CN108640526B - Glass ceramics - Google Patents
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- CN108640526B CN108640526B CN201810672870.1A CN201810672870A CN108640526B CN 108640526 B CN108640526 B CN 108640526B CN 201810672870 A CN201810672870 A CN 201810672870A CN 108640526 B CN108640526 B CN 108640526B
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- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C10/00—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition
- C03C10/0009—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition containing silica as main constituent
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Abstract
The invention discloses microcrystalline glass which comprises the following components in percentage by weight: SiO 22：65～80％，Al2O3：0～3.5％，Li2O：7～12.5％，K2O：0.5～3％，3％<Y2O3≦10％，P2O5：1.5～4％，ZrO2: 1-5%, MgO: 0.5-2%, ZnO: 0.5 to 2 percent. The invention solves the problem of forming hair cream of the microcrystalline glass which takes quartz solid solution and lithium disilicate as main crystal phases by adjusting the components of the microcrystalline glass, ensures that the internal quality of the microcrystalline glass is uniform, and the microcrystalline glass can be produced efficiently and stably, has high hardness, high Young modulus and higher transmittance, and is widely applied.
Description
Technical Field
The invention relates to microcrystalline glass.
Background
The microcrystalline glass using quartz solid solution and lithium disilicate as main crystal phase has controllable thermal expansion coefficient, high hardness, high mechanical strength, high heat stability, high chemical stability, high electric insulating property and high transparency, and may be used as the substrate of dielectric film in filter, protecting mirror, magnetic disc substrate, etc.
The microcrystalline glass is a material which forms a random uniform network structure through rapid cooling. During the production of the glass ceramics, the glass ceramics are firstly cooled to become a uniform glass body, and then the uniform distribution and controllable growth of crystals in the glass are achieved through subsequent heat treatment. At present, the heat treatment temperature of the microcrystalline glass is divided into two stages, namely a nucleation stage and a crystal growth stage.
In the forming process of the original glass of the microcrystalline glass, the glass is easy to be milky and green, so that crystal nuclei or crystals with different sizes appear in the glass, and after heat treatment, the sizes and the distribution of the crystals in the glass are not uniform, so that the performance of the glass generates huge fluctuation; particularly in the initial glass molding for molding a glass ceramics having a quartz solid solution and lithium disilicate as main crystal phases, it is easy to develop stringiness and greenness, resulting in non-uniformity in the inside of the glass, and continuous stable production with high efficiency is not possible.
Disclosure of Invention
The invention aims to provide the microcrystalline glass which has high hardness and high Young modulus and can be stably produced.
The technical scheme adopted by the invention for solving the technical problems is to provide a microcrystalThe glass comprises the following components in percentage by weight: SiO 22：65～80％，Al2O3：0～3.5％，Li2O：7～12.5％，K2O：0.5～3％，3％<Y2O3≦10％，P2O5：1.5～4％，ZrO2：1～5％，MgO：0.5～2％，ZnO：0.5～2％。
Further, the microcrystalline glass also comprises the following components in percentage by weight: TiO 22：0～2％，B2O3：0～2％，CaO：0～2％，BaO：0～2％，SrO：0～2％，SnO2：0～2％，La2O3：0～3％，Nb2O5：0～1％，Ta2O5：0～1％，WO3: 0-1%, clarifying agent: 0 to 2 percent.
Preferably, in the above-mentioned glass ceramics, SiO is2：70～77％。
Preferably, in the above-mentioned glass ceramics, Al is2O3：1～3.5％。
Preferably, in the above-mentioned glass ceramics, Li2O：7～10％。
Preferably, in the above-mentioned glass ceramics, Y is2O3：4～8％。
Preferably, in the above-mentioned glass ceramics, K is2O：0.5～2％。
Preferably, in the above-mentioned glass ceramics, P is2O5：1.5～4％。
Preferably, in the above-mentioned microcrystalline glass, ZrO2：1～5％。
Preferably, in the above glass ceramics, MgO: 0.5 to 2 percent.
Preferably, in the above glass ceramics, ZnO: 0.5 to 2 percent.
Preferably, in the above-mentioned glass ceramics, TiO2：0.5～1.5％。
Preferably, in the above-mentioned glass ceramics, B2O3：0～1％。
Preferably, in the above-mentioned glass ceramics, a ratio of CaO: 0 to 1 percent.
Preferably, in the above glass ceramics, BaO: 0 to 1 percent.
Preferably, in the above glass ceramics, SrO: 0 to 1 percent.
Preferably, in the above-mentioned glass ceramics, SnO2：0.01～1％。
Preferably, in the above-mentioned glass ceramics, La2O3：0～2％。
Preferably, in the above-described glass ceramics, the refining agent: 0 to 1 percent.
Wherein, in the microcrystalline glass, the clarifying agent is As2O3、Sb2O3、CeO2And from F, Cl, NOx、SOxAt least one selected from the group of (1).
Wherein in the microcrystalline glass, Al is2O3And Y2O3Is not less than 6.5%.
Wherein, in the above-mentioned microcrystalline glass, ZrO2And P2O5The total content of (A) is 4-7%.
In the microcrystalline glass, the main crystal phase of the microcrystalline glass is quartz and/or a quartz solid solution.
In the microcrystalline glass, the secondary crystal phase of the microcrystalline glass is lithium disilicate crystal.
Wherein, in the microcrystalline glass, the grain size of the microcrystalline glass is not more than 500 nm.
Wherein, in the above-mentioned microcrystalline glass, the microcrystalline glass has a Vickers hardness of not less than 750kgf/mm2。
Wherein, in the glass ceramics, the Young modulus of the glass ceramics is not less than 110 GPa.
Wherein, in the microcrystalline glass, the transmittance of the microcrystalline glass with the thickness of 1mm in the wavelength range of 400 nm-1600 nm is not less than 50%.
The invention has the beneficial effects that:
the invention solves the problem of the forming hair cream of the microcrystalline glass which takes quartz solid solution and lithium disilicate as main crystal phases by adjusting the components of the microcrystalline glass, so that the internal quality of the microcrystalline glass is uniform and the microcrystalline glass can be produced efficiently and stably; the microcrystalline glass has high hardness, high Young's modulus and high transmittance, can be used as a substrate of a dielectric film in a filter, a protective glass, a magnetic disk substrate and the like, and has wide application value.
Drawings
Fig. 1 is an XRD graph of the glass-ceramic of example 1 of the present invention.
FIG. 2 is a graph showing transmittance curves of 400 to 1600nm at a thickness of 1mm in the glass-ceramic of example 13.
FIG. 3 shows the micro-morphology of the microcrystalline glass of example 13 of the present invention on a scale of 1 μm.
Detailed Description
Glass ceramics are also called glass ceramics, and are materials obtained by heat treatment of glass to cause precipitation of crystals in the glass. The glass-ceramic of the present invention is a material having a crystal phase and a glass phase, which is different from amorphous and crystalline solids. The crystallized glass can have properties, such as young's modulus and hardness, which cannot be obtained in glass, due to crystals dispersed therein.
Specifically, the microcrystalline glass comprises the following components in percentage by weight: SiO 22：65～80％，Al2O3：0～3.5％，Li2O：7～12.5％，K2O：0.5～3％，3％<Y2O3≦10％，P2O5：1.5～4％，ZrO2：1～5％，MgO：0.5～2％，ZnO：0.5～2％。
The reasons for the limitations of the composition and content of the glass ceramics of the present invention, as well as the Young's modulus, hardness, transmittance and main crystal phase are described below.
The inventors of the present invention have made extensive experiments and studies, and have obtained a glass-ceramic of the present invention at a low cost by specifying the content and content ratio of specific components constituting the glass-ceramic to specific values and precipitating specific crystal phases. The compositional ranges of the respective components of the glass ceramics of the present invention will be explained below.
SiO2The component (b) is an essential component for forming the glass network structure of the glass ceramics of the present invention, and can be an essential component for constituting a crystal phase by heat treatment of the original glass. If the amount is less than 65%, the hardness of the resulting glass is poor and the devitrification resistance is also poor. Thus, SiO2The lower limit of the content of the component (B) is preferably 65.0%, more preferably 70.0%. On the other hand, by using SiO2The content of the component is 80.0% or less, and excessive viscosity increase and melting property decrease can be inhibited, and SiO2When the content is too high, the glass is liable to crystallize during molding. Thus, SiO2The upper limit of the content of the component (B) is preferably 80.0%, more preferably 77.0%.
Li2The component O is a component for improving the low-temperature melting property and the formability of the glass, and can be an essential component for constituting a crystal phase even by heat treatment of the raw glass. However, if the amount is less than 7.0%, the effect of forming crystals is not good. On the other hand, if Li is contained excessively2The component O is easily crystallized during molding, and the main crystal phase is changed, so that the glass is easily opaque during crystallization. Thus, Li2The upper limit of the content of the O component is preferably 12.5%, more preferably 10%.
Y2O3The component (A) is a component necessary for improving the hardness and Young's modulus of the glass ceramics and further suppressing crystallization during molding. If the amount is less than 3%, the resulting glass has poor hardness, low Young's modulus, and poor resistance to devitrification. Thus, Y2O3The content of the component (A) is more than 3%, preferably not less than 4.0%, more preferably not less than 5%. On the other hand, if Y is contained excessively2O3The components are poor in glass forming performance and easy to crystallize. Thus, Y2O3The upper limit of the content of the component (B) is preferably 10.0%, more preferably 8.0%.
Al2O3With SiO2Also a component forming a network structure of glass, which is a component contributing to the stabilization of the original glass,Important optional ingredients to improve chemical durability. Al (Al)2O3The lower limit of the content is 0%, preferably 1%. On the other hand, if Al2O3When the content of (b) exceeds 3.5%, the glass is easily devitrified during crystallization, resulting in a decrease in the hardness of the glass-ceramic. Thus, Al2O3The upper limit of the content is 3.5%.
In the present invention, Y is controlled2O3And Al2O3The total content is not less than 6.5%, the crystallization of the original glass (glass before crystallization) during molding is reduced, the crystal molding is more stable, and the crystallization effect is not influenced.
K2The main function of O is to promote the melting of the glass and to lower the melting temperature of the glass, and the addition of small amounts can prevent the crystallization of the starting glass during shaping on the one hand and can promote the formation of quartz crystals or quartz solid solutions during crystallization on the other hand, so that K is the product of2The lower limit of the content of the O component is 0.5%; if K is2When the O content exceeds 3%, undesirable crystals such as potassium feldspar are formed in the glass ceramics, and the crystals in the glass become coarse and large, which affects the transmittance of the glass and easily causes devitrification at the time of molding. Thus, K2The upper limit of the content of the O component is preferably 3.0%, more preferably 2.0%.
The MgO contributes to lowering the viscosity of the glass and suppressing devitrification of the raw glass during molding, and also has the effect of improving the low-temperature meltability, and the lower limit of the MgO content is preferably more than 0.5%; however, if the content of MgO is too high, devitrification resistance may be deteriorated, and undesirable crystals are obtained after crystallization, resulting in deterioration of the performance of the glass ceramics, so that the upper limit of the content of MgO is preferably 2%.
ZnO can improve the melting performance of the glass, inhibit crystallization of the original glass during forming and improve the chemical stability of the glass, and the lower limit of the ZnO content is preferably more than 0.5 percent; on the other hand, the upper limit of the ZnO content is controlled to 2% or less, and the deterioration of the devitrification property can be suppressed.
P2O5The reason why phase separation can be performed in the glass to form crystal nuclei is to contribute to improvement of low-temperature meltability of the glass. P2O5The lower limit of the content is preferably 1.5%, butIf it contains too much P2O5The deterioration of devitrification resistance and phase separation of the glass are easily caused. Thus, P2O5The upper limit of the content is preferably 4%.
ZrO2It also has a function of forming crystal nuclei by precipitation of crystals, and is a component contributing to improvement of chemical durability of the glass. ZrO (ZrO)2The lower limit of the content is preferably 1%, but if ZrO is contained excessively2The resistance to devitrification of the glass is easily lowered. Thus, ZrO2The upper limit of the content is preferably 5%.
In the present invention, ZrO is controlled so that devitrification resistance at the time of melting, meltability and formability are improved and uniform crystals can be precipitated2And P2O5Total content of, i.e. ZrO2+P2O54 to 7 percent.
In the present invention, in order to obtain uniform, fine and more crystal phases in the glass and thereby improve the hardness and young's modulus of the glass-ceramic substrate, it is necessary to control Y2O3And Al2O3Total content of (i.e. Y)2O3+Al2O3Is not less than 6.5%.
TiO2Is an optional component which is helpful for reducing the melting temperature of the microcrystalline glass and improving the chemical durability. TiO 22The lower limit of the content is preferably more than 0, more preferably 0.5%. On the other hand, an excess of TiO2The glass forming and crystallization can be promoted. Thus, TiO2The upper limit of the content is preferably 2%, more preferably 1.5%.
B2O3The glass is beneficial to reducing the viscosity of the glass, improving the melting property and the formability of the glass and improving the toughening property of the glass, so the glass can be added as an optional component. If B is contained excessively2O3The chemical durability of the glass ceramics is likely to be lowered, and the precipitation of desired crystals is likely to be suppressed. Thus, B2O3The upper limit of the content is preferably 2%, more preferably 1%.
CaO is an optional component contributing to improvement of the low-temperature melting property of the glass, but if CaO is contained excessively, resistance to devitrification is liable to be lowered. Therefore, the upper limit of the CaO content is preferably 2%, and most preferably 1%.
BaO is an optional component contributing to improvement of the low-temperature melting property of the glass, but if BaO is excessively contained, resistance to devitrification is easily lowered. Therefore, the upper limit of the BaO content is preferably 2%, and most preferably 1%.
SrO is an optional component for improving the low-temperature melting property of the glass, but if SrO is contained excessively, resistance to devitrification is liable to be lowered. Therefore, the upper limit of the SrO content is preferably 2%, and most preferably 1%.
SnO2Is an optional component capable of exerting the function as a clarifying agent and the function of precipitating crystals to form crystal nuclei. Thus, SnO2The lower limit of the content is preferably more than 0, more preferably 0.01%, most preferably 0.05%; however, if it contains too much SnO2The resistance to devitrification of the glass is easily lowered. Thus, SnO2The upper limit of the content is preferably 2%, more preferably 1%, still more preferably 0.4%, most preferably 0.2%.
La2O3Is an optional component for improving the hardness of the microcrystalline glass, can reduce the melting temperature of the glass by adding a small amount, and can reduce the liquid phase temperature to a certain extent, but if La is excessively contained, the hardness of the microcrystalline glass is improved2O3The resistance to devitrification is liable to be lowered. Thus, La2O3The content of (b) is 3% or less, preferably 2% or less, and most preferably 1%.
Nb2O5Is an optional component for improving the mechanical properties of the glass-ceramic, but if Nb is contained excessively2O5The resistance to devitrification is liable to be lowered. Thus, Nb2O5The upper limit of the content is preferably 1%.
Ta2O5Is an optional component for improving the mechanical properties of the glass, but if Ta is contained excessively2O5The resistance to devitrification is liable to be lowered. Thus, Ta2O5The upper limit of the content is preferably 1%.
WO3Is an optional component for improving the mechanical properties of the glass, but if too much WO is contained3Then it is durableThe devitrification is easily reduced. Thus, WO3The upper limit of the content is preferably 1%.
As may be contained As a fining agent in the glass ceramics of the present invention2O3、Sb2O3、CeO2And from F, Cl, NOx、SOxGroup (e.g. NaCl, Na)2SO4Etc.); the upper limit of the content of the clarifying agent is preferably 2%, more preferably 1%.
The crystallized glass of the present invention is a material having a crystal phase and a glass phase, which is different from an amorphous solid. The crystalline phase of the glass-ceramic can be distinguished by the angle of the peak value appearing in the X-ray diffraction pattern of the X-ray diffraction analysis, the main crystalline phase of the glass-ceramic is quartz or quartz solid solution, and the secondary crystalline phase of the glass-ceramic is lithium disilicate crystal.
Wherein, the crystal phase of quartz and quartz solid solution belongs to a trigonal or hexagonal system, and exists in the microcrystalline glass in a spherical form, so that the hardness and Young modulus of the microcrystalline glass are improved; the lithium disilicate crystal phase being based on [ Si ]2O5]The crystal shape of the tetrahedral array orthorhombic crystal is flat or plate-shaped, and the lithium disilicate crystal phase is a random non-oriented interlocking microstructure in the microcrystalline glass, so that the hardness and the Young modulus of the microcrystalline glass are improved.
The crystallite glass of the invention has the crystal size of preferably below 500nm, and has smaller crystal size, so that the crystallite glass has relatively high transmittance.
The Vickers hardness (Hv) of the glass-ceramic of the present invention is preferably not less than 750kgf/mm2. With such hardness, occurrence of scratches can be suppressed, and mechanical strength can be improved. Therefore, the Vickers hardness (Hv) of the glass-ceramic of the present invention is preferably not less than 750kgf/mm2More preferably not less than 760kgf/mm2Most preferably not less than 770kgf/mm2。
The glass ceramics of the present invention preferably have a young's modulus of not less than 110 GPa. Since the glass has a high Young's modulus and the glass has an increased rigidity, the Young's modulus of the glass ceramics of the present invention is preferably not less than 110GPa, more preferably not less than 115 GPa.
In the crystallized glass of the present invention, the transmittance of the 1mm glass sheet in the wavelength range of 400 to 1600nm is more than 50%, more preferably more than 70%, and still more preferably more than 80%.
The microcrystalline glass of the present invention can be prepared by the following method: uniformly mixing raw materials (the raw materials of each component can be corresponding oxides, composite salts, metal fluorides and the like) according to the component proportion range, putting the uniform mixture into a crucible made of platinum or quartz, melting the mixture for 5 to 24 hours in an electric furnace or a gas furnace at the temperature of 1250 to 1600 ℃ according to the melting difficulty of glass composition, stirring the mixture to be uniform, cooling the mixture to a proper temperature, casting the mixture into a mold, and slowly cooling the mixture to obtain raw glass;
the raw glass is crystallized to uniformly deposit crystals in the glass. The crystallization may be performed in 1 stage or 2 stages, but the crystallization is preferably performed in 2 stages. The treatment of the nucleation process is performed at the 1 st temperature, and then the treatment of the crystal growth process is performed at the 2 nd temperature higher than the nucleation process temperature. The crystallization process performed at the 1 st temperature is referred to as a 1 st crystallization process, and the crystallization process performed at the 2 nd temperature is referred to as a 2 nd crystallization process.
In order to obtain desired physical properties of the glass ceramics, preferred heat treatment conditions are:
the above-mentioned crystallization treatment is performed in 1 stage, and the nucleus formation process and the crystal growth process can be continuously performed. That is, the temperature is raised to a predetermined crystallization temperature, and after reaching the heat treatment temperature, the temperature is maintained for a certain period of time, and then the temperature is lowered. The temperature of the crystallization treatment is preferably 500-700 ℃, and the holding time at the crystallization treatment temperature is preferably 0-8h, and more preferably 1-6h, in order to precipitate a desired crystal phase, more preferably 550-680 ℃.
When the crystallization treatment is performed in 2 stages, the 1 st temperature is preferably 500-700 ℃, and the 2 nd temperature is preferably 650-850 ℃. The holding time at the temperature 1 is preferably from 0 to 24h, most preferably from 2 to 15 h. The holding time at the 2 nd temperature is preferably from 0 to 10 hours, most preferably from 2 to 5 hours.
The above-mentioned holding time of 0 minutes means that the temperature is lowered or raised less than 1 minute after the temperature is reached.
The present invention is further illustrated by the following examples, which are not intended to limit the scope of the invention.
Examples 1 to 40 (tables 1 to 4) of the present invention microcrystalline glasses were prepared by the following methods: firstly, selecting raw materials of various components, selecting respective corresponding raw materials of oxides, hydroxides, carbonates, nitrates, fluorides, chlorides, hydroxides, metaphosphoric acid compounds and the like, uniformly mixing the raw materials according to the component proportion range, putting the uniform mixture into a crucible made of platinum or quartz, melting the mixture for 5-24 hours in an electric furnace or a gas furnace at the temperature of 1250-1600 ℃ according to the melting difficulty of glass composition, stirring the mixture uniformly, cooling the mixture to a proper temperature, casting the mixture into a mold, and slowly cooling the mixture to obtain raw glass;
the core formation and crystallization were carried out in 2 stages for the obtained raw glass, and in tables 1 to 4, the heat treatment conditions of the 1 st stage were recorded in the column of "nucleation process", and the heat treatment conditions of the 2 nd stage were recorded in the column of "crystallization process", and the temperature of the heat treatment and the holding time at the temperature thereof were as shown in the tables.
In the examples, the crystalline phase of the crystallized glass was analyzed by an X-ray diffraction analyzer from the angle of the peak shown in the X-ray diffraction pattern.
In the embodiment, the size of the crystal grain of the microcrystalline glass is determined by using an SEM scanning electron microscope, the microcrystalline glass is subjected to surface treatment in HF acid, the surface of the microcrystalline glass is sprayed with gold, and the surface scanning is performed under the SEM scanning electron microscope to determine the size of the crystal grain.
The Vickers hardness of the crystallized glass in the examples was calculated by dividing the load (N) when a diamond quadrangular pyramid indenter having an included angle of 136 degrees with respect to the opposing surface was pressed into a pyramid-shaped indentation on the test surface by the surface area (mm) calculated from the length of the indentation2) The value of (d) represents; the test load was set to 100(N) and the holding time was set to 20 (sec).
The young's modulus of the glass ceramics in the examples was measured by using an ultrasonic probe, and the elastic constant of the material was obtained from the propagation speed of elastic waves in a solid sample.
The microcrystalline glass of the examples had a light transmittance in the wavelength range of 400-.
The compositions, heat treatment conditions and properties of the microcrystalline glasses of examples 1 to 40 are shown in tables 1 to 4:
TABLE 1 examples 1 to 10 microcrystalline glasses
TABLE 2 examples 11 to 20 microcrystalline glasses
TABLE 3 examples 21 to 30 microcrystalline glasses
TABLE 4 examples 31 to 40 microcrystalline glasses
As can be seen from the above examples, the crystallized glass of the present invention has high hardness, high young's modulus, and high transmittance, and can be used as a substrate for a dielectric film in a filter, a protective mirror, a magnetic disk substrate, and the like.
Claims (19)
1. The microcrystalline glass is characterized in that: comprises the following components in percentage by weight: SiO 22：65～80％，Al2O3：0～3.5％，Li2O：7～12.5％，K2O：0.5～3％，3％<Y2O3≦10％，P2O5：1.5～4％，ZrO2：1～5％，MgO：0.5～2％，ZnO：0.5～2％。
2. The glass-ceramic according to claim 1, characterized in that: also comprises the following components in percentage by weight: TiO 22：0～2％，B2O3：0～2％，CaO：0～2％，BaO：0～2％，SrO：0～2％，SnO2：0～2％，La2O3：0～3％，Nb2O5：0～1％，Ta2O5：0～1％，WO3: 0-1%, clarifying agent: 0 to 2 percent.
3. A glass-ceramic according to claim 1 or 2, characterized in that: at least one of the following is satisfied:
SiO2：70～77％；
Al2O3：1～3.5％；
Li2O：7～10％；
Y2O3：4～8％；
K2O：0.5～2％；
P2O5：1.5～4％；
ZrO2：1～5％；
MgO：0.5～2％；
ZnO：0.5～2％。
4. a glass-ceramic according to claim 2, characterized in that: at least one of the following is satisfied:
TiO2：0.5～1.5％；
B2O3：0～1％；
CaO：0～1％；
BaO：0～1％；
SrO：0～1％；
SnO2：0.01～1％；
La2O3：0～2％；
a clarifying agent: 0 to 1 percent.
5. A glass-ceramic according to claim 2, characterized in that: the clarifying agent is As2O3、Sb2O3、CeO2And from F, Cl, NOx、SOxAt least one selected from the group of (1).
6. A glass-ceramic according to claim 1 or 2, characterized in that: al (Al)2O3And Y2O3Is not less than 6.5%.
7. A glass-ceramic according to claim 1 or 2, characterized in that: ZrO (ZrO)2And P2O5The total content of (A) is 4-7%.
8. The glass-ceramic according to any one of claims 1, 2, 4 or 5, characterized in that: the main crystal phase of the microcrystalline glass is quartz and/or quartz solid solution.
9. A glass-ceramic according to claim 3, characterized in that: the main crystal phase of the microcrystalline glass is quartz and/or quartz solid solution.
10. The glass-ceramic according to claim 6, characterized in that: the main crystal phase of the microcrystalline glass is quartz and/or quartz solid solution.
11. The glass-ceramic according to claim 7, characterized in that: the main crystal phase of the microcrystalline glass is quartz and/or quartz solid solution.
12. The glass-ceramic according to any one of claims 1, 2, 4 or 5, characterized in that: the secondary crystal phase of the microcrystalline glass is lithium disilicate crystal.
13. A glass-ceramic according to claim 3, characterized in that: the secondary crystal phase of the microcrystalline glass is lithium disilicate crystal.
14. The glass-ceramic according to claim 6, characterized in that: the secondary crystal phase of the microcrystalline glass is lithium disilicate crystal.
15. The glass-ceramic according to claim 7, characterized in that: the secondary crystal phase of the microcrystalline glass is lithium disilicate crystal.
16. The glass-ceramic according to any one of claims 1, 2, 4 or 5, characterized in that: at least one of the following is satisfied:
the crystallite size of the microcrystalline glass is not more than 500 nm;
the microcrystalline glass has a Vickers hardness of not less than 750kgf/mm2；
The Young modulus of the microcrystalline glass is not less than 110 GPa;
the transmittance of the 1mm microcrystalline glass in the wavelength range of 400 nm-1600 nm is not less than 50%.
17. A glass-ceramic according to claim 3, characterized in that: at least one of the following is satisfied:
the crystallite size of the microcrystalline glass is not more than 500 nm;
the microcrystalline glass has a Vickers hardness of not less than 750kgf/mm2；
The Young modulus of the microcrystalline glass is not less than 110 GPa;
the transmittance of the 1mm microcrystalline glass in the wavelength range of 400 nm-1600 nm is not less than 50%.
18. The glass-ceramic according to claim 6, characterized in that: at least one of the following is satisfied:
the crystallite size of the microcrystalline glass is not more than 500 nm;
the microcrystalline glass has a Vickers hardness of not less than 750kgf/mm2；
The Young modulus of the microcrystalline glass is not less than 110 GPa;
the transmittance of the 1mm microcrystalline glass in the wavelength range of 400 nm-1600 nm is not less than 50%.
19. The glass-ceramic according to claim 7, characterized in that: at least one of the following is satisfied:
the crystallite size of the microcrystalline glass is not more than 500 nm;
the microcrystalline glass has a Vickers hardness of not less than 750kgf/mm2；
The Young modulus of the microcrystalline glass is not less than 110 GPa;
the transmittance of the 1mm microcrystalline glass in the wavelength range of 400 nm-1600 nm is not less than 50%.
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| CN112608032B (en) * | 2018-10-26 | 2022-04-22 | 成都光明光电股份有限公司 | Glass ceramics, glass ceramics product and manufacturing method thereof |
| CN113831020A (en) * | 2021-01-28 | 2021-12-24 | 成都光明光电股份有限公司 | Glass ceramics, glass ceramics product and manufacturing method thereof |
| CN113213949B (en) * | 2021-03-10 | 2022-11-01 | 安徽华封电子科技有限公司 | High-frequency low-loss LTCC substrate material capable of being electroplated or chemically plated and preparation method thereof |
| CN112939469B (en) * | 2021-03-23 | 2022-03-08 | 成都光明光电股份有限公司 | Glass ceramics and glass ceramics product |
| CN112919810B (en) * | 2021-03-23 | 2022-02-18 | 成都光明光电股份有限公司 | Glass-ceramic, glass-ceramic article and method for producing same |
| CN117819824B (en) * | 2023-10-10 | 2024-10-01 | 常熟佳合显示科技有限公司 | Lithium aluminum silicon microcrystalline glass and preparation method thereof |
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