CN113354288B - Microcrystalline glass plate and preparation method thereof - Google Patents
Microcrystalline glass plate and preparation method thereof Download PDFInfo
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- CN113354288B CN113354288B CN202110690382.5A CN202110690382A CN113354288B CN 113354288 B CN113354288 B CN 113354288B CN 202110690382 A CN202110690382 A CN 202110690382A CN 113354288 B CN113354288 B CN 113354288B
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- C—CHEMISTRY; METALLURGY
- 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
- C03C10/0036—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 SiO2, Al2O3 and a divalent metal oxide as main constituents
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- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
- C03B32/00—Thermal after-treatment of glass products not provided for in groups C03B19/00, C03B25/00 - C03B31/00 or C03B37/00, e.g. crystallisation, eliminating gas inclusions or other impurities; Hot-pressing vitrified, non-porous, shaped glass products
- C03B32/02—Thermal crystallisation, e.g. for crystallising glass bodies into glass-ceramic articles
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- C—CHEMISTRY; METALLURGY
- 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
- C03C10/16—Halogen containing crystalline phase
Abstract
The application provides a microcrystalline glass plate and a preparation method thereof, and a main crystal phase stilbite NaCa of the microcrystalline glass plate 2 Si 4 O 10 F accounts for the following mass percent: 20% -70%; s1, preparing a glass frit by adopting a fusion method, drying, and crushing the glass frit into a certain particle range by using a double-roll crusher to obtain a glass frit A; s2, according to the mass percentage, stirring and mixing 65-85% of glass frit A, 10-27% of clay B and 3-15% of bonding additive C uniformly in a stirring tank, homogenizing, and performing dry pressing to obtain a microcrystalline glass green body, wherein the glass frit A contains 8-15% of CaO and Na 2 O 3‑7％，SiO 2 60-72% of F3-7%; s3, firing at 600-630 ℃ for 30-50min, and at 880-1000 ℃ for 30-50 min; and S4, polishing to obtain the microcrystalline glass plate.
Description
Technical Field
The application relates to the field of microcrystalline glass, in particular to a microcrystalline glass plate and a preparation method thereof.
Background
The microcrystal glass plate is a mixture of microcrystal and glass prepared from proper glass particles through sintering and crystallization. The microcrystalline glass plate looks different from common glass, has the dual characteristics of glass and ceramic, has texture on the outer surface which is more inclined to the ceramic, but has higher brightness than the ceramic, certain light transmittance, and natural jade feeling by combining the crystal morphology, and has stronger toughness, bending strength and bending strength than the glass, and mechanical strength which can meet the use function of paving and pasting the ground and the wall.
The microcrystalline glass plate in the prior art has rich and various main crystal phases, wherein most of the main crystal phases of the jade series microcrystalline glass are the xonotlite, the crystallization temperature required for the production of the crystal phases is 800-900 ℃, the time required for heat preservation and crystallization is more than 60min, the total crystallization energy consumption is high, and the microcrystalline glass taking the xonotlite as the main crystal phase has insufficient impact toughness and poor processing and cutting performance when the light transmittance reaches a certain degree.
The production method of the microcrystalline glass plate in the prior art mainly comprises the following steps
1. Preparing by a rolling method: taking the publication number CN105271642B as an example, the method mainly comprises the steps of adding ingredients into a melting furnace, clarifying the melted ingredients under the condition of stirring to generate a proportional melt, and then feeding the glass melt into a roller press for rolling and calendering to form a glass plate; and finally, entering a roller kiln, and performing primary nucleation, reinforced nucleation and crystallization to obtain the microcrystalline glass plate. The disadvantages of this method are: the production capacity is very low, (2) the production process is very unstable, (3) the production condition requirement is high, (4) the energy consumption is very high, and finally the whole production cost is very high; in addition, the product has single color and only white color, has higher expansion coefficient and is not easy to carry out secondary decoration on the microcrystalline glass plate.
2. The advanced preparation method of the calendering method comprises the following steps: taking the publication number CN105294168B as an example, the method is to carry out ink-jet decoration on the basis of obtaining a basic microcrystalline glass plate by a rolling method and further attach a layer of low-temperature fritted glaze, thereby solving the problem of single product. However, this method requires secondary firing, which increases the cost and energy consumption.
3. Preparing by a sagger method: taking the publication number CN111960674A as an example, the method is formed by sintering a refractory material sagger, and the method comprises the steps of pre-burning a microcrystalline glass raw material to prepare microcrystalline glass granules with different grain sizes, taking the granules as a composition raw material, classifying and screening the granules, layering and stacking the different granular granules, and then carrying out nucleation and crystallization in a kiln to obtain the microcrystalline glass plate. The method is likely to be difficult to industrialize and is not applied much.
The main problems of the prior art for comprehensively producing the microcrystalline glass plate are that the product process is complex, the production process is unstable, the yield is low, and therefore, the whole production cost is very high.
Disclosure of Invention
The main purpose of the present application is to provide a main crystal phase of stilbite NaCa 2 Si 4 O 10 F, and provides a preparation method of the microcrystalline glass plate, aiming at solving the problems of complex production process, difficult control of production conditions, low productivity and the like in the prior art.
In order to achieve the purpose, the application provides a microcrystalline glass plate and a preparation method thereof.
The application provides a microcrystalline glass plate, the main crystal phase of which is stilbite, stilbite NaCa 2 Si 4 O 10 The main crystal phase of F accounts for the mass percent of the material: 20 to 70 percent.
Preferably, the microcrystalline glass plate comprises the following crystalline phases in percentage by mass:
stilbite NaCa 2 Si 4 O 10 F30-50%; calcium fluoride CaF 2 1 to 10 percent; bulk stevensite Mg 3 SiO 4 F 2 0.5 to 5 percent; kaliophilite KAlSiO 4 0.5-5％。
The application also provides a preparation method of the microcrystalline glass plate, which comprises the following steps:
s1, preparing a glass frit A by adopting a fusion method;
s2, uniformly mixing 65-85% of glass frit A, 10-27% of clay B and 3-15% of bonding additive C by mass percent, homogenizing, and performing dry pressing forming to obtain a microcrystalline glass green body;
s3, firing;
s4, polishing to obtain a microcrystalline glass plate;
the glass frit A contains CaO8-15%, and Na in terms of chemical oxides 2 O 3-7％，SiO 2 60-72％，F 3-7％；
The temperature of the sintering is kept at 600-630 ℃ for 30-50min, and the temperature of 880-1000 ℃ for 30-50min.
Preferably, the glass frit A comprises the following components in percentage by weight of chemical oxides: siO 2 2 60-72％，Al 2 O 3 1.5～6％，CaO 8-15％，K 2 O 3-7％，Na 2 O 3-7％，MgO 0-1％，F 3-7％，CeO 2 0-1％，Fe 2 O 3 0-0.1％。
Preferably, clay B is: one or more of bentonite and kaolin.
Preferably, the bonding additive C is: one or more of polyacrylic resin, polyvinyl acetate, polyethylene-vinyl acetate and the above modified resins.
Preferably, the following steps are further included between step S2 and step S3;
s2-1, applying a layer of ground coat on the microcrystalline glass green body obtained in the step S2;
s2-2, decorating the microcrystalline glass green body obtained in the step S2-1;
s2-3, applying a layer of transparent dry particles on the green glass-ceramic body obtained in the step S2-2;
preferably, the ground coat comprises the following chemical components in percentage by mass: siO 2 2 55-65％，Al 2 O 3 4-9％，B 2 O 3 0.5-2％，CaO 13-22％，ZnO 1-5％，BaO 2-8％，K 2 O 1-5％，Na 2 O 3-7％。
Preferably, the chemical composition of the transparent dry granules is as follows by mass percent: siO 2 2 35-48％，Al 2 O 3 11-14％，B 2 O 3 18-22％，CaO 7-10％，ZnO 0.5-1.5％，BaO 5-7％，K 2 O 3-5％，Na 2 O 3-5％，Li 2 O 1-3％。
Preferably, the thickness of the cloth of the transparent dry granules is 500-1500g/m 2 。
In the microcrystalline glass plate in the prior art, the main crystal phase is the xonotlite, the crystallization temperature required for producing the crystal phase is 800-900 ℃, the heat preservation crystallization time is more than 60min, and the total crystallization energy consumption is high. The microcrystalline glass using the kenyaite as the main crystal phase has insufficient impact toughness when the light transmittance reaches a certain degree, and has poor processing and cutting performance. Meanwhile, compared with the microcrystalline glass with the main crystalline phase of the sillimanite, the microcrystalline glass plate with the stilbite crystalline phase has lower expansion coefficient, is more favorable for secondary decoration on the microcrystalline glass plate, and enriches the types of products.
The technical proposal is that the sintering is carried outIn the process, stilbite NaCa is generated in large quantity 2 Si 4 O 10 The crystal phase F needs to have proper contents of Ca, na, si and F elements in the glass frit and simultaneously has certain nucleation temperature and nucleation time, crystallization temperature and crystallization time, and a large amount of experimental researches show that the stilbite NaCa needs to be prepared 2 Si 4 O 10 The crystal phase of F is 20-70%, the glass frit A contains CaO8-15% and Na calculated by chemical oxide 2 O 3-7％，SiO 2 60-72% of F3-7%; the nucleation temperature is within the range of 600-630 ℃, and the optimal nucleation time is within the range of 30-50 min; the crystallization temperature is in the range of 880-1000 ℃, and the optimal crystallization time is in the range of 30-50min.
Compared with the prior art for producing the microcrystalline glass plate, the forming method in the technical scheme adopts dry pressing forming, the production process conditions of the dry pressing forming are simpler, the yield is higher, more than 20% of stilbite crystal phase needs to be generated on the microcrystalline glass plate, 65% of glass frit is needed and is a barren material, and the problem that the forming can be carried out and the bending strength of a green body is more than 4MPa needs to be solved by performing dry pressing forming on the glass frit with the content of more than 65%; experimental studies have found that this technical problem can be solved by incorporating 10-27% clay material and 3-15% binding additive.
To sum up, the following beneficial effects of this application technical scheme:
(1) The microcrystalline glass plate with stilbite as main crystal phase has proper light transmittance and whiteness, high breaking strength and impact toughness and low expansion coefficient, and is favorable for subsequent further processing.
(2) The invention provides a preparation method of a microcrystalline glass plate, which has the advantages of simple process, high yield and low energy consumption.
Drawings
In order to more clearly illustrate the embodiments of the present application or the technical solutions in the prior art, the drawings used in the description of the embodiments or the prior art will be briefly described below, it is obvious that the drawings in the following description are only some embodiments of the present application, and for those skilled in the art, other related drawings can be obtained according to the drawings without creative efforts.
FIG. 1 is a flow chart of a preparation method in an example of the present application.
Fig. 2 is an XRD diffraction pattern of the microcrystalline glass plate of example 1 of the present application.
The implementation, functional features and advantages of the object of the present application will be further explained with reference to the embodiments, and with reference to the accompanying drawings.
Detailed Description
In order to make the objects, technical solutions and advantages of the embodiments of the present application clearer, the technical solutions of the embodiments of the present application will be clearly and completely described below. The examples, in which specific conditions are not specified, were conducted under conventional conditions or conditions recommended by the manufacturer. The reagents or instruments used are not indicated by the manufacturer, and are all conventional products available commercially.
The preparation method of the microcrystalline glass plate comprises the following steps:
s1, preparing a glass frit A by adopting a fusion method;
uniformly mixing 36-46% of quartz sand, 25-32% of potash feldspar, 15-22% of calcite, 2-6% of potassium carbonate, 5-10% of sodium fluosilicate, 0-2% of soda ash and 0-1% of cerium oxide, feeding the mixture into a frit kiln, controlling the temperature range to be 1500-1600 ℃ for melting, enabling the melting period to be 10-20 hours, enabling formed glass liquid to flow to a water tank from a discharge port of the frit kiln, carrying out water quenching to produce glass frit, and crushing the frit into required particles by using a double-roller crusher to obtain the glass frit A.
S2, according to the mass percentage, stirring and mixing 65-85% of glass frit A, 10-27% of clay B and 3-15% of bonding additive C uniformly in a stirring tank, homogenizing, and performing dry pressing to obtain a microcrystalline glass green body with the thickness of 2-30 mm;
wherein the clay B is one or two of bentonite and kaolin, and the adhesive additive C is one or two of polyacrylic resin, polyvinyl acetate, polyethylene-vinyl acetate and the above modified resins.
S2-1, applying a layer of ground coat on the microcrystalline glass green body obtained in the step S2;
the ground glaze comprises the following raw materials in formula: 45-50 parts of quartz powder, 22-27 parts of calcite, 4-7 parts of soda ash, 5-8 parts of potassium carbonate, 0.5-2.5 parts of borax pentahydrate, 3-5 parts of zinc oxide, 5-8 parts of aluminum oxide and 5-7 parts of barium carbonate. Feeding into a frit kiln, controlling the temperature to be in the range of 1350-1450 ℃ for melting, feeding the glass liquid from an outlet of the frit kiln to a water tank, quenching with water, crushing the frit to 200-325 meshes, ball-milling the frit, and then adopting a glaze spraying and glaze spraying mode.
S2-2, decorating the microcrystalline glass green body obtained in the step S2-1;
s2-3, applying a layer of transparent dry particles on the microcrystalline glass green body obtained in the step S2-2;
preparation of transparent dry granules: 33-37% of quartz, 5-10% of barium carbonate, 10-15% of calcite, 8-12% of alumina, 0.5-1% of zinc oxide, and borax pentahydrate: 8-12%, boric acid: mixing 18-23% and 3-8% potassium carbonate, melting in a frit kiln at 1350-1450 deg.C, flowing the molten glass from the outlet of the frit kiln to a water tank, quenching with water, crushing the frit to 100-325 mesh, and oven drying to obtain dry transparent frit particles.
Distributing with a dry particle distributing machine, wherein the distributing thickness is 500-1500g/m 2 。
S3, firing;
s31, heating and draining: 2-10min at room temperature of-600-630 ℃;
s32, constant-temperature nucleation: 30-50min, 600-630 ℃;
s33, temperature rise: 2-10min, 600-630-880-1000 ℃;
s34, constant temperature crystallization: 30-50min,880-1000 ℃;
and S35, cooling and annealing.
S4, polishing to obtain a microcrystalline glass plate;
the glass frit a obtained in the above example was tested to have a composition and content range of components in terms of oxides: siO 2 2 60-72％，Al 2 O 3 1.5～6％，CaO 8-15％，K 2 O 3-7％，Na 2 O 3-7％，MgO 0-1％，F 3-7％，CeO 2 0-1％，Fe 2 O 3 0-0.1％。
The above examples are examples in which the formulation compositions and temperatures are within ranges, inclusive of the endpoints and any values within the ranges, are implementable, and examples of specific components and temperatures are set forth below in specific point values.
Example 1
A preparation method of a microcrystalline glass plate comprises the following steps:
s1, preparing a glass frit A by adopting a fusion method;
uniformly mixing 43% of quartz sand, 28.8% of potassium feldspar, 17.3% of calcite, 2.9% of potassium carbonate, 6.7% of sodium fluosilicate, 1% of soda ash and 0.3% of cerium oxide, feeding the mixture into a frit kiln, controlling the temperature range to be 1520 ℃ for melting, enabling the firing period to be 15 hours, enabling formed glass liquid to flow from a discharge port of the frit kiln to a water tank, carrying out water quenching to produce glass frit, and crushing the glass frit into required particles to obtain the glass frit A.
S2, according to the mass percentage, stirring and mixing 80% of glass frit A, 5% of kaolin, 10% of bentonite and 5% of adhesive additive C, namely polyvinyl acetate, in a stirring tank uniformly, homogenizing, and performing dry pressing to obtain a 10 mm-thick microcrystalline glass green body;
s3, firing;
s31, heating and draining: 5min, room temperature-620 ℃;
s32, constant-temperature nucleation: 40min,620 deg.C;
s33, temperature rising: 5min,620-920 ℃;
s34, constant temperature crystallization: 40min,920 ℃;
and S35, cooling and annealing.
S4, polishing to obtain a microcrystalline glass plate;
the glass frit a obtained in the above example was tested for composition and content of components in terms of oxides: siO 2 2 67.2％，Al 2 O 3 3.6％，CaO 12.9％，K 2 O 3.2％，Na 2 O 6.25％，MgO 0.12％，F 6.2％，CeO 2 0.52％，Fe 2 O 3 0.01％。
The microcrystalline glass has the following crystal phase contents in the tests: stilbite NaCa 2 Si 4 O 10 F48%, calcium fluoride CaF 2 3% bulk stevensite Mg 3 SiO 4 F 2 1.5 percent of kaliophilite KAlSiO 4 0.8％。
Example 2
A preparation method of a microcrystalline glass plate comprises the following steps:
s1, preparing a glass frit A by adopting a fusion method;
uniformly mixing 36% of quartz sand, 30% of potassium feldspar, 18.5% of calcite, 5.2% of potassium carbonate, 9% of sodium fluosilicate, 0.8% of soda ash and 0.5% of cerium oxide, feeding the mixture into a frit kiln, controlling the temperature range to be 1580 ℃ for melting, wherein the firing period is 20 hours, the formed glass liquid flows from a discharge port of the frit kiln to a water tank, water quenching is carried out to produce glass frit, and the frit is crushed into required particles to form the glass frit A.
S2, according to the mass percentage, 75% of glass frit A, 22% of bentonite and 3% of bonding additive C, namely polyethylene-vinyl acetate, are stirred and mixed uniformly in a stirring tank, homogenized and subjected to dry pressing forming to obtain a microcrystalline glass green body with the thickness of 3 mm;
s3, firing;
s31, heating and draining: 3min at room temperature of-610 ℃;
s32, constant-temperature nucleation: 30min,610 deg.C;
s33, temperature rising: 5min,880 ℃;
s34, constant temperature crystallization: 30min,880 deg.C;
and S35, cooling and annealing.
S4, polishing to obtain a microcrystalline glass plate;
the glass frit a obtained in the above example was tested for composition and content of components in terms of oxides: siO 2 2 66.68％，Al 2 O 3 4.2％，CaO 11.21％，K 2 O 5.62％，Na 2 O 5.47％，MgO 0.63％，F 5.56％，CeO 2 0.61％，Fe 2 O 3 0.02％。
Example 3
A preparation method of a microcrystalline glass plate comprises the following steps:
s1, preparing a glass frit A by adopting a fusion method;
uniformly mixing 46% of quartz sand, 26% of potassium feldspar, 15% of calcite, 4.5% of potassium carbonate, 6% of sodium fluosilicate, 1.5% of soda ash and 1% of cerium oxide, feeding the mixture into a frit kiln, controlling the temperature range to be 1500 ℃ for melting, wherein the firing period is 18 hours, the formed glass liquid flows from a discharge port of the frit kiln to a water tank, water quenching is carried out to produce glass frit, and the frit is crushed into required particles to form glass frit A.
S2, according to the mass percentage, 70 percent of glass frit A, 15 percent of kaolin and 5 percent of adhesive additive C are polyacrylic resin, 5 percent of polyvinyl acetate and 5 percent of polyethylene-vinyl acetate are stirred and mixed evenly in a stirring tank, homogenized and subjected to dry pressing forming to obtain a microcrystalline glass green body with the thickness of 25 mm;
s3, firing;
s31, heating and draining: 5min at room temperature of-650 ℃;
s32, constant-temperature nucleation: 50min,650 deg.C;
s33, temperature rising: 8min,650-980 ℃;
s34, constant temperature crystallization: 50min,980 deg.C;
and S35, cooling and annealing.
S4, polishing to obtain a microcrystalline glass plate;
the glass frit a obtained in the above example was tested to have a composition and contents of components in terms of oxides: siO 2 2 71.1％，Al 2 O 3 4.89％，CaO 10.28％，K 2 O 4.96％，Na 2 O 3.78％，MgO 0.24％，F 4.39％，CeO 2 0.31％，Fe 2 O 3 0.05％。
Example 4
The conditions in this example are the same as those in example 1, except that the firing in step S3 is performed with an additional strong nucleation stage, as follows:
s3, firing;
s31, heating and draining: 5min, room temperature-620 ℃;
s32, constant-temperature nucleation: 40min,620 deg.C;
s33, temperature rising: 3min,620-720 ℃;
s34, constant-temperature strong nucleation: 15min,720 ℃;
s35, temperature rising: 3min,720-920 ℃;
s36, constant-temperature crystallization: 40min,920 ℃;
s37, quenching and annealing.
S4, polishing to obtain a microcrystalline glass plate;
example 5
The conditions in the comparative example are the same as those in example 1, except that a decorative layer is added to the microcrystalline glass plate between the step S2 and the step S3, and the specific steps are as follows:
s2-1, applying a layer of ground coat on the microcrystalline glass green compact obtained in the step S2;
the ground glaze comprises the following raw materials in formula: 47.3 parts of quartz powder, 25 parts of calcite, 6 parts of soda ash, 4 parts of potassium carbonate, 1.2 parts of borax pentahydrate, 4 parts of zinc oxide, 6.5 parts of aluminum oxide and 6 parts of barium carbonate, the quartz powder, the calcite, the soda ash, the potassium carbonate, the borax pentahydrate, the zinc oxide, the aluminum oxide and the barium carbonate are fed into a frit kiln, the frit kiln is controlled to be melted within 1400 ℃, glass liquid flows to a water tank from an outlet of the frit kiln, water quenching is carried out, the frit is crushed to 200-325 meshes, and glaze spraying and glaze are adopted after the frit is subjected to ball milling.
S2-2, decorating the microcrystalline glass green body obtained in the step S2-1;
s2-3, applying a layer of transparent dry particles on the microcrystalline glass green body obtained in the step S2-2;
preparation of transparent dry granules: 35.1% of quartz, 6.7% of barium carbonate, 12.1% of calcite, 10.4% of aluminum oxide, 0.8% of zinc oxide, and borax pentahydrate: 10.7%, boric acid: 20.2 percent and 4 percent of potassium carbonate are evenly mixed and sent into a frit kiln, the temperature is controlled within 1400 ℃ for melting, glass liquid flows into a water tank from the outlet of the frit kiln, water quenching is carried out, the frit is crushed to 100-250 meshes, and the frit is dried into transparent frit dry particles.
Distributing by adopting a dry particle distributing machine, wherein the distributing thickness is 1200g/m 2 。
The performance of the microcrystalline glass sheets of examples 1 to 5 was tested, and in addition, a commercially available microcrystalline glass sheet with a thickness of 10mm and a main crystal phase of xonotlite prepared by a calendering method was purchased for comparison, and the specific performance test and effect comparison results are shown in the following table:
the transmittance detection method comprises the following steps: and (4) detecting by using a light transmittance measuring instrument.
Whiteness degree: and detecting by using a whiteness measuring instrument.
Breaking strength: and (4) detecting by using a bending strength measuring instrument.
Impact toughness: and (4) detecting by using an impact toughness measuring instrument.
Coefficient of expansion: and (4) detecting by using an expansion coefficient measuring instrument.
Crystal phase content: obtained by XRD diffraction pattern and component analysis instrument detection.
From the table, the light transmittance of the microcrystalline glass plate prepared by the method is basically up to the level even superior to that of the existing product under the same thickness, the whiteness is whiter than that of the existing product, the breaking strength and the impact toughness are superior to those of the existing product, the expansion coefficient is lower than that of the existing product, and the expansion coefficient of the existing product without stilbite crystal phase is higher.
Comparative example 1
The comparative example was performed under the same conditions as in example 1, except that the composition of the glass-ceramic sheet in step S2 was:
s2, mixing and ball-milling 70% of glass frit A, 15% of kaolin and 5% of polyacrylic resin serving as an adhesive additive C, 5% of polyvinyl acetate and 5% of polyethylene-vinyl acetate in percentage by mass, homogenizing slurry, spray-drying, and then carrying out dry-pressing forming to obtain the microcrystalline glass green body with the thickness of 10 mm.
Comparative example 2
The comparative example was performed under the same conditions as in example 1, except that the composition of the glass-ceramic sheet in step S2 was:
s2, mixing and ball-milling 75% of glass frit A, 22% of bentonite and 3% of adhesive additive C which is polyethylene-vinyl acetate, homogenizing slurry, spray-drying, and performing dry pressing to obtain a 10 mm-thick microcrystalline glass green body.
Comparative example 3
The comparative example was performed under the same conditions as in example 1 except that the microcrystalline glass sheet in step S2 was composed of:
s2, mixing and ball-milling 65% of glass frit A, 15% of kaolin, 5% of bentonite and 5% of bonding additive C which are polyacrylic resin, 5% of polyvinyl acetate and 5% of polyethylene-vinyl acetate, homogenizing slurry, spray-drying, and performing dry pressing to obtain the 10mm thick microcrystalline glass green body.
Comparative example 4
The comparative example was performed under the same conditions as in example 1, except that the composition of the glass-ceramic sheet in step S2 was:
s2, mixing and ball-milling 85% of glass frit A, 5% of kaolin, 5% of bentonite and 5% of adhesive additive C which is 5% of polyacrylic resin, homogenizing slurry, spray-drying, and then carrying out dry pressing forming to obtain a 10mm thick microcrystalline glass green body.
The components of the comparative examples are shown in the following table in percentage by mass:
the microcrystalline glass sheets of comparative examples 1 to 4 were subjected to performance tests, and the specific results of the performance tests and the effect comparison are shown in the following table:
from the above table, it can be seen that, under the condition of the same thickness, the light transmittance and the flexural strength of the glass plate are gradually increased along with the increase of the content of the stilbite crystal phase, the whiteness of the glass plate is the highest between 30% and 40% of the content of the stilbite crystal phase, the impact toughness of the glass plate is the highest between 40% and 50% of the content of the stilbite crystal phase, and by combining the data, the stilbite crystal phase content with the optimal comprehensive performance of the microcrystalline glass plate is 30% to 50%.
Comparative example 5
The comparative example was performed under the same conditions as in example 1, except that the composition of the glass-ceramic sheet in step S2 was:
s2, mixing and ball-milling 50% of glass frit A, 25% of kaolin, 20% of bentonite and 5% of polyvinyl acetate serving as an adhesive additive C according to mass percentage, homogenizing slurry, spray-drying, and then carrying out dry-pressing forming to obtain a 10 mm-thick microcrystalline glass green body.
Comparative example 6
The comparative example was performed under the same conditions as in example 1 except that the microcrystalline glass sheet in step S2 was composed of:
s2, mixing and ball-milling 90% of glass frit A, 5% of kaolin and 5% of adhesive additive C which is 5% of polyvinyl acetate, homogenizing slurry, spray-drying, and then carrying out dry pressing forming to obtain a 10mm thick microcrystalline glass green body.
Comparative example 7
The comparative example was performed under the same conditions as in example 1, except that the composition of the glass-ceramic sheet in step S2 was:
s2, mixing and ball-milling 70% of glass frit A, 15% of kaolin and 15% of bentonite according to mass percentage, homogenizing slurry, spray-drying, and then carrying out dry pressing forming to obtain a microcrystalline glass green body with the thickness of 10 mm.
Comparative example 8
The comparative example was performed under the same conditions as in example 1 except that the microcrystalline glass sheet in step S2 was composed of:
s2, mixing and ball-milling 70% of glass frit A and 30% of polyvinyl acetate as bonding additive C in percentage by mass, homogenizing slurry, spray-drying, and performing dry pressing to obtain a 10 mm-thick microcrystalline glass green body.
The microcrystalline glass sheets of comparative examples 5 to 8 were subjected to performance tests, wherein comparative example 6, comparative example 7 and comparative example 8 were not subjected to subsequent performance tests because they could not be press-formed or the green strength after forming did not reach 4 or more, and the results of the performance tests and the effect comparison of the other comparative examples are shown in the following table:
as can be seen from the above table, the content of the glass frit needs to be controlled in a reasonable range, and if the content of the glass frit is relatively low, the light transmittance and whiteness of the product are not sufficient, and the visual effect of the suet white jade cannot be generated, if the content of the glass frit is relatively high, the whole glass plate is not easy to mold, cracks are easily generated after molding, the breaking strength and the impact toughness of the product are relatively poor, and if the content of the glass frit is relatively low, the crystalline phase content of the final stilbite of the glass plate is not high, and the light transmittance, the whiteness, the breaking strength and the toughness of the product are relatively poor.
Comparative example 9
The conditions in this comparative example were the same as those in example 1 except that the change in the nucleation temperature in the firing in step S3 was changed to 400 ℃, specifically:
s3, firing;
s31, heating and draining: 3min at room temperature-400 ℃;
s32, constant-temperature nucleation: 40min,400 deg.C;
s33, temperature rising: 8min,400-920 ℃;
s34, constant temperature crystallization: 40min,920 ℃;
s35, quenching and annealing.
Comparative example 10
The conditions in this comparative example were the same as those in example 1 except for the change in the temperature of nucleation in the firing in step S3. Changing to 800 ℃, specifically:
s3, firing;
s31, heating and draining: 5min at room temperature of-800 ℃;
s32, constant-temperature nucleation: 40min,800 deg.C;
s33, temperature rising: 3min,800-920 ℃;
s34, constant temperature crystallization: 40min,920 ℃;
and S35, cooling and annealing.
Comparative example 11
The conditions in this comparative example were the same as those in example 1 except that the change in the nucleation time in the firing of step S3 was changed to 10min, specifically:
s3, firing;
s31, heating and draining: 5min, room temperature-620 ℃;
s32, constant-temperature nucleation: 10min,620 ℃;
s33, temperature rising: 5min,620-920 ℃;
s34, constant temperature crystallization: 40min,920 ℃;
and S35, cooling and annealing.
Comparative example 12
The conditions in this comparative example were the same as those in example 1 except that the change in the nucleation time in the firing in step S3 was changed to 70min, specifically:
s3, firing;
s31, heating and draining: 5min, room temperature-620 ℃;
s32, constant-temperature nucleation: 70min,620 ℃;
s33, temperature rising: 5min,620-920 ℃;
s34, constant temperature crystallization: 40min,920 ℃;
and S35, cooling and annealing.
Comparative example 13
The conditions in this comparative example are the same as those in example 1, except that the crystallization temperature in the step S3 is changed, and the crystallization temperature is 700 ℃, specifically:
s3, firing;
s31, heating and draining: 5min, room temperature-620 ℃;
s32, constant-temperature nucleation: 40min,620 deg.C;
s33, temperature rising: 5min,620-700 ℃;
s34, constant temperature crystallization: 40min,700 deg.C;
and S35, cooling and annealing.
Comparative example 14
The conditions in this comparative example are the same as those in example 1, except that the crystallization temperature in the step S3 is changed, and the crystallization temperature is 1100 ℃, specifically:
s3, firing;
s31, heating and draining: 5min, room temperature-620 ℃;
s32, constant-temperature nucleation: 40min,620 deg.C;
s33, temperature rising: 8min,620-1100 ℃;
s34, constant temperature crystallization: 40min,1100 deg.C;
and S35, cooling and annealing.
Comparative example 15
The conditions in this comparative example are the same as those in example 1, except that the crystallization time in the firing in step S3 is changed to 10min, specifically:
s3, firing;
s31, heating and draining: 5min, room temperature-620 ℃;
s32, constant-temperature nucleation: 40min,620 deg.C;
s33, temperature rise: 5min,620-920 ℃;
s34, constant-temperature crystallization: 10min,920 ℃;
and S35, cooling and annealing.
Comparative example 16
The conditions in this comparative example are the same as those in example 1, except that the crystallization time in the step S3 is changed, the crystallization temperature is 70min, specifically:
s3, firing;
s31, heating and draining: 5min, room temperature-620 ℃;
s32, constant-temperature nucleation: 40min,620 deg.C;
s33, temperature rising: 5min,620-920 ℃;
s34, constant temperature crystallization: 70min,920 ℃;
and S35, cooling and annealing.
When the microcrystalline glass plates of the above comparative examples 5 to 12 were subjected to the property test, the sintered crystallization temperature of comparative example 14 was too high, and thus the green body was completely melted into the glass phase, and the related properties could not be tested, and the specific property test and effect comparison results of the other comparative examples are shown in the following table:
as can be seen from the above table, the firing schedule of the microcrystalline glass plate is very important, especially when stilbite crystal forms need to be generated, the process needs to be performed at a certain nucleation temperature and time and a certain crystallization temperature and time, the content of the crystal phase of the last stilbite cannot be well generated if the nucleation temperature is low or the nucleation time is short, or if the crystallization temperature is low or the crystallization time is short, the content of the crystal phase of the stilbite is slightly increased but not significantly increased if the nucleation temperature is too high or the crystallization temperature is too high, and therefore, the time can be controlled within a certain range from the viewpoint of energy saving.
The above description is only a preferred embodiment of the present application, and not intended to limit the scope of the present application, and all modifications and equivalents of the subject matter of the present application, which are made by the following claims and their equivalents, or which are directly or indirectly applicable to other related arts, are intended to be included within the scope of the present application.
Claims (8)
1. A glass-ceramic plate, characterized in thatThe microcrystalline glass plate comprises the following crystalline phases in percentage by mass: naCa 2 Si 4 O 10 F30-50%; calcium fluoride CaF 2 1 to 10 percent; bulk stevensite Mg 3 SiO 4 F 2 0.5 to 5 percent; kaliophilite KAlSiO 4 0.5-5%；
The preparation method of the microcrystalline glass plate comprises the following steps:
s1, preparing a glass frit A by adopting a fusion method;
s2, uniformly mixing 65-85% of the glass frit A, 10-27% of clay B and 3-15% of bonding additive C by mass percent, homogenizing, and performing dry pressing forming to obtain a microcrystalline glass green body;
s3, firing;
s4, polishing to obtain the microcrystalline glass plate;
the glass frit A contains 8-15% of CaO and Na in percentage by weight of chemical oxides 2 O 3-7%，SiO 2 60-72%，F 3-7%；
The sintering is carried out at the temperature of 600-630 ℃ for 30-50min, and at the temperature of 880-1000 ℃ for 30-50min.
2. The glass-ceramic plate according to claim 1, wherein the glass frit A comprises the following components in percentage by weight in terms of chemical oxides: siO 2 2 60-72%，Al 2 O 3 1.5~6%，CaO 8-15%，K 2 O 3-7%， Na 2 O 3-7%，MgO 0-1%，F 3-7%，CeO 2 0-1%，Fe 2 O 3 0-0.1%。
3. A crystallized glass sheet according to claim 2, wherein the clay B is: more than one of bentonite and kaolin.
4. The crystallized glass sheet according to claim 2, wherein the bonding additive C is: more than one of polyacrylic resin, polyvinyl acetate and polyethylene-vinyl acetate.
5. A glass-ceramic sheet according to any one of claims 2-4, characterized in that the following steps are included between step S2 and step S3;
s2-1, applying a layer of ground coat on the microcrystalline glass green body obtained in the step S2;
s2-2, decorating the microcrystalline glass green body obtained in the step S2-1;
s2-3, applying a layer of transparent dry particles on the microcrystalline glass green body obtained in the step S2-2.
6. The microcrystalline glass sheet according to claim 5, wherein the ground coat comprises the following chemical components in percentage by mass: siO 2 2 55-65%，Al 2 O 3 4-9%，B 2 O 3 0.5-2%，CaO 13-22%，ZnO 1-5%，BaO 2-8%，K 2 O 1-5%，Na 2 O 3-7%。
7. The glass-ceramic plate according to claim 5, wherein the chemical composition of the transparent dry particles is, in mass percent: siO 2 2 35-48%，Al 2 O 3 11-14%，B 2 O 3 18-22%，CaO 7-10%，ZnO 0.5-1.5%，BaO 5-7%，K 2 O 3-5%，Na 2 O 3-5%，Li 2 O 1-3%。
8. The microcrystalline glass sheet according to claim 5, wherein the transparent dry pellets have a cloth thickness of 500-1500g/m 2 。
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| CN104176938A (en) * | 2014-09-01 | 2014-12-03 | 九江金凤凰装饰材料有限公司 | Microcrystal glass plate taking agrellite as main crystal phase and production method of microcrystal glass plate |
| CN111908797A (en) * | 2020-07-28 | 2020-11-10 | 电子科技大学 | Low-thermal-expansion cordierite-based microcrystalline glass material and preparation method thereof |
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| CN104176938A (en) * | 2014-09-01 | 2014-12-03 | 九江金凤凰装饰材料有限公司 | Microcrystal glass plate taking agrellite as main crystal phase and production method of microcrystal glass plate |
| CN111908797A (en) * | 2020-07-28 | 2020-11-10 | 电子科技大学 | Low-thermal-expansion cordierite-based microcrystalline glass material and preparation method thereof |
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