CN117263522A - High-transparency high-fracture-toughness complex-phase alkaline earth aluminosilicate transparent glass ceramic and preparation method thereof - Google Patents
High-transparency high-fracture-toughness complex-phase alkaline earth aluminosilicate transparent glass ceramic and preparation method thereof Download PDFInfo
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- CN117263522A CN117263522A CN202311091835.8A CN202311091835A CN117263522A CN 117263522 A CN117263522 A CN 117263522A CN 202311091835 A CN202311091835 A CN 202311091835A CN 117263522 A CN117263522 A CN 117263522A
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- 229910000323 aluminium silicate Inorganic materials 0.000 title claims abstract description 18
- HNPSIPDUKPIQMN-UHFFFAOYSA-N dioxosilane;oxo(oxoalumanyloxy)alumane Chemical compound O=[Si]=O.O=[Al]O[Al]=O HNPSIPDUKPIQMN-UHFFFAOYSA-N 0.000 title claims abstract description 18
- 239000002241 glass-ceramic Substances 0.000 title claims abstract description 16
- 238000002360 preparation method Methods 0.000 title claims abstract description 12
- 239000011521 glass Substances 0.000 claims abstract description 29
- 238000002425 crystallisation Methods 0.000 claims abstract description 16
- 230000008025 crystallization Effects 0.000 claims abstract description 15
- 238000002844 melting Methods 0.000 claims abstract description 8
- 230000008018 melting Effects 0.000 claims abstract description 8
- 239000000919 ceramic Substances 0.000 claims description 36
- 238000000498 ball milling Methods 0.000 claims description 20
- 239000000843 powder Substances 0.000 claims description 15
- 238000010438 heat treatment Methods 0.000 claims description 14
- 238000000034 method Methods 0.000 claims description 12
- 238000000137 annealing Methods 0.000 claims description 11
- 239000006064 precursor glass Substances 0.000 claims description 11
- 239000002994 raw material Substances 0.000 claims description 10
- 238000001035 drying Methods 0.000 claims description 9
- 239000011268 mixed slurry Substances 0.000 claims description 9
- 239000007788 liquid Substances 0.000 claims description 7
- 238000001816 cooling Methods 0.000 claims description 6
- 229910018072 Al 2 O 3 Inorganic materials 0.000 claims description 5
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 5
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims description 5
- 229910004298 SiO 2 Inorganic materials 0.000 claims description 5
- 229910052802 copper Inorganic materials 0.000 claims description 5
- 239000010949 copper Substances 0.000 claims description 5
- 229910010413 TiO 2 Inorganic materials 0.000 claims description 4
- 230000006698 induction Effects 0.000 claims description 4
- 238000004519 manufacturing process Methods 0.000 claims description 4
- 239000002667 nucleating agent Substances 0.000 claims description 4
- 238000004321 preservation Methods 0.000 claims description 2
- 238000005303 weighing Methods 0.000 claims description 2
- 239000013078 crystal Substances 0.000 abstract description 14
- 229910003668 SrAl Inorganic materials 0.000 abstract description 8
- 230000009286 beneficial effect Effects 0.000 abstract description 5
- 230000015572 biosynthetic process Effects 0.000 abstract description 4
- 230000003287 optical effect Effects 0.000 abstract description 4
- 239000000463 material Substances 0.000 abstract description 3
- 239000000126 substance Substances 0.000 abstract description 3
- 239000000203 mixture Substances 0.000 abstract 1
- 238000002834 transmittance Methods 0.000 description 10
- 239000002002 slurry Substances 0.000 description 4
- 229910010293 ceramic material Inorganic materials 0.000 description 3
- 239000006060 molten glass Substances 0.000 description 3
- 238000001878 scanning electron micrograph Methods 0.000 description 3
- 238000005245 sintering Methods 0.000 description 3
- PNEYBMLMFCGWSK-UHFFFAOYSA-N Alumina Chemical compound [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000000879 optical micrograph Methods 0.000 description 2
- 238000010521 absorption reaction Methods 0.000 description 1
- 230000004913 activation Effects 0.000 description 1
- 238000000149 argon plasma sintering Methods 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000008033 biological extinction Effects 0.000 description 1
- 238000005467 ceramic manufacturing process Methods 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 239000008395 clarifying agent Substances 0.000 description 1
- 238000004891 communication Methods 0.000 description 1
- 230000007123 defense Effects 0.000 description 1
- 238000000280 densification Methods 0.000 description 1
- 238000001514 detection method Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000007496 glass forming Methods 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 238000005286 illumination Methods 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 238000007373 indentation Methods 0.000 description 1
- 238000011068 loading method Methods 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 239000011858 nanopowder Substances 0.000 description 1
- 238000013001 point bending Methods 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- 238000007493 shaping process Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 238000003786 synthesis reaction Methods 0.000 description 1
Classifications
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
- C03B19/00—Other methods of shaping glass
- C03B19/02—Other methods of shaping glass by casting molten glass, e.g. injection moulding
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
- C03B25/00—Annealing glass products
-
- 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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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Organic Chemistry (AREA)
- Crystallography & Structural Chemistry (AREA)
- Ceramic Engineering (AREA)
- Life Sciences & Earth Sciences (AREA)
- Chemical Kinetics & Catalysis (AREA)
- General Chemical & Material Sciences (AREA)
- Geochemistry & Mineralogy (AREA)
- Dispersion Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Glass Compositions (AREA)
Abstract
The invention discloses a high-transparency high-fracture-toughness complex-phase alkaline earth aluminosilicate transparent glass ceramic and a preparation method thereof. Using glass crystallization methods, a controlled degree of chemical disorder is used in the structure to achieve micron length scale optical isotropy, caAl 2 Si 2 O 8 The crystal form is a rod-shaped structure, which is beneficial to increasing the crack resistance toughness of the material and can inhibit SrAl 2 Si 2 O 8 And (5) grain growth. CaAl (CaAl) 2 Si 2 O 8 The grains can effectively inhibit SrAl 2 Si 2 O 8 The grain size is 0.1-30 mu m, the composition between crystal phases is compactThe addition of the crystal nucleus agent can effectively reduce the melting temperature and the crystallization temperature of the glass, is beneficial to the formation of crystalline phases and can improve the stability of the glass.
Description
Technical Field
The invention relates to the technical field of ceramic material preparation, in particular to a high-transparency high-fracture-toughness complex phase alkaline earth aluminosilicate transparent glass ceramic and a preparation method thereof.
Background
The transparent ceramic is a polycrystalline material which allows incident photons to pass through without obvious absorption and internal scattering, and has wide application prospect in the fields of illumination, transparent armor, medical treatment, communication, infrared detection, space science, national defense and the like. Conventional ceramic materials are generally opaque due to their potential extinction factors such as anisotropy, low symmetry crystal structure, grain boundaries, pores, and impurities. Currently, classical transparent ceramic manufacturing processes generally follow the same technical route, with basic steps including powder preparation, shaping, sintering, annealing, grinding and polishing. Most transparent ceramic solid state fabrication techniques are considered expensive because they often involve high purity, high dispersibility, high sintering activity nanopowder synthesis techniques and long-period high temperature high pressure densification sintering techniques.
Disclosure of Invention
The invention aims to provide a preparation method of high-transparency high-fracture-toughness complex-phase alkaline earth aluminosilicate transparent glass ceramic.
It is another object of the present invention to provide a high transparent high fracture toughness complex phase alkaline earth aluminosilicate transparent glass ceramic made by the above-described method.
In order to achieve the above purpose, the technical scheme adopted by the invention is as follows:
in one aspect, the invention provides a method for preparing a high-transparency high-fracture-toughness complex-phase alkaline earth aluminosilicate transparent glass ceramic, comprising the following steps:
(1) Weighing glass powder raw materials, placing the glass powder raw materials into a ball milling tank, adding absolute ethyl alcohol, ball milling to obtain mixed slurry, drying the mixed slurry, and placing the dried powder into a 1450-1850 ℃ and preserving heat for 30-120 min to melt to obtain glass liquid; wherein the glass powder raw material consists of the following components in percentage by mole: srCO 3 20～40％、CaCO 3 3～10％、SiO 2 30～50％、Al 2 O 3 15 to 45 percent, 2 to 10 percent of nucleating agent and Sb 2 O 3 0.03% of a nucleating agent selected from the group consisting of P 2 O 5 、ZrO 2 、TiO 2 One or more of the following;
(2) Pouring the glass liquid into a copper mold to obtain a transparent glass block;
(3) Annealing the glass block at 600-800 ℃ for 10-60 h to obtain precursor glass;
(4) And (3) sequentially placing the precursor glass at a crystallization temperature of 700-850 ℃ and 900-1050 ℃ for heat preservation for 1-10 hours, cooling to room temperature, taking out, and thus obtaining the multiphase transparent ceramic, and annealing in air.
Preferably, the ball milling rotating speed in the step (1) is 160-210 r/min, and the ball milling time is 10-20 h.
Preferably, the drying temperature of the mixed slurry in the step (1) is 70 ℃ and the drying time is 6-12 h.
Preferably, in the step (1), the induction melting furnace is used for heating, and the heating rate is 5-20 ℃/min.
Preferably, in the step (4), the temperature is kept at 700-850 ℃ for 0.5-1.5 h, then the temperature is raised to 900-1050 ℃ and the temperature is kept for 1-10 h.
Preferably, in the step (4), the multiphase transparent ceramic is air annealed at 650-850 ℃ for 15h.
On the other hand, the invention also provides the high-transparency high-fracture-toughness complex-phase alkaline earth aluminosilicate transparent glass ceramic prepared by the preparation method.
The complex phase alkaline earth aluminosilicate transparent glass ceramic consists of a plurality of crystal phases, wherein the main crystal phase is SrAl 2 Si 2 O 8 、CaAl 2 Si 2 O 8 . Using a controlled degree of chemical disorder in a structure to achieve optical isotropy of the micrometer length scale, srAl 2 Si 2 O 8 The crystallization activation energy is low, the high transparent ceramic is easy to obtain after the glass is crystallized, and CaAl 2 Si 2 O 8 The crystal form is a rod-shaped structure, which is beneficial to increasing the crack resistance toughness of the material and can inhibit SrAl 2 Si 2 O 8 And (5) grain growth. CaAl (CaAl) 2 Si 2 O 8 The grains can effectively inhibit SrAl 2 Si 2 O 8 The crystal grains grow up, the grain boundaries are thinner, the grain size is 1-30 mu m, a compact structure is formed between crystal phases, and P 2 O 5 、ZrO 2 、TiO 2 The addition of the crystal nucleus agent can effectively reduce the melting temperature and the crystallization temperature of the glass, is beneficial to the formation of crystalline phases, can improve the stability of the glass, and additionally introduces Sb 2 O 3 As a clarifying agent.
The average grain size of the ceramic prepared by the invention is 0.1-30 mu m, the visible light transmittance of the ceramic can reach more than 88 percent, and the fracture toughness can reach 2-10 MPa.m 1/2 。
Compared with the prior art, the invention has the following beneficial effects:
(1) The transparent ceramic prepared by the invention realizes controllable crystallization by controlling the crystallization time and temperature in a two-step crystallization mode, and preferentially generates CaAl 2 Si 2 O 8 Crystalline phase, free of SrAl 2 Si 2 O 8 The primary crystal phase causes light scattering;
(2) The preparation method of the ceramic provided by the invention generates CaAl 2 Si 2 O 8 The crystalline phase limits SrAl by pinning effect 2 Si 2 O 8 The growth of the crystal grains is effectively controlled, and the crystal grains areThe size is uniform, the chemical disorder of a controlled degree is used in the structure to obtain the optical isotropy of the micrometer length scale, the optical quality and the transmittance are good, and the transmittance of the ceramic at 800nm is 90.1%;
(3) The preparation method of the ceramic provided by the invention adopts a melting method to further control the growth of ceramic grains, and the prepared ceramic grains have smaller size and generate SrAl 2 Si 2 O 8 The crystal phase is in a rod-shaped structure, so that the mechanical property of the transparent ceramic is effectively improved;
(4) Based on mature glass forming technology, the transparent ceramic can be obtained after the precursor glass is subjected to heat treatment, the process is simple and efficient, the crystallinity is high, and the preparation of the large-size transparent ceramic can be realized by the method.
Drawings
FIG. 1 is a graph showing the transmittance of transparent ceramics according to example 1 of the present invention;
FIG. 2 is an optical micrograph of the heterogeneous transparent ceramic prepared in example 1 after crystallization at 800 ℃.
FIG. 3 is an optical micrograph of the heterogeneous transparent ceramic prepared in example 1 after crystallization at 1020 ℃;
FIG. 4 is a schematic diagram of the heterogeneous transparent ceramics prepared in examples 1 to 3 according to the present invention.
Detailed Description
The invention will be described in further detail with reference to the drawings and the specific examples.
The raw material powders used in the following examples were all commercially available and had purities of more than 99.9%.
(1) The following raw materials are weighed according to the following mole percentage: 24% SrCO 3 、27％Al 2 O 3 、43.5％SiO 2 、3％CaCO 3 2.47% P 2 O 5 、2％ZrO 2 And 0.03% Sb 2 O 3 Placing the powder in a ball milling tank, adding 70mL of absolute ethyl alcohol to prepare slurry, adopting planetary ball milling at the ball milling rotating speed of 200r/min for 16h, and drying the mixed slurry after ball milling.
(2) Pouring the powder prepared in the step (1) into a crucible, heating the crucible from room temperature to 1200 ℃ at 10 ℃/min by using an induction melting furnace, preserving heat for 1h, heating the crucible to 1760 ℃ at 5 ℃/min, and preserving heat for 1h to obtain molten glass;
(3) Pouring the glass liquid into a copper plate mould preheated at 600 ℃, wherein the mould is phi 22 mm in size and is cooled along with a preheating platform at a cooling rate of 10 ℃/min, so as to obtain a transparent glass block;
(4) Annealing the glass block at 700 ℃ for 30 hours to obtain precursor glass;
(5) And (3) placing the precursor glass at a crystallization temperature of 800 ℃ for 0.5h, then heating to 1020 ℃, preserving heat for 4h, cooling to room temperature, and taking out to obtain the multiphase transparent ceramic, and carrying out air annealing at 750 ℃ for 15h.
FIG. 1 is a graph showing the transmittance of the transparent alumina ceramic prepared in this example, wherein the transmittance of the prepared ceramic at 800nm is 90.1%, indicating that the ceramic has high transmittance.
FIG. 2 shows the formation of CaAl by crystallization of the complex phase alkaline earth aluminosilicate transparent ceramic prepared in this example at 800 DEG C 2 Si 2 O 8 SEM of the phase, it can be seen that CaAl 2 Si 2 O 8 The phase grows into a long strip shape, and the grain size is very small.
Fig. 3 is an SEM image of crystallization of the complex phase alkaline earth aluminosilicate transparent ceramic prepared in this example at 1020 ℃, and it can be seen that the two phases are densely grown and the ceramic has excellent mechanical properties.
Fig. 4 is a physical view of the alumina transparent ceramic prepared in this example, and the ceramic sample has excellent light transmittance, and the image under the ceramic can be clearly seen.
Example 2
(1) The following raw materials are weighed according to the following mole percentage: 21.5% SrCO 3 、26.5％ Al 2 O 3 、42.5％SiO 2 、5％CaCO 3 2.47% P 2 O 5 、2％ZrO 2 And 0.03% Sb 2 O 3 Placing the powder in a ball milling tank, adding 70mL of absolute ethyl alcohol to prepare slurry, adopting planetary ball milling at a ball milling rotating speed of 180r/min for 15h, and drying the mixed slurry after ball milling.
(2) Pouring the slurry prepared in the step (1) into a crucible, heating the crucible to 1600 ℃ from room temperature at 10 ℃/min, preserving heat for 0.5h, heating the crucible to 1750 ℃ at 5 ℃/min, and preserving heat for 1.5h to obtain molten glass;
(3) Pouring the glass liquid into a copper plate mould preheated at 580 ℃, wherein the mould is phi 22 mm in size and is cooled along with a preheating platform to obtain transparent glass blocks;
(4) Annealing the glass block at 800 ℃ for 15 hours to obtain precursor glass;
(5) And (3) placing the precursor glass at a crystallization temperature of 820 ℃ for 0.5h, then heating to 1130 ℃, preserving heat for 2.5h, cooling to room temperature, taking out, and obtaining the multiphase transparent ceramic, and carrying out air annealing at 850 ℃ for 15h.
The SEM image, transmittance curve and physical image of the complex phase transparent ceramic surface prepared in this example are similar to those of example 1.
Example 3
(1) The following raw materials are weighed according to the following mole percentage: 26% SrCO 3 、26％ Al 2 O 3 、41.5％SiO 2 、4％CaCO 3 2.47% P 2 O 5 、2％ZrO 2 、2％TiO 2 And 0.03% Sb 2 O 3 Placing the powder in a ball milling tank, adding 70mL of absolute ethyl alcohol to prepare slurry, adopting planetary ball milling at a ball milling rotating speed of 180r/min for 16h, and drying the mixed slurry after ball milling.
(2) Pouring the powder prepared in the step (1) into a crucible, heating the crucible from room temperature to 1700 ℃ at 15 ℃/min by using an induction melting furnace, preserving heat for 1h, heating the crucible to a melting temperature of 1760 ℃ at 5 ℃/min, and preserving heat for 1h to obtain molten glass;
(3) Pouring the glass liquid into a copper plate mould preheated at 580 ℃, wherein the mould is phi 22 mm in size and is cooled along with a preheating platform to obtain transparent glass blocks;
(4) Annealing the glass block at 720 ℃ for 15 hours to obtain precursor glass;
(5) And (3) placing the precursor glass at a crystallization temperature of 800 ℃ for 0.5h, then heating to 1010 ℃, preserving heat for 3h, cooling to room temperature, and taking out to obtain the multiphase transparent ceramic, and carrying out air annealing at 800 ℃ for 15h.
The SEM image, transmittance curve and physical image of the complex phase transparent ceramic surface prepared in this example are similar to those of example 1.
The ceramic samples of examples 1, 2 and 3 were tested for vickers hardness and flexural strength, and fracture toughness was measured by indentation, and the data are shown in table 1.
Measuring the bending strength of the sample by using a WDW-200 electronic universal tester in a three-point bending mode, wherein the loading speed is 0.5mm/min; the span is 16mm, the fracture toughness of the sample is measured by adopting a single-side notched beam (SENB) method on the same equipment,
TABLE 1 mechanical Properties of ceramic materials
| Example 1 | Example 2 | Example 3 | |
| Vickers hardness (GPa) | 12.4 | 11.9 | 12.1 |
| Flexural Strength (MPa) | 538 | 552±18 | 530±15 |
| Fracture toughness (MPa.m) 1/2 ) | 8.9 | 9.5 | 9.1 |
The foregoing is merely illustrative of specific embodiments of the present invention, and the scope of the invention is not limited thereto, but any modifications, equivalents, improvements and alternatives falling within the spirit and principles of the present invention will be apparent to those skilled in the art within the scope of the present invention.
Claims (7)
1. The preparation method of the high-transparency high-fracture-toughness complex-phase alkaline earth aluminosilicate transparent glass ceramic is characterized by comprising the following steps of:
(1) Weighing glass powder raw materials, placing the glass powder raw materials into a ball milling tank, adding absolute ethyl alcohol, ball milling to obtain mixed slurry, drying the mixed slurry, and placing the dried powder into a 1450-1850 ℃ and preserving heat for 30-120 min to melt to obtain glass liquid; wherein the glass powder raw material consists of the following components in percentage by mole: srCO 3 20～40％、CaCO 3 3～10％、SiO 2 30～50％、Al 2 O 3 15 to 45 percent, 2 to 10 percent of nucleating agent and Sb 2 O 3 0.03% of a nucleating agent selected from the group consisting of P 2 O 5 、ZrO 2 、TiO 2 One or more of the following;
(2) Pouring the glass liquid into a copper mold to obtain a transparent glass block;
(3) Annealing the glass block at 600-800 ℃ for 10-60 h to obtain precursor glass;
(4) And (3) sequentially placing the precursor glass at the crystallization temperature of 700-850 ℃ and 900-1050 ℃ for heat preservation for 1-10 h, cooling to room temperature, taking out, and thus obtaining the multiphase transparent ceramic, and annealing in air.
2. The method for preparing the high-transparency high-fracture-toughness complex-phase alkaline earth aluminosilicate transparent glass ceramic according to claim 1, wherein the ball milling rotation speed in the step (1) is 160-210 r/min, and the ball milling time is 10-20 h.
3. The method for preparing high-transparency high-fracture-toughness complex-phase alkaline earth aluminosilicate transparent glass ceramic according to claim 1, wherein the drying temperature of the mixed slurry in step (1) is 70 ℃ and the drying time is 6-12 h.
4. The method for producing a high-transparency high-fracture-toughness complex-phase alkaline earth aluminosilicate transparent glass ceramic according to claim 1, wherein in step (1), an induction melting furnace is used for heating, and the heating rate is 5 to 20 ℃/min.
5. The method for preparing a high-transparency high-fracture-toughness complex-phase alkaline earth aluminosilicate transparent glass ceramic according to claim 1, wherein in the step (4), the temperature is kept at 700-850 ℃ for 0.5-1.5 h, and then the temperature is raised to 900-1050 ℃ and kept for 1-10 h.
6. The method for producing a high-transparency high-fracture-toughness complex-phase alkaline earth aluminosilicate transparent glass ceramic according to claim 1, wherein in step (4), the multi-phase transparent ceramic is air-annealed at 650 to 850 ℃ for 15 hours.
7. A high transparent high fracture toughness complex phase alkaline earth aluminosilicate transparent glass ceramic produced by the production process of any one of claims 1 to 6.
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| CN202311091835.8A CN117263522A (en) | 2023-08-26 | 2023-08-26 | High-transparency high-fracture-toughness complex-phase alkaline earth aluminosilicate transparent glass ceramic and preparation method thereof |
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| CN202311091835.8A CN117263522A (en) | 2023-08-26 | 2023-08-26 | High-transparency high-fracture-toughness complex-phase alkaline earth aluminosilicate transparent glass ceramic and preparation method thereof |
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| CB03 | Change of inventor or designer information | ||
| CB03 | Change of inventor or designer information |
Inventor after: Zhang Le Inventor after: Chen Hao Inventor after: Chen Xu Inventor after: Zhou Chunming Inventor after: Zhou Tianyuan Inventor after: Chen Hang Inventor after: Wang Peng Inventor after: Zhou Zihan Inventor after: Zheng Xinyu Inventor after: Kang Jian Inventor before: Zhou Chunming Inventor before: Chen Hao Inventor before: Chen Xu Inventor before: Zhang Le Inventor before: Zhou Tianyuan Inventor before: Chen Hang Inventor before: Wang Peng Inventor before: Zhou Zihan Inventor before: Zheng Xinyu Inventor before: Kang Jian |