CN109721250B - Method for preparing luminescent glass ceramic by using low-melting-point glass powder - Google Patents
Method for preparing luminescent glass ceramic by using low-melting-point glass powder Download PDFInfo
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- 239000011521 glass Substances 0.000 title claims abstract description 104
- 239000000843 powder Substances 0.000 title claims abstract description 82
- 239000002241 glass-ceramic Substances 0.000 title claims abstract description 38
- 238000000034 method Methods 0.000 title claims abstract description 16
- 238000002844 melting Methods 0.000 claims abstract description 36
- 230000007704 transition Effects 0.000 claims abstract description 31
- 230000008018 melting Effects 0.000 claims abstract description 28
- 239000007788 liquid Substances 0.000 claims abstract description 11
- 238000002156 mixing Methods 0.000 claims abstract description 11
- 239000003814 drug Substances 0.000 claims abstract description 8
- 239000002994 raw material Substances 0.000 claims abstract description 8
- 229940079593 drug Drugs 0.000 claims abstract description 5
- 238000010791 quenching Methods 0.000 claims abstract description 5
- 230000000171 quenching effect Effects 0.000 claims abstract description 5
- 239000002419 bulk glass Substances 0.000 claims abstract description 4
- 238000001816 cooling Methods 0.000 claims abstract description 4
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 claims description 20
- 229910052681 coesite Inorganic materials 0.000 claims description 14
- 229910052906 cristobalite Inorganic materials 0.000 claims description 14
- 239000000377 silicon dioxide Substances 0.000 claims description 14
- 229910052682 stishovite Inorganic materials 0.000 claims description 14
- 229910052905 tridymite Inorganic materials 0.000 claims description 14
- 238000000498 ball milling Methods 0.000 claims description 13
- WMWLMWRWZQELOS-UHFFFAOYSA-N bismuth(iii) oxide Chemical compound O=[Bi]O[Bi]=O WMWLMWRWZQELOS-UHFFFAOYSA-N 0.000 claims description 13
- 238000001354 calcination Methods 0.000 claims description 12
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims description 6
- MCMNRKCIXSYSNV-UHFFFAOYSA-N ZrO2 Inorganic materials O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 claims description 6
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 claims description 6
- 229910052593 corundum Inorganic materials 0.000 claims description 6
- 238000002360 preparation method Methods 0.000 claims description 6
- 229910001845 yogo sapphire Inorganic materials 0.000 claims description 6
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims description 4
- ADCOVFLJGNWWNZ-UHFFFAOYSA-N antimony trioxide Inorganic materials O=[Sb]O[Sb]=O ADCOVFLJGNWWNZ-UHFFFAOYSA-N 0.000 claims description 4
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 3
- 229910052802 copper Inorganic materials 0.000 claims description 3
- 239000010949 copper Substances 0.000 claims description 3
- 239000000203 mixture Substances 0.000 claims description 3
- GHPGOEFPKIHBNM-UHFFFAOYSA-N antimony(3+);oxygen(2-) Chemical compound [O-2].[O-2].[O-2].[Sb+3].[Sb+3] GHPGOEFPKIHBNM-UHFFFAOYSA-N 0.000 claims description 2
- 239000002245 particle Substances 0.000 claims description 2
- CPLXHLVBOLITMK-UHFFFAOYSA-N magnesium oxide Inorganic materials [Mg]=O CPLXHLVBOLITMK-UHFFFAOYSA-N 0.000 claims 3
- XLOMVQKBTHCTTD-UHFFFAOYSA-N zinc oxide Inorganic materials [Zn]=O XLOMVQKBTHCTTD-UHFFFAOYSA-N 0.000 claims 3
- 238000005286 illumination Methods 0.000 abstract description 8
- 238000004519 manufacturing process Methods 0.000 abstract description 8
- 238000004806 packaging method and process Methods 0.000 abstract description 5
- 239000005394 sealing glass Substances 0.000 abstract description 5
- 239000000463 material Substances 0.000 abstract description 4
- 230000015556 catabolic process Effects 0.000 abstract description 3
- 238000006731 degradation reaction Methods 0.000 abstract description 3
- 230000005284 excitation Effects 0.000 description 8
- 238000005245 sintering Methods 0.000 description 7
- 238000000295 emission spectrum Methods 0.000 description 6
- 238000003825 pressing Methods 0.000 description 4
- 239000000126 substance Substances 0.000 description 4
- 229910019142 PO4 Inorganic materials 0.000 description 3
- 239000011368 organic material Substances 0.000 description 3
- NBIIXXVUZAFLBC-UHFFFAOYSA-K phosphate Chemical compound [O-]P([O-])([O-])=O NBIIXXVUZAFLBC-UHFFFAOYSA-K 0.000 description 3
- 239000010452 phosphate Substances 0.000 description 3
- YUOWTJMRMWQJDA-UHFFFAOYSA-J tin(iv) fluoride Chemical compound [F-].[F-].[F-].[F-].[Sn+4] YUOWTJMRMWQJDA-UHFFFAOYSA-J 0.000 description 3
- 239000012876 carrier material Substances 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 230000009477 glass transition Effects 0.000 description 2
- 230000003287 optical effect Effects 0.000 description 2
- 229910002059 quaternary alloy Inorganic materials 0.000 description 2
- 238000007789 sealing Methods 0.000 description 2
- 230000001360 synchronised effect Effects 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 108010043121 Green Fluorescent Proteins Proteins 0.000 description 1
- 241000282414 Homo sapiens Species 0.000 description 1
- 229910020617 PbO—B2O3—SiO2 Inorganic materials 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
- LFVGISIMTYGQHF-UHFFFAOYSA-N ammonium dihydrogen phosphate Chemical compound [NH4+].OP(O)([O-])=O LFVGISIMTYGQHF-UHFFFAOYSA-N 0.000 description 1
- UNTBPXHCXVWYOI-UHFFFAOYSA-O azanium;oxido(dioxo)vanadium Chemical compound [NH4+].[O-][V](=O)=O UNTBPXHCXVWYOI-UHFFFAOYSA-O 0.000 description 1
- KGBXLFKZBHKPEV-UHFFFAOYSA-N boric acid Chemical compound OB(O)O KGBXLFKZBHKPEV-UHFFFAOYSA-N 0.000 description 1
- 239000004327 boric acid Substances 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 230000003750 conditioning effect Effects 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 239000003822 epoxy resin Substances 0.000 description 1
- 238000000695 excitation spectrum Methods 0.000 description 1
- 239000000891 luminescent agent Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 239000006060 molten glass Substances 0.000 description 1
- 239000005416 organic matter Substances 0.000 description 1
- 239000012994 photoredox catalyst Substances 0.000 description 1
- 229920003229 poly(methyl methacrylate) Polymers 0.000 description 1
- 239000004417 polycarbonate Substances 0.000 description 1
- 229920000647 polyepoxide Polymers 0.000 description 1
- 239000004926 polymethyl methacrylate Substances 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 239000011347 resin Substances 0.000 description 1
- 229920005989 resin Polymers 0.000 description 1
- ANOBYBYXJXCGBS-UHFFFAOYSA-L stannous fluoride Chemical compound F[Sn]F ANOBYBYXJXCGBS-UHFFFAOYSA-L 0.000 description 1
- 229960002799 stannous fluoride Drugs 0.000 description 1
Images
Classifications
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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
- C03C12/00—Powdered glass; Bead compositions
-
- 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
-
- 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
-
- 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
- C03C4/00—Compositions for glass with special properties
- C03C4/12—Compositions for glass with special properties for luminescent glass; for fluorescent glass
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F21—LIGHTING
- F21K—NON-ELECTRIC LIGHT SOURCES USING LUMINESCENCE; LIGHT SOURCES USING ELECTROCHEMILUMINESCENCE; LIGHT SOURCES USING CHARGES OF COMBUSTIBLE MATERIAL; LIGHT SOURCES USING SEMICONDUCTOR DEVICES AS LIGHT-GENERATING ELEMENTS; LIGHT SOURCES NOT OTHERWISE PROVIDED FOR
- F21K9/00—Light sources using semiconductor devices as light-generating elements, e.g. using light-emitting diodes [LED] or lasers
- F21K9/90—Methods of manufacture
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F21—LIGHTING
- F21V—FUNCTIONAL FEATURES OR DETAILS OF LIGHTING DEVICES OR SYSTEMS THEREOF; STRUCTURAL COMBINATIONS OF LIGHTING DEVICES WITH OTHER ARTICLES, NOT OTHERWISE PROVIDED FOR
- F21V19/00—Fastening of light sources or lamp holders
- F21V19/001—Fastening of light sources or lamp holders the light sources being semiconductors devices, e.g. LEDs
- F21V19/0015—Fastening arrangements intended to retain light sources
- F21V19/002—Fastening arrangements intended to retain light sources the fastening means engaging the encapsulation or the packaging of the semiconductor device
Abstract
The invention discloses a method for preparing luminescent glass ceramic by using low-melting-point glass powder, which comprises the steps of uniformly mixing raw material medicines, melting for 15-90 minutes at 300-700 ℃ to obtain glass liquid; quenching the glass liquid at the temperature of 300-700 ℃, and naturally cooling to room temperature to obtain bulk glass; the low-melting-point glass powder has a low glass phase transition temperature, and the glass phase transition temperature of the low-melting-point glass powder can be adjusted within a range of 200-500 ℃, so that the low-melting-point glass powder is suitable for manufacturing sealing glass and vacuum components and packaging LEDs, is particularly suitable for manufacturing luminescent glass ceramics with fluorescent powder materials, and is particularly suitable for laser illumination. The glass ceramic is molded and sintered at a lower temperature, so that the thermal degradation of the fluorescent powder at a high temperature can be effectively avoided, and the glass ceramic has an important application value in the field of laser illumination.
Description
The present application is a divisional application of "low melting point glass powder and glass ceramic for laser lighting produced by the same" as a parent application, wherein the application number of the parent application is 2016110912313, and the application date is 2016, 12, and 01.
Technical Field
The invention belongs to the technical field of special glass production and manufacturing, and particularly relates to a method for preparing luminescent glass ceramic by using low-melting-point glass powder.
Background
The low-melting glass is special glass with a glass transition temperature remarkably lower than that of common glass, and can be widely used as a bonding phase in sealing glass and electronic paste. With the rapid development of the electronic industry, low melting point glass is widely used for sealing and protecting electronic components and display devices, such as vacuum fluorescent display panels (VFDs), Plasma Display Panels (PDPs), Cathode Ray Tubes (CRTs), and the like. In the field of LED packaging and white light conditioning thereof, low melting point glass is required to replace organic matter for packaging. Glass ceramics for LED/Laser (LD) illumination also have a high demand for low melting point glass powders to reduce thermal degradation of the phosphor during high temperature sintering. The remote phosphor for the LED/laser illumination system is composed of a carrier material and a luminescent agent, and the commonly used carrier material is organic materials such as PC, epoxy resin, PMMA, and the like. However, organic materials generally have a disadvantage of poor thermal stability and chemical stability, and particularly, organic materials are seriously degraded by laser irradiation with high energy density. The fluorescent glass ceramic combines the advantages of luminescent crystals and inorganic glass materials, has good optical performance, and compared with organic resin, the glass has the advantages of good thermal stability, high chemical stability, simple preparation method, good optical performance, coating protection effect on fluorescent powder and the like. The manufacture of the fluorescent glass ceramic needs to adopt low-melting-point glass powder and fluorescent powder materials to sinter and form at high temperature, and the luminescent performance of the fluorescent powder is deteriorated due to the overhigh sintering temperature. Therefore, the development of low-melting glass frit is important for the production of glass ceramics for laser illumination.
The traditional low-melting point glass powder mostly contains PbO and PbO has good adjusting effect on the structure and the performance of the glass. The PbO not only has the function of reducing the phase transition temperature of the glass powder, but also can enhance the chemical stability and the fluidity of the system. PbO-SiO is often selected for preparing lead-containing sealing glass powder at home and abroad2、PbO-B2O3、PbO-B2O3-SiO2、PbO-ZnO-B2O3And the like. Although the lead-containing low-melting-point glass powder has the advantages of low softening temperature, high chemical stability and the like, lead has great harm to the health of human beings. For this reason, researchers in the related art have been working on the development of low melting point glass frit without lead.
The well-known low melting point glass frit without lead is Bi2O3-B2O3-ZnO ternary and B2O3-BaO-SiO-Bi2O3The quaternary system, but the glass transition temperature of the quaternary system is higher than 550 ℃, and the application requirements of low-temperature sealing/packaging and sintering are difficult to meet. In the development of lead-free low-melting glass frit, phosphate system is one of the systems which have been actively studied abroad in recent years. U.S. Pat. No. 5021366 discloses a phosphate low-melting glass powder, the softening temperature of the glass is 400-430 ℃. U.S. Pat. No. P5153151 discloses a phosphate sealing glass having a transition temperature of 300 to 340 ℃, however, the glass has a disadvantage of containing Tl, which is very toxic2O。
Disclosure of Invention
Aiming at the defects of the prior art, the invention provides a method for preparing luminescent glass ceramic by using low-melting-point glass powder.
Another object of the present invention is to provide a luminescent glass-ceramic obtained by the above method.
The purpose of the invention is realized by the following technical scheme.
A preparation method of low-melting-point glass powder comprises the following steps:
1) uniformly mixing the raw material medicines, and melting for 15-90 minutes at 300-700 ℃ to obtain glass liquid;
2) quenching the glass liquid at 300-700 ℃: pouring the glass liquid into a copper mold, and naturally cooling to room temperature of 20-25 ℃ to obtain bulk glass;
3) crushing the massive glass, and putting the crushed massive glass into a ball mill for ball milling to obtain low-melting-point glass powder;
wherein the raw material medicine comprises, by weight, 40-70% of SnF 220 to 60% of P2O5And 0-20% of a glass powder phase transition temperature adjusting component, wherein the glass powder phase transition temperature adjusting component is B2O3、V2O5、Sb2O3、Bi2O3、SiO2、Al2O3、ZnO、MgO、ZrO2And CaO in any proportion.
In the technical scheme, the raw material medicine comprises 45-60% of SnF (stannic fluoride) in percentage by weight 230 to 50% of P2O5And 0-20% of glass powder phase transition temperature adjusting component.
In the technical scheme, in the step 1), the melting temperature is 400-600 ℃, and the melting time is 20-60 minutes.
In the above technical solution, the SnF2And P2O5The mass part ratio of (1.9-2) to 1, and the glass powder phase transition temperature adjusting component is B2O。
In the above technical solution, the SnF2And P2O5The mass portion ratio of (1.4-1.5): 1, and the glass powder phase transition temperature adjusting component is V2O5、Sb2O3And Bi2O3In which V is2O5、Sb2O3And Bi2O3The mass ratio of (1-3): (1-2): 1.
in the above technical solution, the SnF2And P2O5The mass portion ratio of (1.1-1.2): 1, and the glass powder phase transition temperature adjusting component is B2O3、Bi2O3And SiO2In which B is2O3、Bi2O3And SiO2The mass ratio of (1-2): (1-3): 1.
in the above technical solution, the SnF2And P2O5The mass portion ratio of (1.4-1.5): 1, and the glass powder phase transition temperature adjusting component is SiO2A mixture of ZnO and MgO, wherein SiO2And the mass ratio of ZnO to MgO is (1-4): (0.5-2): 1.
in the above technical solution, the SnF2And P2O5The mass part ratio of (1.5-2) to 1, and the glass powder phase transition temperature adjusting component is B2O3、SiO2、Al2O3、ZrO2And CaO, wherein B2O3、SiO2、Al2O3、ZrO2And CaO in a mass ratio of (0.7-1.5): (1-3): (0.5-2): 1.
the low-melting-point glass powder obtained by the preparation method.
A method for preparing luminescent glass ceramic by using the low-melting-point glass powder comprises the following steps: uniformly mixing the low-melting-point glass powder and the fluorescent powder, and calcining; wherein the calcining temperature is higher than the phase transition temperature of the low-melting-point glass powder by 25-35 ℃, and the calcining time is 10-30 minutes.
In the technical scheme, the particle size of the low-melting-point glass powder is 3-10 microns.
In the above technical solution, the phase transition temperature is measured by a differential scanning calorimeter.
In the technical scheme, the calcining temperature is 200-500 ℃.
In the above technical scheme, the calcination temperature is higher than 30 ℃ of the phase transition temperature of the low melting point glass powder.
In the technical scheme, the low-melting-point glass powder and the fluorescent powder are uniformly mixed by ball milling, ethanol is used as a ball milling medium, and the ball milling time is at least 2 hours.
In the technical scheme, the ball milling time is 4 hours.
A luminescent glass-ceramic prepared by the above method.
The application of the glass ceramic prepared from the low-melting-point glass powder in illumination as a remote fluorescent light-emitting body is characterized in that the low-melting-point glass powder and fluorescent powder are uniformly mixed, pressed into a sheet with the thickness of 1-5 mm and calcined; wherein the calcining temperature is higher than the phase transition temperature by 25-35 ℃, and the calcining time is 10-30 minutes.
In the technical scheme, the ratio of the low-melting-point glass powder to the fluorescent powder in parts by mass is (6-10): (1-3).
In the above technical scheme, the calcination temperature is higher than 30 ℃ of the phase transition temperature.
Compared with the prior art, the low-melting-point glass powder has lower glass phase transition temperature, and the glass phase transition temperature of the low-melting-point glass powder can be adjusted within the range of 200-500 ℃, so that the low-melting-point glass powder is suitable for manufacturing sealing glass and vacuum components and packaging LEDs, is particularly suitable for manufacturing luminescent glass ceramics with fluorescent powder materials, and is particularly suitable for laser illumination. The glass ceramic is molded and sintered at a lower temperature, so that the thermal degradation of the fluorescent powder at a high temperature can be effectively avoided, and the glass ceramic has an important application value in the field of laser illumination.
Drawings
FIG. 1 is an XRD diffraction pattern of the low melting point glass powder prepared in example 1;
FIG. 2 shows the low melting point glass frit obtained in example 1 and 20% YAG: ce3+Emission spectrum of the glass ceramic prepared from the yellow fluorescent powder under the excitation of a 447nm blue laser;
FIG. 3 shows the low melting point glass frit and 10% CaAlSiN in example 33：Eu2+The emission spectrum of the glass ceramic prepared from the red fluorescent powder under the excitation of a 447nm blue laser is shown, wherein the wavelength 1 is the excitation spectrum, and the wavelength 2 is the emission spectrum.
Detailed Description
In a specific embodiment of the invention, SnF2Purchased from Henan Green resources science and technology Limited in Hubei, with a purity of 99.5%; other various medicines are purchased from Shanghai Aladdin Biotechnology GmbH with purity ofAnd (5) purifying. SnF2Introduced from stannous fluoride, P2O5B of glass powder phase transition temperature regulating component introduced by ammonium dihydrogen phosphate2O3Introduced by boric acid, V2O5Introduced by ammonium metavanadate, the others by the corresponding oxides. The differential scanning calorimeter is model number TA instruments Q2000. YAG: ce3+The yellow phosphor is purchased from Shenzhen Shenxing Lianli science and technology Limited. CaAlSiN3：Eu2+The red phosphor was prepared according to the following literature: [1]Preparation and Performance Studies of Eu-doped CaAlSiN-3 and YAG Red phosphor [ D ]]University of Nanchang, 2015. The water quenching mode is forbidden when the molten glass is cooled and formed (quenched), otherwise, the glass components react with water. The XRD tester is Shimadzu X-ray diffractometer XRD-6000, and the emission spectrum tester is F-4600 fluorescence spectrometer (Hitachi).
The technical scheme of the invention is further explained by combining specific examples.
A preparation method of low-melting-point glass powder comprises the following steps:
1) uniformly mixing the raw material medicines according to the parameters and the formula described in the table 1, and melting at the melting temperature of 300-700 ℃ for 15-90 minutes to obtain glass liquid;
2) quenching glass liquid at 300-700 ℃: pouring the glass liquid into a copper mold (disc-shaped, the depth of the inner cavity of the mold is 1cm, and the radius of the inner cavity of the mold is 5cm), and naturally cooling to room temperature of 20-25 ℃ to obtain bulk glass;
3) mechanically crushing the massive glass, and putting the crushed massive glass into a ball mill for ball milling to obtain low-melting-point glass powder;
wherein, the weight percentage of the raw material medicine, the melting temperature and the melting time are shown in the table 1.
TABLE 1 weight ratios of the components, melting temperatures and times, and phase transition temperatures of the low melting glass powders of examples 1-6
FIG. 1 is an XRD diffraction pattern of the low melting point glass powder prepared in example 1, and from the XRD pattern, the obtained sample has a very wide amorphous cell at about 23 degrees, which illustrates the SnF provided by the invention2-P2O5The system is a good glass system.
80% by weight of the low-melting glass frit of example 1 and 20% by weight of YAG: ce3+Ball-milling the yellow fluorescent powder for 4 hours, uniformly mixing, pressing into a 2mm slice, and sintering in an electric furnace at 230 ℃ for 20 minutes to obtain the luminescent glass ceramic; the luminescent glass ceramic can obtain white light emission under the excitation of a blue laser, and the emission spectrum of the luminescent glass ceramic is shown in figure 2.
70% by weight of the low-melting glass frit of example 2 and 30% by weight of YAG: ce3+Ball-milling the yellow fluorescent powder for 4 hours, uniformly mixing, pressing into a sheet with the thickness of 3mm, and sintering in an electric furnace at the temperature of 260 ℃ for 20 minutes to obtain the luminescent glass ceramic; the luminescent glass ceramic can obtain white light emission under the excitation of a blue laser.
90% by weight of the low-melting glass frit of example 3 and 10% by weight of CaAlSiN3：Eu2+Ball-milling the red fluorescent powder for 4 hours, uniformly mixing, pressing into a sheet with the thickness of 2.5mm, and sintering in an electric furnace at the temperature of 300 ℃ for 30 minutes to obtain the luminescent glass ceramic; under the excitation of a blue laser, the luminescent glass ceramic can obtain synchronous emission of red light and blue light, and the emission spectrum of the luminescent glass ceramic is shown in figure 3.
80% by weight of the low melting glass frit of example 4 and 20% by weight of CaAlSiN3：Eu2+Ball-milling the red fluorescent powder for 4 hours, uniformly mixing, pressing into a 2mm slice, and sintering in an electric furnace at 380 ℃ for 30 minutes to obtain the luminescent glass ceramic; under the excitation of blue laser, the luminescent glass ceramic can obtain synchronous emission of red light and blue light.
According to the weight percentage, 70 percent of the low-melting-point glass powder of the embodiment 5 and 30 percent of red, green and blue fluorescent powder are evenly mixed by ball milling for 4 hours, pressed into a sheet with the thickness of 2mm and sintered in an electric furnace at the temperature of 450 ℃ for 20 minutes to obtain the luminescent glass ceramic; the luminescent glass ceramic can obtain white light emission under the excitation of an ultraviolet laser.
According to the weight percentage, 80 percent of the low-melting-point glass powder of the embodiment 6 and 20 percent of red and green fluorescent powder which can be excited by blue light are ball-milled for 4 hours and are evenly mixed, pressed into a sheet with the thickness of 2mm, and sintered for 20 minutes in an electric furnace at the temperature of 500 ℃ to obtain the luminescent glass ceramic; under the excitation of the luminescent glass ceramic blue laser, white light emission can be obtained.
The properties consistent with the above examples can be obtained by adjusting the phase transition temperature adjusting component, the base component, the melting temperature and the melting time of the present technical solution.
The invention has been described in an illustrative manner, and it is to be understood that any simple variations, modifications or other equivalent changes which can be made by one skilled in the art without departing from the spirit of the invention fall within the scope of the invention.
Claims (8)
1. A method for preparing luminescent glass ceramic by using low-melting-point glass powder is characterized by comprising the following steps: uniformly mixing the low-melting-point glass powder and the fluorescent powder, and calcining; wherein the calcining temperature is higher than the phase transition temperature by 25-35 ℃, and the calcining time is 10-30 minutes;
the preparation method of the low-melting-point glass powder comprises the following steps:
1) uniformly mixing the raw material medicines, and melting for 15-90 minutes at 300-700 ℃ to obtain glass liquid;
2) quenching the glass liquid at 300-700 ℃: pouring the glass liquid into a copper mold, and naturally cooling to room temperature of 20-25 ℃ to obtain bulk glass;
3) crushing the block glass, putting the crushed block glass into a ball mill for ball milling to obtain low-melting-point glass powder,
wherein the raw material comprises, by weight, 40-70% of SnF230 to 50% of P2O5And 0-20% of a glass powder phase transition temperature adjusting component, wherein the glass powder phase transition temperature adjusting component is B2O3、V2O5、Sb2O3、Bi2O3、SiO2、Al2O3、ZnO、MgO、ZrO2And one or a mixture of more than one of CaO in any proportion;
the SnF2And P2O5The mass part ratio of (1.9-2) to 1, and the glass powder phase transition temperature adjusting component is B2O3；
Or, the SnF2And P2O5The mass portion ratio of (1.4-1.5): 1, and the glass powder phase transition temperature adjusting component is V2O5、Sb2O3And Bi2O3In which V is2O5、Sb2O3And Bi2O3The mass ratio of (1-3): (1-2): 1;
or, the SnF2And P2O5The mass portion ratio of (1.1-1.2): 1, and the glass powder phase transition temperature adjusting component is B2O3、Bi2O3And SiO2In which B is2O3、Bi2O3And SiO2The mass ratio of (1-2): (1-3): 1;
or, the SnF2And P2O5The mass portion ratio of (1.4-1.5): 1, and the glass powder phase transition temperature adjusting component is SiO2A mixture of ZnO and MgO, wherein SiO2And the mass ratio of ZnO to MgO is (1-4): (0.5-2): 1;
or, the SnF2And P2O5The mass part ratio of (1.5-2) to 1, and the glass powder phase transition temperature adjusting component is B2O3、SiO2、Al2O3、ZrO2And CaO, wherein B2O3、SiO2、Al2O3、ZrO2And CaO in the massThe amount ratio is (0.7-1.5): (1-3): (0.5-2): 1.
2. the method according to claim 1, wherein the ratio of the low-melting-point glass powder to the fluorescent powder in parts by mass is (6-10): (1-3).
3. The method according to claim 2, wherein in the step 1), the melting temperature is 400 to 600 ℃.
4. The method according to claim 3, wherein in 1), the melting time is 20 to 60 minutes.
5. The method of claim 4, wherein the low melting point glass powder and the phosphor powder are ball milled to achieve uniform mixing, and ethanol is used as a ball milling medium for at least 2 hours.
6. The method according to claim 5, wherein the calcination temperature is 200 to 500 ℃ and 30 ℃ higher than the phase transition temperature.
7. The method according to claim 6, wherein the low-melting-point glass frit has a particle size of 3 to 10 μm.
8. A luminescent glass-ceramic prepared by the method of any one of claims 1 to 7.
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