of heat release in the crystallization peak region of the glass;

[0075] Step 2: Calculate the crystallization degree value through the following formula;

[0076]

[0077] y = f(T);

[0078] In the formula, y = f(T) is the heat flow Q - temperature T curve of the lithium aluminosilicate glass obtained by the synchronous thermal analyzer, and A i is the integral value corresponding to the crystallization peak region, which is used to represent the crystallization degree value, with the unit of W·℃·g -1 ;

[0079] Step 3: Calculate the cross-sectional size of the lithium aluminosilicate glass that can be produced through the following formula:

[0080] S i = K ÷ A i ;

[0081] In the formula, S i is the cross-sectional size of the actually produced lithium aluminosilicate glass, with the unit of dm 2 ; K = S max × A max ; S i ≥ S max ; Among them, S max is the maximum cross-sectional size of the lithium aluminosilicate glass that the production line can produce by itself; A max is the maximum crystallization degree value that the production line can accept when producing the lithium aluminosilicate glass plate with the largest cross-sectional size and the product yield is 80%; the unit of K is dm 2 ·W·℃·g -1 .

[0082] In this application, for the first time in the overflow method production, the relationship formula S i = K ÷ A i between the crystallization degree value A i and the cross-sectional size S i that it can produce is established. The establishment of this relationship formula can intuitively and quantitatively characterize the relationship between the glass forming size and the crystallization degree, thus realizing the refined control of the crystallization situation of the glass in the production process. When it is necessary to produce glass of a specific size, the maximum crystallization degree value A i can be adjusted through the above relationship formula, and then the process parameters can be accurately and quickly adjusted to ensure the product quality.

[0083] In some embodiments of the present application, the test temperature in the test method ranges from 30 to 1000 °C. The test temperature can be 30 °C, 100 °C, 300 °C, 500 °C, 600 °C, 700 °C, 800 °C, 900 °C or 1000 °C, or within the numerical range formed by any two of the above specific values as endpoints. It should be understood that in the embodiments, any of the above ranges can be combined with any other range.

[0084] In some embodiments of the present application, the heating rate in the test method is 1 - 15 °C / min, preferably 10 °C / min. The heating rate in the test method can be 1 °C / min, 2 °C / min, 3 °C / min, 4 °C / min, 5 °C / min, 6 °C / min, 7 °C / min, 8 °C / min, 9 °C / min, 10 °C / min, 11 °C / min, 12 °C / min, 13 °C / min, 14 °C / min or 15 °C / min, or within the numerical range formed by any two of the above specific values as endpoints. It should be understood that in the embodiments, any of the above ranges can be combined with any other range.

[0085] In some embodiments of the present application, the A max is obtained through the following steps:

[0086] S1: Use a certain production line to produce N glass formulas, and calculate the crystallization degree value A corresponding to each glass formula through the above step 2 i ; where N ≥ 1000;

[0087] S2: Statistically analyze the relationship between the production yield (i.e., the good rate) and the crystallization degree value A i , and record the crystallization degree value A i corresponding to a production yield of 80% as the maximum crystallization degree value A max of this production line.

[0088] In the present application, when producing lithium aluminosilicate glass by the overflow method, in the forming section of the lithium aluminosilicate glass, since the temperature of the glass melt is lower than its crystallization upper limit temperature, and then a crystallization tendency occurs. When the lithium aluminosilicate glass crystallizes, this process is exothermic, and an almost symmetric exothermic peak will appear on the Q - T curve of the heat flow of DSC. The integral area of this exothermic peak can represent the total energy of the crystallization of the lithium aluminosilicate glass, that is, it can characterize the crystallization degree value of the lithium aluminosilicate glass crystallization. Through actual production of N (N is greater than or equal to 1000) glass formulas, use DSC to test the crystallization degree value A i of this series of glass formulas, and statistically analyze the relationship between the production yield (i.e., the good rate) and the crystallization degree value A i , and further find that the crystallization degree value A iIs inversely proportional to the production yield rate, that is, as the crystallization degree value A i increases, the production yield rate gradually decreases, and then a standard curve graph is obtained. Then, to achieve high efficiency and high economic benefits in the actual production of glass, it is necessary to control the production yield rate ≥ 80%. The crystallization degree value A i corresponding to a production yield rate (i.e., the good rate) of 80% is max denoted as the maximum crystallization degree value A i . Specifically, for example: when producing 1000 glass recipes, the standard curve graph of the production yield rate (i.e., the good rate) and the crystallization degree value A Figure 5 is as shown; further, the crystallization degree value A i corresponding to a production yield rate (i.e., the good rate) of 80% is denoted as the maximum crystallization degree A max of 5.7235 W·℃·g -1 . The crystallization degree value A i of the glass is only determined by the composition of the lithium aluminosilicate glass itself. Therefore, the maximum crystallization degree value A max that can be used to produce lithium aluminosilicate glass with a good rate of more than 80% by the overflow method process is a fixed value; in addition, the maximum cross-sectional size that the overflow method process can produce lithium aluminosilicate glass is also a fixed value, and at this time K = S max ×A max , indicating the crystallization degree value that the overflow method production line can accept for producing lithium aluminosilicate glass with a good rate of more than 80%. Therefore, K is a fixed value, that is, a constant, which characterizes the inherent characteristics of the overflow method production line.

[0089] Based on the above test method, the present application proposes a preparation method for lithium aluminosilicate glass, controlling the crystallization degree value A i of the lithium aluminosilicate glass to be 0.00 - 5.73, and A i is obtained by the following calculation formula:

[0090]

[0091] In the formula, y = f(T) is the Q-T curve of the lithium aluminosilicate glass obtained by a synchronous thermal analyzer, and A i is the integral value corresponding to the crystallization peak region, with the unit of W·℃·g -1 ;

[0092] At the same time, the cross-sectional size of the lithium aluminosilicate glass during forming satisfies the following relationship:

[0093] S i = K ÷ A i ;

[0094] In the formula, S i is the cross-sectional size of the actually produced lithium aluminosilicate glass, with the unit of dm 2 ;

[0095] K = S max ×A max ; S i ≥S max ; where S max is the maximum cross-sectional size of the production line itself that can produce lithium aluminosilicate glass; A max is the maximum devitrification degree value that the production line can accept when producing lithium aluminosilicate glass plates with the maximum cross-sectional size and a product yield of 80%; the unit of K is dm 2 ·W·°C·g -1 .

[0096] In some embodiments of the present application, the devitrification degree value A i is 0.00 - 5.73 W·°C·g -1 , preferably 0.10 - 5.73 W·°C·g -1 .

[0097] In some embodiments of the present application, S max is 0.59 dm 2 .

[0098] In some embodiments of the present application, the composition of the lithium aluminosilicate glass, in terms of mole percentage of oxides, includes the following components:

[0099] SiO2: 50.00 mol% - 75.00 mol%;

[0100] Al2O3: 5.00 mol% - 20.00 mol%;

[0101] Li2O: 0.01 mol% - 15.00 mol%;

[0102] Na2O: 2.00 mol% - 12.00 mol%.

[0103] In the present application, SiO2 is the main component constituting the lithium aluminosilicate glass, and its structure is a silicon-oxygen tetrahedron [SiO4]. It can endow the glass with a series of excellent properties, such as mechanical strength, chemical stability, and thermal stability. In some embodiments of the present application, in terms of the mole percentage of oxides, the content of SiO2 is 50.00 mol% or more, controlled within 50.00 mol% - 75.00 mol%. The content of SiO2 can be 50.00 mol%, 51.00 mol%, 53.00 mol%, 55.00 mol%, 57.00 mol%, 59.00 mol%, 59.20 mol%, 60.00 mol%, 61.00 mol%, 62.00 mol%, 63.34 mol%, 63.93 mol%, 64.21 mol%, 64.77 mol%, 64.99 mol%, 65.00 mol%, 65.54 mol%, 65.66 mol%, 66.00 mol%, 67.00 mol%, 68.00 mol%, 69.00 mol%, 70.00 mol%, 71.00 mol%, 72.00 mol%, 73.00 mol%, 74.00 mol%, or 75.00 mol%, or within the numerical range formed by any two of the above specific values as endpoints. It should be understood that in the embodiments, any of the above ranges can be combined with any other range.

[0104] Al2O3 is a component for improving the ion exchangeability during chemical strengthening, increasing the surface compressive stress after strengthening, and enhancing the mechanical properties of the glass. In some embodiments of the present application, in terms of the mole percentage of oxides, the content of Al2O3 is 5.00 mol% - 20.00 mol%. In some embodiments of the present application, in terms of the mole percentage of oxides, the content of Al2O3 can be 5.00 mol%, 6.00 mol%, 7.00 mol%, 8.00 mol%, 8.89 mol%, 9.50 mol%, 10.00 mol%, 10.80 mol%, 11.00 mol%, 11.10 mol%, 11.33 mol%, 11.72 mol%, 12.00 mol%, 13.00 mol%, 14.85 mol%, 15.03 mol%, 16.00 mol%, 17.46 mol%, 18.00 mol%, 18.50 mol%, 19.00 mol%, or 20.00 mol%, or within the numerical range formed by any two of the above specific values as endpoints. It should be understood that in the embodiments, any of the above ranges can be combined with any other range.

[0105] Na2O exists in the glass in the form of an extra-network former. It is a component for ion exchange and reducing the tendency of glass crystallization. In the glass structure, it mainly plays the role of breaking the network, can significantly reduce the viscosity of the glass melt, lower the melting temperature of the glass, and increase the fluidity of the glass melt. It is a good flux. In some embodiments of the present application, calculated in terms of the mole percentage of oxides, the content of Na2O is 2.00 mol% to 12.00 mol%. In some embodiments of the present application, calculated in terms of the mole percentage of oxides, the content of Na2O can be 2.00 mol%, 3.50 mol%, 4.00 mol%, 5.00 mol%, 5.14 mol%, 5.19 mol%, 6.03 mol%, 6.45 mol%, 7.00 mol%, 7.50 mol%, 8.00 mol%, 8.68 mol%, 9.00 mol%, 9.20 mol%, 10.00 mol%, 11.00 mol% or 12.00 mol%, or within the numerical range formed by any two of the above specific values as endpoints. It should be understood that in the embodiments, any of the above ranges can be combined with any other range.

[0106] Li2O exists in the glass in the form of an extra-network former. It is the main component for ion exchange, which is beneficial to increasing the exchange amount of sodium-lithium ions and improving the deep compressive stress. In some embodiments of the present application, calculated in terms of the mole percentage of oxides, the content of Li2O is 0.01 mol% to 15.00 mol%. In some embodiments of the present application, calculated in terms of the mole percentage of oxides, the content of Li2O can be 0.01 mol%, 0.50 mol%, 1.00 mol%, 2.00 mol%, 3.00 mol%, 4.00 mol%, 5.00 mol%, 6.93 mol%, 7.00 mol%, 7.38 mol%, 7.43 mol%, 7.91 mol%, 8.00 mol%, 9.00 mol%, 9.07 mol%, 10.00 mol%, 10.23 mol%, 11.03 mol%, 12.00 mol%, 13.00 mol%, 14.00 mol% or 15.00 mol%, or within the numerical range formed by any two of the above specific values as endpoints. It should be understood that in the embodiments, any of the above ranges can be combined with any other range.

[0107] In some embodiments of the present application, the composition of the lithium aluminosilicate glass, calculated in terms of the mole percentage of oxides, further includes the following components:

[0108] P2O5: 0.00 mol% to 10.00 mol%;

[0109] K2O: 0.00 mol% to 2.00 mol%;

[0110] MgO: 0.00 mol% to 10.00 mol%;

[0111] CaO: 0.00 mol% to 5.00 mol%;

[0112] SrO: 0.00 mol% to 2.00 mol%;

[0113] ZnO: 0.00 mol% to 1.00 mol%;

[0114] ZrO₂: 0.00 mol% to 3.00 mol%;

[0115] B₂O₃: 0.00 mol% to 5.00 mol%;

[0116] La₂O₃: 0.00 mol% to 3.00 mol%;

[0117] Y₂O₃: 0.00 mol% to 3.00 mol%.

[0118] In the present application, P₂O₅, as a network former, is a component that improves the ion exchange performance and crush resistance. In some embodiments of the present application, based on the mole percentage of the oxide, the content of P₂O₅ is 0.00 mol% to 10.00 mol%. In some embodiments of the present application, based on the mole percentage of the oxide, the content of P₂O₅ can be 0 mol%, 0.43 mol%, 0.50 mol%, 0.60 mol%, 0.70 mol%, 0.80 mol%, 0.90 mol%, 0.93 mol%, 1.00 mol%, 1.10 mol%, 1.20 mol%, 1.30 mol%, 1.40 mol%, 1.50 mol%, 1.60 mol%, 1.70 mol%, 1.80 mol%, 1.90 mol%, 2.00 mol%, 2.50 mol%, 3.00 mol%, 3.50 mol%, 4.00 mol%, 4.50 mol%, 5.00 mol%, 5.50 mol%, 6.00 mol%, 6.50 mol%, 7.00 mol%, 7.50 mol%, 8.00 mol%, 8.50 mol%, 9.00 mol%, 9.50 mol% or 10.00 mol%, or within the numerical range formed by any two of the above specific values as endpoints. It should be understood that in the embodiments, any of the above ranges can be combined with any other range.

[0119] Similar to Na2O, K2O is also a network modifier oxide that can significantly reduce the viscosity of the glass melt, although its effect is slightly weaker. It is also a flux for glass manufacturing. Replacing Na2O with K2O has a "double-alkali effect", which can improve the chemical stability of the glass, reduce glass crystallization, and improve the crystallization tendency of the glass. In some embodiments of the present application, based on the mole percentage of oxides, the content of K2O is 0.00 mol% to 2.00 mol%. In some embodiments of the present application, based on the mole percentage of oxides, the content of K2O can be 0 mol%, 0.05 mol%, 0.19 mol%, 0.37 mol%, 0.42 mol%, 0.51 mol%, 0.60 mol%, 0.70 mol%, 0.75 mol%, 0.80 mol%, 0.83 mol%, 0.85 mol%, 0.90 mol%, 0.93 mol%, 0.97 mol%, 1.02 mol%, 1.10 mol%, 1.20 mol%, 1.30 mol%, 1.40 mol%, 1.50 mol%, 1.58 mol%, 1.60 mol%, 1.70 mol%, 1.80 mol%, 1.90 mol%, 1.95 mol% or 2.00 mol%, or within the numerical range formed by any two of the above specific values as endpoints. It should be understood that in the embodiments, any of the above ranges can be combined with any other range.

[0120] MgO can improve the chemical stability and mechanical strength of glass, reduce the crystallization tendency of glass, and enhance the thermal stability of glass. In some embodiments of the present application, based on the mole percentage of oxides, the content of MgO is 0.00 mol% to 10.00 mol%. In some embodiments of the present application, based on the mole percentage of oxides, the content of MgO can be 0 mol%, 0.54 mol%, 0.60 mol%, 0.70 mol%, 0.80 mol%, 0.90 mol%, 1.00 mol%, 1.08 mol%, 1.20 mol%, 1.40 mol%, 1.60 mol%, 1.80 mol%, 1.90 mol%, 2.01 mol%, 2.10 mol%, 2.30 mol%, 2.48 mol%, 2.56 mol%, 2.60 mol%, 2.70 mol%, 2.80 mol%, 2.90 mol%, 3.00 mol%, 3.20 mol%, 3.40 mol%, 3.50 mol%, 3.68 mol%, 3.70 mol%, 3.80 mol%, 3.90 mol%, 4.00 mol%, 4.10 mol%, 4.20 mol%, 4.40 mol%, 4.50 mol%, 4.60 mol%, 4.70 mol%, 4.80 mol%, 4.91 mol%, 5.00 mol%, 5.20 mol%, 5.30 mol%, 5.42 mol%, 5.50 mol%, 6.00 mol%, 6.20 mol%, 6.30 mol%, 6.40 mol%, 6.50 mol%, 6.60 mol%, 6.70 mol%, 6.80 mol%, 6.90 mol%, 7.00 mol%, 7.20 mol%, 7.40 mol%, 7.60 mol%, 7.80 mol%, 8.00 mol%, 8.20 mol%, 8.30 mol%, 8.50 mol%, 8.70 mol%, 8.90 mol%, 9.00 mol%, 9.10 mol%, 9.30 mol%, 9.40 mol%, 9.50 mol%, 9.60 mol%, 9.70 mol%, 9.80 mol%, 9.90 mol% or 10.00 mol%, or within the numerical range formed by any two of the above specific values as endpoints. It should be understood that in the embodiments, any of the above ranges can be combined with any other range.

[0121] CaO can accelerate the melting and clarification process of glass and improve the chemical stability of glass within a certain range. In some embodiments of the present application, the content of CaO is 0.00 mol% to 5.00 mol% in terms of mol percentage of oxides. In some embodiments of the present application, in terms of mol percentage of oxides, the content of CaO can be 0.00 mol%, 0.24 mol%, 0.33 mol%, 0.50 mol%, 1.00 mol%, 1.11 mol%, 1.30 mol%, 1.40 mol%, 1.50 mol%, 1.60 mol%, 1.70 mol%, 1.80 mol%, 1.90 mol%, 2.00 mol%, 2.10 mol%, 2.20 mol%, 2.30 mol%, 2.40 mol%, 2.50 mol%, 2.60 mol%, 2.70 mol%, 2.80 mol%, 2.90 mol%, 3.00 mol%, 3.10 mol%, 3.20 mol%, 3.30 mol%, 3.40 mol%, 3.50 mol%, 3.60 mol%, 3.70 mol%, 3.80 mol%, 3.90 mol%, 4.00 mol%, 4.10 mol%, 4.20 mol%, 4.30 mol%, 4.40 mol%, 4.50 mol%, 4.60 mol%, 4.70 mol%, 4.80 mol%, 4.90 mol% or 5.00 mol%, or within the numerical range formed by any two of the above specific values as endpoints. It should be understood that in the embodiments, any of the above ranges can be combined with any other range.

[0122] In some embodiments of the present application, the content of SrO is 0.00 mol% to 2.00 mol% in terms of mol percentage of oxides. In some embodiments of the present application, in terms of mol percentage of oxides, the content of SrO can be 0.00 mol%, 0.10 mol%, 0.24 mol%, 0.30 mol%, 0.33 mol%, 0.40 mol%, 0.45 mol%, 0.50 mol%, 0.60 mol%, 0.70 mol%, 0.80 mol%, 0.90 mol%, 0.95 mol%, 1.00 mol%, 1.11 mol%, 1.20 mol%, 1.30 mol%, 1.40 mol%, 1.50 mol%, 1.60 mol%, 1.70 mol%, 1.80 mol%, 1.90 mol% or 2.00 mol%, or within the numerical range formed by any two of the above specific values as endpoints. It should be understood that in the embodiments, any of the above ranges can be combined with any other range.

[0123] In some embodiments of the present application, the content of ZnO is 0.00 mol% to 1.00 mol% in terms of mol percentage of the oxide. In some embodiments of the present application, the content of ZnO can be 0.00 mol%, 0.17 mol%, 0.24 mol%, 0.33 mol%, 0.40 mol%, 0.50 mol%, 0.60 mol%, 0.70 mol%, 0.80 mol%, 0.90 mol%, 0.95 mol% or 1.00 mol%, or within the numerical range formed by any two of the above specific values as endpoints. It should be understood that in the embodiments, any of the above ranges can be combined with any other range.

[0124] In some embodiments of the present application, the content of ZrO2 is 0.00 mol% to 3.00 mol% in terms of mol percentage of the oxide. In some embodiments of the present application, the content of ZrO2 can be 0.00 mol%, 0.10 mol%, 0.20 mol%, 0.30 mol%, 0.40 mol%, 0.50 mol%, 0.60 mol%, 0.70 mol%, 0.80 mol%, 0.90 mol%, 1.00 mol%, 1.10 mol%, 1.20 mol%, 1.30 mol%, 1.32 mol%, 1.40 mol%, 1.48 mol%, 1.50 mol%, 1.54 mol%, 1.60 mol%, 1.70 mol%, 1.80 mol%, 1.90 mol%, 2.00 mol%, 2.10 mol%, 2.20 mol%, 2.30 mol%, 2.40 mol%, 2.50 mol%, 2.60 mol%, 2.70 mol%, 2.80 mol%, 2.90 mol% or 3.00 mol%, or within the numerical range formed by any two of the above specific values as endpoints. It should be understood that in the embodiments, any of the above ranges can be combined with any other range.

[0125] In some embodiments of the present application, the content of B2O3 is 0.00 mol% to 5.00 mol% in terms of mol percentage of the oxide. In some embodiments of the present application, the content of B2O3 can be 0.00 mol%, 0.17 mol%, 0.20 mol%, 0.30 mol%, 0.40 mol%, 0.50 mol%, 0.60 mol%, 0.70 mol%, 0.80 mol%, 0.90 mol%, 1.00 mol%, 1.10 mol%, 1.20 mol%, 1.30 mol%, 1.40 mol%, 1.50 mol%, 1.60 mol%, 1.70 mol%, 1.80 mol%, 1.90 mol%, 2.00 mol%, 2.10 mol%, 2.20 mol%, 2.30 mol%, 2.40 mol%, 2.50 mol%, 2.60 mol%, 2.70 mol%, 2.80 mol%, 2.97 mol%, 3.00 mol%, 3.10 mol%, 3.21 mol%, 3.30 mol%, 3.40 mol%, 3.50 mol%, 3.60 mol%, 3.70 mol%, 3.80 mol%, 3.90 mol%, 3.95 mol%, 4.00 mol%, 4.10 mol%, 4.20 mol%, 4.30 mol%, 4.40 mol%, 4.50 mol%, 4.60 mol%, 4.70 mol%, 4.80 mol%, 4.90 mol% or 5.00 mol%, or within the numerical range formed by any two of the above specific values as endpoints. It should be understood that in the embodiments, any of the above ranges can be combined with any other range.

[0126] In some embodiments of the present application, the content of La2O3 is 0.00 mol% to 3.00 mol% in terms of mol percentage of the oxide. In some embodiments of the present application, the content of La2O3 can be 0.00 mol%, 0.10 mol%, 0.20 mol%, 0.30 mol%, 0.40 mol%, 0.50 mol%, 0.60 mol%, 0.70 mol%, 0.80 mol%, 0.90 mol%, 1.00 mol%, 1.10 mol%, 1.20 mol%, 1.25 mol%, 1.30 mol%, 1.40 mol%, 1.50 mol%, 1.54 mol%, 1.60 mol%, 1.70 mol%, 1.80 mol%, 1.90 mol%, 2.00 mol%, 2.10 mol%, 2.20 mol%, 2.30 mol%, 2.40 mol%, 2.50 mol%, 2.60 mol%, 2.70 mol%, 2.80 mol%, 2.90 mol% or 3.00 mol%, or within the numerical range formed by any two of the above specific values as endpoints. It should be understood that in the embodiments, any of the above ranges can be combined with any other range.

[0127] In some embodiments of the present application, the content of Y2O3 is 0.00 mol% to 3.00 mol% in terms of mol percentage of the oxide. In some embodiments of the present application, the content of Y2O3 can be 0.00 mol%, 0.10 mol%, 0.20 mol%, 0.30 mol%, 0.40 mol%, 0.50 mol%, 0.54 mol%, 0.60 mol%, 0.70 mol%, 0.80 mol%, 0.90 mol%, 1.00 mol%, 1.10 mol%, 1.20 mol%, 1.25 mol%, 1.30 mol%, 1.40 mol%, 1.50 mol%, 1.54 mol%, 1.60 mol%, 1.70 mol%, 1.80 mol%, 1.90 mol%, 2.00 mol%, 2.10 mol%, 2.20 mol%, 2.30 mol%, 2.40 mol%, 2.50 mol%, 2.60 mol%, 2.70 mol%, 2.80 mol%, 2.90 mol% or 3.00 mol%, or within the numerical range formed by any two of the above specific values as endpoints. It should be understood that in the embodiments, any of the above ranges can be combined with any other range.

[0128] In some embodiments of the present application, the thickness of the lithium aluminosilicate glass is 0.1 mm to 2.0 mm. In some embodiments of the present application, the thickness of the lithium aluminosilicate glass can be 0.1 mm, 0.2 mm, 0.3 mm, 0.4 mm, 0.5 mm, 0.6 mm, 0.7 mm, 0.8 mm, 0.9 mm, 1.0 mm, 1.1 mm, 1.2 mm, 1.3 mm, 1.4 mm, 1.5 mm, 1.6 mm, 1.7 mm, 1.8 mm, 1.9 mm or 2.0 mm, or within the numerical range formed by any two of the above specific values as endpoints. It should be understood that in the embodiments, any of the above ranges can be combined with any other range.

[0129] The technical solutions of the present invention will be further described in detail below with reference to specific embodiments. It should be understood that the following specific embodiments are only used to explain the present invention and are not used to limit the present invention.

[0130] Examples 1 - 10

[0131] According to the glass compositions described in Table 1 - Table 2, each raw material component of the glass is heated and melted in a glass melting furnace and mixed. Then, the molten glass is homogenized by bubbling, stirring, adding fining agents, etc., and formed into a glass plate with a cross-sectional size of 0.59 dm in a tin bath by the overflow method. 2 of the glass plate.

[0132] Comparative Examples 1 - 4

[0133] Comparative Examples 1 to 4 were operated under the same conditions as Example 1, except that the glass plates with a cross-sectional size of 0.59 dm were prepared according to the glass compositions shown in Table 2. 2 of the glass plate.

[0134] Table 1

[0135]

[0136]

[0137] Table 2

[0138]

[0139] Table 3

[0140]

[0141]

[0142] Examples 3, 7, Comparative Example 2 and Comparative Example 4 were actually produced by the overflow method, and the situation is shown in Table 4.

[0143] Table 4

[0144]

[0145]

[0146] It can be seen from Tables 1 to 4 that:

[0147] (1) The A value of the examples is generally low, indicating that the crystallization during the forming process is minimal, the product quality is high. Especially for Examples 1 and 2, it shows excellent crystallization control ability; while the A value of the comparative examples is generally high, indicating that their crystallization tendency is relatively large and quality problems are likely to occur during the production process. i The A value of the examples is generally low, indicating that the crystallization during the forming process is minimal, the product quality is high. Especially for Examples 1 and 2, it shows excellent crystallization control ability; while the A value of the comparative examples is generally high, indicating that their crystallization tendency is relatively large and quality problems are likely to occur during the production process. i The A value of the examples is generally low, indicating that the crystallization during the forming process is minimal, the product quality is high. Especially for Examples 1 and 2, it shows excellent crystallization control ability; while the A value of the comparative examples is generally high, indicating that their crystallization tendency is relatively large and quality problems are likely to occur during the production process.

[0148] (2) The polarized light microscope images of the crystallization conditions of Examples 3 and 9 as Figures 1 - 2 also show that very little crystallization occurs during the forming process below the crystallization temperature, while Comparative Examples 2 and 4 as Figures 3 - 4 show that a lot of crystallization occurs during the forming process below the crystallization temperature, with a greater crystallization tendency, proving that under the condition of a low A value of the examples, it has good mass production ability. i The A value of the examples is generally low, indicating that the crystallization during the forming process is minimal, the product quality is high. Especially for Examples 1 and 2, it shows excellent crystallization control ability; while the A value of the comparative examples is generally high, indicating that their crystallization tendency is relatively large and quality problems are likely to occur during the production process.

[0149] (3) The S value of the examples is relatively large, indicating that the examples can produce larger-sized glass substrates while ensuring quality; while the S value of the comparative examples is relatively small, especially for Comparative Example 4, indicating that its ability to produce large-sized glass is limited, and the crystallization risk is significantly higher than that of the examples, restricting its ability to produce large-sized glass. i The S value of the examples is relatively large, indicating that the examples can produce larger-sized glass substrates while ensuring quality; while the S value of the comparative examples is relatively small, especially for Comparative Example 4, indicating that its ability to produce large-sized glass is limited, and the crystallization risk is significantly higher than that of the examples, restricting its ability to produce large-sized glass. i The S value of the examples is relatively large, indicating that the examples can produce larger-sized glass substrates while ensuring quality; while the S value of the comparative examples is relatively small, especially for Comparative Example 4, indicating that its ability to produce large-sized glass is limited, and the crystallization risk is significantly higher than that of the examples, restricting its ability to produce large-sized glass.

[0150] (4) The production yield of the examples is generally high, indicating that the production process corresponding to the components of the examples is very stable and can mass-produce high-quality products; while the production yield of the comparative examples is generally low, indicating that the quality of the components corresponding to the comparative examples is unstable during the actual production process, the glass crystallization risk is significantly higher than that of the examples, and quality problems are more likely to occur.

[0151] Finally, it should be noted that the above examples are only used to illustrate the technical solutions of the present invention rather than to limit the technical solutions. Those of ordinary skill in the art should understand that any modifications or equivalent replacements made to the technical solutions of the present invention without departing from the purpose and scope of the technical solutions should be covered within the scope of the claims of the present invention.

Claims

1. A test method for controlling the molding production of lithium aluminosilicate glass, characterized in that: The steps include: Step 1: Use a synchronous thermal analyzer to obtain the heat flow Q-temperature T curve of lithium aluminum silicate glass, and determine T according to the crystallization peak area of ​​the glass in the figure. pbmin , T pbmax ; Among them, T pbmin It is the lowest temperature at which the glass starts to crystallize in the crystallization peak region; T pbmax It is the temperature at the end of heat release in the crystallization peak region of the glass; Step 2: Calculate the degree of crystallization by the following formula; y = f(T); Where, y = f(T) is the heat flow Q-temperature T curve of lithium aluminum silicate glass obtained by synchronous thermal analyzer, A i It is the integral value corresponding to the crystallization peak area, which is used to indicate the degree of crystallization. The unit is W·℃·g -1 ; Step 3: Calculate the cross-sectional dimensions of the lithium aluminosilicate glass that can be produced by the following formula: S i =K÷A i ; In the formula, S i The cross-sectional dimensions of the lithium aluminosilicate glass actually produced, in dm 2 .

2. The testing method according to claim 1, characterized in that: K also satisfies the following relationship: K=S max ×A max ; and S i ≥S max ; Among them, S max The maximum cross-sectional size of lithium aluminosilicate glass that can be produced by the production line itself; A max It is the maximum acceptable crystallization degree when the production line can produce lithium aluminum silicon glass plates with the largest cross-sectional size and the product yield is 80%; the unit of K is dm 2 ·W·℃·g -1 .

3. The testing method according to any one of claims 1 to 2, characterized in that: The test temperature in the test method ranges from 30 to 1000°C.

4. The testing method according to any one of claims 1 to 3, characterized in that: The heating rate in the test method is 1 to 15°C / min.

5. The testing method according to any one of claims 1 to 4, characterized in that: The A max Obtained through the following steps: S1: Use a certain production line to produce N glass formulas, and calculate the crystallization degree value A corresponding to each glass formula through the above step 2. i ; Where N ≥ 1000; S2: Statistical production rate and crystallization degree value A i The relationship between the production rate and the crystallization degree A corresponding to 80% i Recorded as the maximum crystallization degree value A max .

6. The testing method according to any one of claims 1 to 5, characterized in that: When producing lithium aluminosilicate glass by overflow method, the maximum cross-sectional dimension S max 0.59dm 2 .

7. The testing method according to any one of claims 1 to 6, characterized in that: Crystallization degree value A i 0.00-5.73W·℃·g -1 , preferably 0.10-5.73W·℃·g -1 .

8. A method for preparing lithium aluminosilicate glass, characterized in that: Controlling the crystallization degree of lithium aluminum silicate glass A i 0.00-5.73, A i It is calculated by the following formula: Where, y = f(T) is the heat flow Q-temperature T curve of lithium aluminum silicate glass obtained by synchronous thermal analyzer, A i is the integral value corresponding to the crystallization peak area, the unit is W·℃·g -1 ; At the same time, the cross-sectional dimensions of lithium aluminosilicate glass during molding satisfy the following relationship: S i =K÷A i ; In the formula, S i The cross-sectional dimensions of the lithium aluminosilicate glass actually produced, in dm 2 ; K=S max ×A max ;S i ≥S max ; Among them, S max A is the maximum cross-sectional size of lithium aluminosilicate glass that can be produced by the production line itself; max It is the maximum acceptable crystallization degree when the production line can produce lithium aluminum silicon glass plates with the largest cross-sectional size and the product yield is 80%; the unit of K is dm 2 ·W·℃·g -1 ; The composition of the lithium aluminosilicate glass, measured in terms of mole percentage of oxides, includes the following components: SiO2: 50.00mol% ~ 75.00mol%; Al2O3: 5.00mol% ~ 20.00mol%; Li2O: 0.01mol%~15.00mol%; Na2O: 2.00mol%~12.00mol%.

9. The preparation method according to claim 8, characterized in that: The composition of the lithium aluminosilicate glass, measured in terms of mole percentage of oxides, also includes the following components: P2O5: 0.00mol%~10.00mol%; K2O: 0.00mol% ~ 2.00mol%; MgO: 0.00mol% ~ 10.00mol%; CaO: 0.00mol% ~ 5.00mol%; SrO:0.00mol%~2.00mol%; ZnO: 0.00mol% ~ 1.00mol%; ZrO2: 0.00mol%~3.00mol%; B2O3: 0.00mol% ~ 5.00mol%; La2O3: 0.00mol% ~ 3.00mol%; Y2O3: 0.00mol% ~ 3.00mol%.

10. The preparation method according to any one of claims 8 to 9, characterized in that: The glass has a thickness of 0.1 to 2.0 mm.

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