WO2020082328A1 - 电子设备盖板用微晶玻璃制品和微晶玻璃 - Google Patents

电子设备盖板用微晶玻璃制品和微晶玻璃 Download PDF

Info

Publication number
WO2020082328A1
WO2020082328A1 PCT/CN2018/112078 CN2018112078W WO2020082328A1 WO 2020082328 A1 WO2020082328 A1 WO 2020082328A1 CN 2018112078 W CN2018112078 W CN 2018112078W WO 2020082328 A1 WO2020082328 A1 WO 2020082328A1
Authority
WO
WIPO (PCT)
Prior art keywords
glass
zro
sio
ceramic
mgo
Prior art date
Application number
PCT/CN2018/112078
Other languages
English (en)
French (fr)
Inventor
原保平
Original Assignee
成都创客之家科技有限公司
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by 成都创客之家科技有限公司 filed Critical 成都创客之家科技有限公司
Priority to KR1020207033502A priority Critical patent/KR102294910B1/ko
Priority to JP2020567227A priority patent/JP7048767B2/ja
Priority to CN201880090187.5A priority patent/CN111936439B/zh
Priority to KR1020217025914A priority patent/KR102609966B1/ko
Priority to PCT/CN2018/112078 priority patent/WO2020082328A1/zh
Priority to EP18937644.5A priority patent/EP3808711A4/en
Priority to US16/223,918 priority patent/US10676390B2/en
Priority to US16/859,527 priority patent/US10913681B2/en
Publication of WO2020082328A1 publication Critical patent/WO2020082328A1/zh

Links

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
    • C03C3/00—Glass compositions
    • C03C3/04—Glass compositions containing silica
    • C03C3/076—Glass compositions containing silica with 40% to 90% silica, by weight
    • C03C3/097—Glass compositions containing silica with 40% to 90% silica, by weight containing phosphorus, niobium or tantalum
    • 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
    • C03C10/0018—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 monovalent metal oxide as main constituents
    • C03C10/0027—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 monovalent metal oxide as main constituents containing SiO2, Al2O3, Li2O as main constituents
    • 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
    • C03C21/00—Treatment of glass, not in the form of fibres or filaments, by diffusing ions or metals in the surface
    • C03C21/001—Treatment of glass, not in the form of fibres or filaments, by diffusing ions or metals in the surface in liquid phase, e.g. molten salts, solutions
    • C03C21/002—Treatment of glass, not in the form of fibres or filaments, by diffusing ions or metals in the surface in liquid phase, e.g. molten salts, solutions to perform ion-exchange between alkali ions
    • 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
    • C03C3/00—Glass compositions
    • C03C3/04—Glass compositions containing silica
    • C03C3/076—Glass compositions containing silica with 40% to 90% silica, by weight
    • C03C3/083—Glass compositions containing silica with 40% to 90% silica, by weight containing aluminium oxide or an iron compound
    • C03C3/085—Glass compositions containing silica with 40% to 90% silica, by weight containing aluminium oxide or an iron compound containing an oxide of a divalent metal
    • H—ELECTRICITY
    • H05—ELECTRIC TECHNIQUES NOT OTHERWISE PROVIDED FOR
    • H05K—PRINTED CIRCUITS; CASINGS OR CONSTRUCTIONAL DETAILS OF ELECTRIC APPARATUS; MANUFACTURE OF ASSEMBLAGES OF ELECTRICAL COMPONENTS
    • H05K5/00—Casings, cabinets or drawers for electric apparatus
    • H05K5/02—Details
    • H05K5/03—Covers
    • 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
    • C03C2201/00—Glass compositions
    • C03C2201/06—Doped silica-based glasses
    • C03C2201/30—Doped silica-based glasses containing metals
    • C03C2201/32—Doped silica-based glasses containing metals containing aluminium
    • 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
    • C03C2201/00—Glass compositions
    • C03C2201/06—Doped silica-based glasses
    • C03C2201/30—Doped silica-based glasses containing metals
    • C03C2201/40—Doped silica-based glasses containing metals containing transition metals other than rare earth metals, e.g. Zr, Nb, Ta or Zn
    • 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
    • C03C2201/00—Glass compositions
    • C03C2201/06—Doped silica-based glasses
    • C03C2201/30—Doped silica-based glasses containing metals
    • C03C2201/50—Doped silica-based glasses containing metals containing alkali metals
    • 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
    • C03C2201/00—Glass compositions
    • C03C2201/06—Doped silica-based glasses
    • C03C2201/30—Doped silica-based glasses containing metals
    • C03C2201/54—Doped silica-based glasses containing metals containing beryllium, magnesium or alkaline earth metals
    • 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
    • C03C2204/00—Glasses, glazes or enamels with special properties

Definitions

  • the invention relates to a crystallized glass product and a crystallized glass, in particular to a crystallized glass product for a cover plate of an electronic device, a crystallized glass, a glass cover plate for an electronic device and an electronic device.
  • Glass-ceramic is a material that precipitates crystals inside the glass by heat-treating the glass.
  • Glass-ceramics can have physical property values not available in glass due to crystals dispersed inside. For example, mechanical strengths such as Young's modulus and fracture toughness, etching properties for acidic or alkaline chemicals, thermal properties such as coefficient of thermal expansion, and increase and disappearance of glass transition temperature. Glass-ceramics have higher mechanical properties, and due to the formation of crystallites in the glass, their bending and abrasion resistance have obvious advantages over ordinary glass.
  • the inventors hope to develop glass-ceramics with excellent mechanical properties through a large number of experimental studies, which are suitable for electronic devices.
  • the technical problem to be solved by the present invention is to provide a glass-ceramic product for a cover plate of an electronic device, which has excellent mechanical properties.
  • Glass-ceramic products for cover plates of electronic equipment whose main crystal phase contains lithium silicate and quartz crystal phases, whose composition is expressed by weight percentage, and contains: SiO 2 : 65-85%, Al 2 O 3 : 1 ⁇ 15%, Li 2 O: 5 to 15%, ZrO 2 : 0.1 to 10%, P 2 O 5 : 0.1 to 10%, K 2 O: 0 to 10%, MgO: 0 to 10%, ZnO: 0 to 10%, Na 2 O: 0 to 5%, where (SiO 2 + Al 2 O 3 + Li 2 O + ZrO 2 ) / P 2 O 5 is 40 to 90, and the height of the ball drop test is 700 mm or more.
  • Glass-ceramic products for electronic equipment cover plates the composition of which is expressed as a percentage by weight, containing: SiO 2 : 65-85%, Al 2 O 3 : 1-15%, Li 2 O: 5-15%, ZrO 2 : 0.1 to 10%, P 2 O 5 : 0.1 to 10%, K 2 O: 0 to 10%, MgO: 0 to 10%, ZnO: 0 to 10%, Na 2 O: 0 to 5%.
  • the glass-ceramic product for electronic equipment cover plates according to any one of (1) to (2), the composition of which is expressed as a percentage by weight, and further contains: SrO: 0 to 5%, BaO: 0 to 5%, TiO 2 : 0 to 5%, Y 2 O 3 : 0 to 5%, B 2 O 3 : 0 to 3%, clarifier: 0 to 2%.
  • the crystallized glass product for electronic device covers according to any one of (1) to (3), wherein: (SiO 2 + Li 2 O) / Al 2 O 3 is 6-15, (Al 2 O 3 + Li 2 O) / P 2 O 5 is 5-20, (SiO 2 + Li 2 O) / P 2 O 5 is 40-80, (K 2 O + MgO) / ZrO 2 is 0.6-1.2, or Li 2 O / (K 2 O + ZrO 2 ) is 2.3 to 4.0.
  • the glass-ceramic product for electronic device covers according to any one of (1) to (4), wherein: (SiO 2 + Li 2 O) / Al 2 O 3 is 8 to 13, and (Al 2 O 3 + Li 2 O) / P 2 O 5 is 6-14, (SiO 2 + Li 2 O) / P 2 O 5 is 40-70, (SiO 2 + Al 2 O 3 + Li 2 O + ZrO 2 ) / P 2 O 5 is 45 to 85, (K 2 O + MgO) / ZrO 2 is 0.7 to 1.1, and Li 2 O / (K 2 O + ZrO 2 ) is 2.5 to 3.5.
  • the glass-ceramic product for electronic device covers according to any one of (1) to (5), whose composition is expressed as a percentage by weight and contains: SiO 2 : 70 to 76%, Al 2 O 3 : 4 to 10%, Li 2 O: 8 to 12.5%, ZrO 2 : 1 to 5%, P 2 O 5 : 1 to 3%, K 2 O: 0 to 3%, MgO: 0.3 to 2%, ZnO: 0 to 3%, Na 2 O: 0 to 1%, Sb 2 O 3 : 0 to 1%, SnO 2 : 0 to 1%, SnO: 0 to 1%, or CeO 2 : 0 to 1%.
  • the glass-ceramic product for electronic device covers according to any one of (1) to (6), wherein: (Al 2 O 3 + Li 2 O) / P 2 O 5 is 8.5 to 14, (SiO 2 + Li 2 O) / P 2 O 5 is 45-60, (SiO 2 + Al 2 O 3 + Li 2 O + ZrO 2 ) / P 2 O 5 is 48-80, or (SiO 2 + Li 2 O ) / Al 2 O 3 is 8.5 to 12.
  • the glass-ceramic product for electronic device covers according to any one of (1) to (7), wherein: (K 2 O + MgO) / ZrO 2 is 0.8 to 1.0, or Li 2 O / (K 2 O + ZrO 2 ) is 2.8 to 3.3.
  • the crystallized glass product for electronic device covers according to any one of (1) to (8), whose composition is expressed as a percentage by weight, contains: Li 2 O: 8 to less than 10%, does not contain SrO, does not With BaO, without TiO 2 , without Y 2 O 3 , without GeO 2 , without CaO, without Cs 2 O, without PbO, without B 2 O 3 , without As 2 O 3 , without La 2 O 3 does not contain Tb 2 O 3 .
  • the glass-ceramic product for electronic device covers according to any one of (1) to (9), having a crystallinity of 70% or more.
  • the ball drop test height is 1000 mm or more; or the four-point bending strength is 650 MPa or more; or the haze of 0.55 mm thickness is 0.5% or less; or the refractive index temperature coefficient is -0.8 ⁇ 10 -6 / ° C or less; or the light transmittance of 0.55 mm thick and 550 nm wavelength is 88% or more.
  • the invention also provides a glass-ceramic with excellent mechanical properties.
  • Glass-ceramics the composition of which is expressed as a percentage by weight, containing: SiO 2 : 65-85%, Al 2 O 3 : 1-15%, Li 2 O: 5-15%, ZrO 2 : 0.1-10% , P 2 O 5 : 0.1-10%, K 2 O: 0-10%, MgO: 0-10%, ZnO: 0-10%.
  • the invention also provides a glass cover for electronic equipment:
  • a glass cover for electronic devices comprising the glass-ceramic product for electronic device covers according to any one of (1) to (11), or the glass-ceramic for any of (12) to (18).
  • the invention also provides an electronic device:
  • the beneficial effects of the present invention are: through reasonable component design, the glass-ceramics and glass-ceramic products of the present invention have excellent mechanical properties and are suitable for electronic equipment.
  • the glass-ceramics and glass-ceramic products of the present invention are materials having a crystal phase and a glass phase, which are different from amorphous solids.
  • the crystal phase of glass-ceramics and glass-ceramic products can be identified by the peak angle appearing in the X-ray diffraction pattern analyzed by X-ray diffraction and by TEMEDX.
  • the main crystal phase is measured by X-ray diffraction.
  • the inventor of the present invention has conducted repeated experiments and researches to determine the specific components constituting the glass-ceramics and glass-ceramics products by setting their contents and content ratios to specific values and precipitating specific crystal phases at a lower cost
  • the crystallized glass or glass-ceramic product of the present invention is obtained.
  • composition converted into oxide refers to the melting of oxides, composite salts, hydroxides, etc. used as raw materials of the glass composition of the present invention, glass-ceramics or glass-ceramic products.
  • the total amount of the oxide is regarded as 100%.
  • glass when only referred to as glass, it is a glass composition before crystallization, and after the glass composition is crystallized, it is called glass-ceramics, and glass-ceramic products refer to glass-ceramics after chemical tempering.
  • the numerical ranges listed herein include upper and lower limits, “above” and “below” include endpoints, all integers and fractions within the range, not limited to the defined range The specific values listed.
  • the term “about” refers to formulas, parameters, and other quantities and characteristics that are not, and need not be precise, and can be approximated and / or larger or lower if necessary, which reflects tolerances, conversion factors, and measurement errors, etc. .
  • “and / or” is inclusive, such as “A and / or B", meaning only A, or only B, or both A and B.
  • the glass, glass-ceramics, and glass-ceramics products of the present invention can be broadly described as lithium-containing aluminosilicate glass, glass-ceramics, and glass-ceramics products, including SiO 2 , Al 2 O 3 , and Li 2 O, in addition, includes other components such as ZrO 2 and P 2 O 5 .
  • the first main crystal phase of the crystallized glass and glass-ceramic product is lithium silicate; in some embodiments, the first main crystal phase is lithium permeable feldspar; in some In the embodiment, the first main crystal phase is a quartz crystal phase (including quartz, quartz, and quartz solid solution).
  • the main crystal phases include lithium silicate and quartz crystal phases.
  • the main crystalline phase includes lithium silicate and lithium feldspar.
  • the first crystal phase is lithium silicate and the second main crystal phase is a quartz crystal phase; in some embodiments, the first crystal phase is a quartz crystal phase and the second main crystal phase is lithium silicate; In some embodiments, the first crystal phase is lithium silicate and the second main crystal phase is lithium permeable feldspar; in some embodiments, the first crystal phase is lithium permeable feldspar and the second main crystal phase is silicic acid lithium.
  • the main crystal phase includes lithium silicate, lithium-permeable feldspar and quartz crystal phases; in some embodiments, the first crystal phase is lithium silicate, the second main crystal phase is lithium-permeable feldspar, and the third The main crystal phase is a quartz crystal phase; in some embodiments, the first crystal phase is lithium silicate, the second main crystal phase is a quartz crystal phase, and the third main crystal phase is lithium-permeable feldspar; in some embodiments, The first main crystal phase is lithium-permeable feldspar, the second main crystal phase is lithium silicate, and the third main crystal phase is a quartz crystal phase; in some embodiments, the first crystal phase is a quartz crystal phase and the second main crystal phase The phase is lithium silicate and the third main crystal phase is lithium-permeable feldspar.
  • the quartz crystal phase is an ⁇ -hexagonal quartz crystal phase; in some embodiments, the lithium silicate is lithium disilicate; there may also be ⁇ -spodumene ss, lithium phosphate as a secondary crystal phase Wait. It should be noted that the quartz crystal phase referred to herein includes two cases including only quartz crystal, quartz and quartz solid solution.
  • the weight percentage of the glass phase remaining in the glass-ceramics and glass-ceramic products is 8 to 45%; in some embodiments, 10 to 40%; in some embodiments, 12 to 40%; in some embodiments, 15-40%; in some embodiments, 15-35%; in some embodiments, 15-32%; in some embodiments, 20-45% 20-40% in some embodiments; 32-45% in some embodiments; 32-40% in some embodiments; 35-45% in some embodiments.
  • the fracture toughness of the crystallized glass becomes higher.
  • the main crystal phase of the crystallized glass is quartz crystal phase and lithium disilicate, the temperature coefficient of the refractive index of the crystallized glass becomes lower and the fracture toughness becomes higher; the height of the falling ball test of the crystallized glass products becomes larger and the four-point bending strength becomes larger .
  • the main crystal phase accounts for 50-92% by weight of the crystallized glass or glass-ceramic product; in some embodiments, the weight percentage reaches 60-90%; in some embodiments, the weight percentage reaches 65-85 %; In some embodiments, the weight percentage reaches 70-80%; in some embodiments, the weight percentage reaches 80-92%.
  • the main crystal phase referred to herein refers to a crystal phase having a higher weight percentage than other crystal phases present in the glass-ceramic or glass-ceramic product.
  • the weight percentage of quartz crystal phase of the crystallized glass or glass-ceramic product is below 70%; in some embodiments, the weight percentage of quartz crystal phase of the crystallized glass or glass-ceramic product is below 65%; In some embodiments, the weight percentage of the quartz crystal phase of the crystallized glass or glass-ceramic product is below 60%; in some embodiments, the weight percentage of the quartz crystal phase of the crystallized glass or glass-ceramic product is below 55%; In some embodiments, the weight percentage of quartz crystal phase of the crystallized glass or glass-ceramic product is below 50%; in some embodiments, the weight percentage of quartz crystal phase of the crystallized glass or glass-ceramic product is below 45%.
  • the weight percentage of the lithium silicate crystal phase of the crystallized glass or glass-ceramic product is below 55%; in some embodiments, the weight percentage of the lithium silicate crystal phase of the crystallized glass or glass-ceramic product is 50% or less; in some embodiments, the weight percentage of the lithium silicate crystal phase of the glass-ceramic or glass-ceramic product is below 45%; in some embodiments, the lithium silicate crystal of the glass-ceramic or glass-ceramic product The weight percentage of the phase is below 40%.
  • the weight percentage of the lithium-permeable feldspar crystal phase of the crystallized glass or glass-ceramic product is below 40%; in some embodiments, the weight of the lithium-permeable feldspar crystal phase of the glass-ceramic or glass-ceramic product The percentage is below 35%; in some embodiments, the weight percentage of the crystal-permeable feldspar crystal phase of the crystallized glass or glass-ceramic product is below 30%; in some embodiments, the transmission of the glass-ceramic or glass-ceramic product The weight percentage of the feldspar crystalline phase is below 25%; in some embodiments, the weight percentage of the lithium-permeable feldspar crystal phase of the glass-ceramic or glass-ceramic product is less than 20%; in some embodiments, the glass-ceramic or microcrystalline The weight percentage of the crystal-permeable feldspar crystal phase of the crystal glass product is below 15%.
  • SiO 2 is the basic component of the glass composition of the present invention and can be used to stabilize the network structure of glass and glass-ceramics. It is one of the components that form lithium silicate, quartz crystal phase and lithium-permeable feldspar after crystallization. If SiO 2 If the content is below 65%, the formation of crystals in the glass-ceramics will be less and the crystals will become coarser easily, which will affect the haze of the glass-ceramics and glass-ceramics products, as well as the drop-ball test height of the glass-ceramics products.
  • the lower limit of the content of SiO 2 is preferably 65%, preferably 70%; if the content of SiO 2 is above 85%, the glass melting temperature is high, the material is difficult, and it is not easy to form, which affects the consistency of the glass. Therefore, the content of SiO 2
  • the upper limit is preferably 85%, preferably 80%, and more preferably 76%. In some embodiments, it may comprise about 66%, 67%, 68%, 69%, 70%, 71%, 72%, 73%, 74%, 75%, 76%, 77%, 78%, 79% , 80%, 81%, 82%, 83%, 84% SiO 2 .
  • Al 2 O 3 is a component that forms a glass network structure. It is an important component that helps stabilize glass forming and improve chemical stability. It can also improve the mechanical properties of glass and increase the depth and surface of the ion exchange layer of glass-ceramic products Stress, but if the content is less than 1%, the effect is not good, so the lower limit of the Al 2 O 3 content is 1%, preferably 4%. On the other hand, if the content of Al 2 O 3 exceeds 15%, the meltability and devitrification resistance of the glass decrease, and the crystals tend to increase during crystallization, reducing the strength of the glass-ceramics and glass-ceramic products, therefore, The upper limit of the Al 2 O 3 content is 15%, preferably 12%, and more preferably 10%. In some embodiments, it may comprise about 1%, 2%, 3%, 4%, 5%, 6%, 7%, 8%, 9%, 10%, 11%, 12%, 13%, 14% , 15% Al 2 O 3 .
  • Li 2 O is an essential component that becomes a crystal phase composition after crystallization, contributes to the formation of a lithium-containing crystal phase such as lithium silicate and lithium permeable feldspar, and is also an essential component for chemical strengthening.
  • the lower limit of the Li 2 O content is 5%, preferably 7%, more preferably 8%, and in some embodiments, further preferably 9%; on the other hand
  • the upper limit of the Li 2 O content is preferably 15% , More preferably 12.5%, and in some embodiments, further preferably less than 10%. In some embodiments, about 5%, 6%, 7%, 8%, 9%, 9.8%, 10%, 11%, 12%, 13%, 14%, 15% of Li 2 O may be included.
  • P 2 O 5 is an optional component that helps to improve the low-temperature meltability of glass. It can separate phases in the glass to form crystal nuclei and improve the thermal expansion stability of the glass during crystallization.
  • the lower limit of the P 2 O 5 content is preferred 0.1, more preferably 0.5%, still more preferably 1%; however, if P 2 O 5 is contained excessively, it is easy to reduce the devitrification resistance of the glass and the phase separation of the glass, and the mechanical properties of the glass are deteriorated trend. Therefore, the upper limit of the P 2 O 5 content is 10%, preferably 5%, and more preferably 3%. In some embodiments, it may comprise about 0%, 0.1%, 0.3%, 0.5%, 1%, 2%, 3%, 4%, 5%, 6%, 7%, 8%, 9%, 10% P 2 O 5 .
  • the depth of the ion exchange layer of the glass-ceramic product can be optimized, especially (SiO 2 + Li 2 O) /
  • the value of P 2 O 5 is in the range of 40 to 70, and the value of (SiO 2 + Li 2 O) / P 2 O 5 is more preferably 42 to 60, further preferably 45 to 60, and the glass-ceramic product can obtain a deeper Ion exchange layer; in some embodiments, the value of (SiO 2 + Li 2 O) / P 2 O 5 is in the range of 40-70, more preferably the value of (SiO 2 + Li 2 O) / P 2 O 5 When it is 42-60, more preferably within 45-60, the crystallization process is beneficial to the formation of quartz crystal phase and lithium disilicate, and it can also make the glass-ceramics and glass-ceramic products have an excellent refractive index temperature coefficient, making
  • the value of (SiO 2 + Li 2 O) / P 2 O 5 may be 40, 41, 42, 43, 44, 45 , 46, 47, 48, 49, 50, 51, 52 , 53 , 54, 55, 56, 57, 58, 59, 60, 61, 62, 63, 64, 65, 66, 67, 68, 69, 70.
  • Al 2 O 3 , Li 2 O and P 2 O 5 are the introduction ratios in the glass, which have an important influence on the surface stress and four-point bending strength of glass-ceramics and glass-ceramic products.
  • glass-ceramics The four-point bending strength of the glass-ceramic product is 600 MPa or more, preferably 650 MPa or more, and more preferably 700 MPa or more.
  • the value of (Al 2 O 3 + Li 2 O) / P 2 O 5 may be 5 , 5.5, 6, 6.5, 7, 7.5, 8, 8.5, 9, 9.5, 10, 10.5, 11 , 11.5, 12, 12.5, 13, 13.5, 14, 14.5, 15, 15.5, 16, 16.5, 17, 17.5, 18, 18.5, 19, 19.5, 20.
  • ZrO 2 has the function of crystal precipitation and formation of crystal nuclei, and at the same time helps to improve the chemical stability of the glass. It is found that ZrO 2 can also significantly reduce glass devitrification and liquidus temperature during the formation process. To improve the stability of Li 2 O-Al 2 O 3 -SiO 2 -P 2 O 5 glass.
  • the lower limit of the ZrO 2 content is preferably 0.1, more preferably 0.5%, and still more preferably 1%; but if ZrO 2 is contained excessively, the devitrification resistance of the glass is easily reduced, and the glass crystallization process is controlled As the difficulty increases, the upper limit of the ZrO 2 content is 10%, preferably 6%, and more preferably 5%. In some embodiments, it may comprise about 0%, 0.1%, 0.3%, 0.5%, 1%, 2%, 3%, 4%, 5%, 6%, 7%, 8%, 9%, 10% ZrO 2 .
  • the inventors found that by controlling the ratio of the total content of SiO 2 , Al 2 O 3 , Li 2 O, and ZrO 2 to the amount of P 2 O 5 introduced (SiO 2 + Al 2 O 3 + Li 2 O + ZrO 2 ) / P 2 O 5 is in the range of 40 ⁇ 90, which can make the glass-ceramic products withstand the impact of falling balls above 700mm, preferably (SiO 2 + Al 2 O 3 + Li 2 O + ZrO 2 ) / P 2 O 5 is 45-85; especially in some embodiments, when (SiO 2 + Al 2 O 3 + Li 2 O + ZrO 2 ) / P 2 O 5 is in the range of 46-80, it is easier to form disilicic acid Lithium and quartz crystal phases, and glass-ceramic products are easier to obtain excellent fracture toughness, the fracture toughness can be 1MPa ⁇ m 1/2 or more, preferably 1.3MPa ⁇ m 1/2 or more, more preferably
  • (SiO 2 + Al 2 O 3 + Li 2 O + ZrO 2 ) / P 2 O 5 may be 40, 41, 42, 43, 44, 45, 46, 47, 48, 49, 50 , 51, 52, 53, 54, 55, 56, 57, 58, 59, 60, 61, 62, 63, 64, 65, 66, 67, 68, 69, 70, 71, 72, 73, 74, 75 , 76, 77, 78, 79, 80, 81, 82, 83, 84, 85, 86, 87, 88, 89, 90.
  • K 2 O is an optional component that contributes to improving the low-temperature meltability and formability of glass.
  • the content of K 2 O is 0 to 10%, preferably 0 to 5%, and more preferably 0 to 3%. In some embodiments, it may comprise about 0%, greater than 0%, 0.1%, 0.3%, 0.5%, 1%, 2%, 3%, 4%, 5%, 6%, 7%, 8%, 9 %, 10% K 2 O.
  • Li 2 O / (K 2 O + ZrO 2 ) is in the range of 2.3 to 4.0 .
  • the ball test height is preferably 800 mm or more, more preferably 1000 mm or more It is more preferably 1200 mm or more.
  • the value of Li 2 O / (K 2 O + ZrO 2 ) may be 2.3, 2.4, 2.5, 2.6, 2.7, 2.8, 2.9, 3.0, 3.1, 3.2, 3.3, 3.4, 3.5, 3.6, 3.7, 3.8, 3.9, 4.0.
  • the ZnO can improve the melting performance of the glass, improve the chemical stability of the glass, refine the crystal grains during crystallization, and control the upper limit of the ZnO content to 10% or less to suppress the loss of devitrification. Therefore, the upper limit of the ZnO content is 10% , Preferably 5%, more preferably 3%. In some embodiments, it may comprise about 0%, greater than 0%, 0.1%, 0.5%, 1%, 2%, 3%, 4%, 5%, 6%, 7%, 8%, 9%, 10 % ZnO.
  • MgO helps to reduce the viscosity of the glass, suppress the devitrification of the glass during molding and refine the crystal grains during crystallization, and also has the effect of improving the low temperature melting property.
  • MgO is an optional component in the present invention, and the preferred content is 0.3% or more; However, if the content of MgO is too high, it may cause the devitrification resistance to decrease, and undesirable crystals will be obtained after crystallization, resulting in the performance of glass-ceramics and glass-ceramics products. Therefore, the upper limit of MgO content is 10%. It is preferably 5%, and more preferably 2%. In some embodiments, it may comprise about 0%, greater than 0%, 0.5%, 1%, 2%, 3%, 4%, 5%, 6%, 7%, 8%, 9%, 10% MgO .
  • the ratio of the amount of K 2 O + MgO and ZrO 2 introduced (K 2 O + MgO) / ZrO 2 is in the range of 0.6 to 1.2.
  • SrO is an optional component that improves the low-temperature melting property of glass and inhibits the formation of crystallizing. In the present invention, it is preferable to control SrO to 5% or less, which can make it easy to obtain excellent crystallite size for glass-ceramics and glass-ceramic products. The content is below 1%, and in some embodiments, it is preferably not introduced. In some embodiments, SrO may be included at about 0%, greater than 0%, 0.3%, 0.5%, 1%, 2%, 3%, 4%, 5%.
  • BaO is an optional component that helps to improve the glass-forming performance of glass. When its content exceeds 5%, the devitrification resistance of glass decreases. Therefore, in the present invention, the BaO content is preferably controlled to 5% or less, more preferably 1% Hereinafter, in some embodiments, it is preferable not to introduce. In some embodiments, BaO may be included at about 0%, greater than 0%, 0.3%, 0.5%, 1%, 2%, 3%, 4%, 5%.
  • TiO 2 is an optional component that helps reduce the melting temperature of glass and improve chemical stability.
  • the introduction of less than 5% in the present invention can make the glass crystallization process easier to control, preferably less than 1%, in In some embodiments, it is preferably not introduced. In some embodiments, it may comprise from about 0%, more than 0%, 0.3%, 0.5%, 1%, 2%, 3%, 4%, 5% of TiO 2.
  • Y 2 O 3 is an optional component that improves the hardness and chemical stability of the glass, but too much content will easily cause devitrification of the glass, and its content is 5% or less, preferably 1% or less, and in some embodiments, it is preferable Not introduced. In some embodiments, Y 2 O 3 may be included at about 0%, greater than 0%, 0.3%, 0.5%, 1%, 2%, 3%, 4%, 5%.
  • glass-ceramic products may preferably contain 5% or less of Na 2 O, more preferably 3% or less of Na 2 O, further preferably 1% or less of Na 2 O; in glass and The crystallized glass may preferably contain 3% or less of Na 2 O, more preferably 1% or less of Na 2 O, and in some embodiments, preferably does not contain Na 2 O.
  • it may comprise about 0%, greater than 0%, 0.1%, 0.2%, 0.3%, 0.4%, 0.5%, 0.6%, 0.7%, 0.8%, 0.9%, 1.0%, 1.1%, 1.2 %, 1.3%, 1.4%, 1.5%, 1.6%, 1.7%, 1.8%, 1.9%, 2.0%, 2.1%, 2.2%, 2.3%, 2.4%, 2.5%, 2.6%, 2.7%, 2.8%, 2.9%, 3.0%, 3.1%, 3.2%, 3.3%, 3.4%, 3.5%, 3.6%, 3.7%, 3.8%, 3.9%, 4.0%, 4.1%. 4.2%, 4.3%, 4.4%, 4.5%, 4.6%, 4.7%, 4.8%, 4.9%, 5.0% Na 2 O.
  • B 2 O 3 helps to provide glass with a low melting temperature.
  • the B 2 O 3 content is 3% or less, and in some embodiments, preferably 0.1 to 2%
  • it may comprise about 0%, greater than 0%, 0.1%, 0.2%, 0.3%, 0.4%, 0.5%, 0.6%, 0.7%, 0.8%, 0.9%, 1.0%, 1.1%, 1.2 %, 1.3%, 1.4%, 1.5%, 1.6%, 1.7%, 1.8%, 1.9%, 2.0%, 2.1%, 2.2%, 2.3%, 2.4%, 2.5%, 2.6%, 2.7%, 2.8%, 2.9%, 3.0% B 2 O 3 .
  • One or several components of Sb 2 O 3 , SnO 2 , SnO, CeO 2 are added as a clarifying agent, and the upper limit of the Sb 2 O 3 content is 2%, preferably 1%, more preferably 0.5%.
  • the upper limit of the content of SnO 2 , SnO, and CeO 2 is 2%, preferably 1%, and more preferably 0.5%.
  • the content of one or more of the above 4 clarifying agents is about 0%, greater than 0%, 0.1%, 0.2%, 0.3%, 0.4%, 0.5%, 0.6%, 0.7% , 0.8%, 0.9%, 1.0%, 1.1%, 1.2%, 1.3%, 1.4%, 1.5%, 1.6%, 1.7%, 1.8%, 1.9%, 2.0%.
  • As 2 O 3 , Cl compounds, Br compounds, etc. may also be used as clarifiers, the contents of which are 2% or less, preferably 1% or less, and more preferably 0.5% or less.
  • the present invention does not contain PbO and As 2 O 3 in some embodiments.
  • the main crystal phases in glass-ceramics and glass-ceramic products include lithium silicate and quartz crystal phases, and lithium silicate is divided into lithium disilicate (Li 2 Si 2 O 5 ) and metasilicate Lithium (Li 2 SiO 3 ), in some embodiments, it is preferred to use lithium disilicate and quartz crystal phases and / or lithium-permeable feldspar as the main crystal phases, and in some embodiments, lithium disilicate and quartz crystal phases are preferred As the main crystal phase, in some preferred embodiments, lithium disilicate and ⁇ -quartz crystal phase are used as the main crystal phases, so as to obtain relatively excellent performance in the present invention.
  • the glass-ceramic of the present invention provides excellent mechanical properties for the glass-ceramic of the present invention, and can also be ion-exchanged to obtain additional mechanical strength.
  • the glass-ceramics and glass-ceramic products of the present invention can obtain a suitable crystal grain size; at the same time, the glass-ceramics and glass-ceramic products of the present invention have good crystallinity, which Crystal glass and glass ceramic products have excellent mechanical properties.
  • the crystallinity referred to in this article refers to the completeness of the crystal.
  • the arrangement of the particles within the crystal is relatively regular.
  • the diffraction lines are strong, sharp and symmetrical.
  • the half-height width of the diffraction peak is close to the width measured by the instrument; crystal crystals with poor crystallinity There are defects such as dislocations, which make the diffraction peak shape wide and diffuse. The worse the crystallinity, the weaker the diffraction ability and the wider the diffraction peak until it disappears into the background.
  • the crystallite size and haze of the glass-ceramic or glass-ceramic product of the present invention will affect the transparency of the glass-ceramic or glass-ceramic product, that is, the light transmittance, the smaller the crystal grain, the higher the transparency, the smaller the haze, and the transparency The higher.
  • the haze with a thickness of 0.55 mm is 0.6% or less, preferably 0.5% or less, and more preferably 0.4% or less.
  • the crystal grain size is 100 nm or less, preferably 80 nm or less, more preferably 60 nm or less, further preferably 50 nm or less, still more preferably 40 nm or less.
  • the glass-ceramic or glass-ceramic article exhibits high transparency in the visible range (ie, the glass-ceramic or glass-ceramic article is transparent).
  • the average light transmittance of 400 mm to 800 nm in a thickness of 1 mm is 80% or more, preferably 85% or more, and more preferably 88% or more.
  • the light transmittance of 0.55 mm thickness 550 nm is 80% or more, preferably 85% or more, more preferably 88% or more, and still more preferably 91% or more.
  • antimicrobial ingredients can be added to glass, glass-ceramics, or glass-ceramic articles.
  • the glass composition, glass-ceramics and glass-ceramic products of the present invention can be produced and manufactured by the following methods:
  • Produce glass composition mix the raw materials uniformly according to the composition ratio range, put the homogeneous mixture into a crucible made of platinum or quartz, according to the melting difficulty of the glass composition, in an electric furnace or gas furnace at 1250 ⁇ 1650 °C Melt within 5 to 24 hours in the temperature range, stir to make it uniform, then drop to the proper temperature and cast into the mold, then cool slowly.
  • the glass composition of the present invention can be molded by a well-known method.
  • the refractive index (nd) of the glass composition of the present invention is 1.500 to 1.530, preferably 1.510 to 1.525.
  • the glass composition of the present invention is subjected to crystallization treatment by a crystallization process after molding or after molding processing, and crystals are uniformly precipitated inside the glass.
  • This crystallization process may be performed in one stage or two stages, but it is preferable to perform the crystallization process in two stages.
  • the nucleation process is performed at the first temperature, and then the crystal growth process is performed at the second temperature that is higher than the nucleation process temperature.
  • the crystallization treatment performed at the first temperature is referred to as the first crystallization treatment
  • the crystallization treatment performed at the second temperature is referred to as the second crystallization treatment.
  • the preferred crystallization process is:
  • the nucleation process and the crystal growth process can be continuously performed. That is, the temperature is raised to a predetermined crystallization treatment temperature, and after reaching the heat treatment temperature, the temperature is maintained for a certain period of time, and then the temperature is lowered.
  • the temperature of the crystallization treatment is preferably from 490 to 800 ° C. In order to be able to precipitate the desired crystal phase, it is more preferably from 550 to 750 ° C.
  • the retention time at the crystallization treatment temperature is preferably from 0 to 8 hours, more preferably For 1 to 6 hours.
  • the first temperature is preferably 490 to 650 ° C
  • the second temperature is preferably 600 to 850 ° C.
  • the holding time at the first temperature is preferably 0 to 24 hours, and more preferably 2 to 15 hours.
  • the holding time at the second temperature is preferably 0 to 10 hours, and more preferably 0.5 to 6 hours.
  • the above holding time of 0 hours means that the temperature starts to decrease or increase again less than 1 minute after reaching its temperature.
  • the refractive index (nd) of the crystallized glass obtained by the crystallization process of the present invention is 1.520 ⁇ 1.550, preferably 1.530 ⁇ 1.545.
  • the glass compositions or glass-ceramics described herein can be manufactured into shaped bodies by various processes, including but not limited to sheets, and the processes include but are not limited to slot drawing , Float, rolling and other sheet forming processes known in the art.
  • the glass composition or glass-ceramics can be formed by a float method or a rolling method known in the art.
  • the glass composition or glass-ceramic of the present invention may be manufactured by a method such as grinding or polishing, and the method of manufacturing a glass shaped body of a sheet, but the method of manufacturing a glass shaped body is not limited to these methods.
  • the glass or glass-ceramic molded body of the present invention can be prepared by a method such as hot bending or pressing at a certain temperature to form various shapes, and is not limited to these methods.
  • the glass compositions, glass-ceramics, and glass-ceramic products described in the present invention can have any thickness that is reasonably useful.
  • the glass-ceramic of the present invention can also be formed into a glass-ceramic product by forming a compressive stress layer to obtain higher strength.
  • the glass composition or glass-ceramic can be processed into a sheet, and / or shaped (such as punching, hot bending, etc.), polished and / or swept after shaping, and then chemically tempered by a chemical tempering process Tempering.
  • the chemical tempering described in the present invention is the ion exchange method. Both the glass and the crystallized glass of the present invention can be ion-exchanged by a method known in the art. During the ion exchange process, the smaller metal ions in the glass or crystallized glass are replaced or "exchanged" by larger metal ions with the same valence state close to the glass or crystallized glass. Replace the smaller ions with larger ions to build a compressive stress in the glass or glass-ceramic to form a compressive stress layer.
  • the metal ion is a monovalent alkali metal ion (e.g., Na + , K + , Rb + , Cs +, etc.), and the ion exchange is performed by immersing the glass or glass-ceramic in at least one containing larger metal ions The molten salt is carried out in a salt bath, and the larger metal ion is used to replace the smaller metal ion in the glass.
  • a monovalent metal ions such as Ag + , Tl + , Cu +, etc. can also be used to exchange monovalent ions.
  • One or more ion exchange processes used to chemically toughen glass or glass-ceramics can include, but are not limited to: immersion in a single salt bath, or immersion in multiple salt baths with the same or different compositions There are washing and / or annealing steps between immersion.
  • the glass or glass-ceramic can be ion-exchanged for about 6 to 20 hours in a salt bath of molten Na salt (eg, NaNO 3 ) immersed at a temperature of about 430 ° C to 470 ° C, preferably a temperature range It is 435 ° C to 460 ° C, and the preferred time range is 8 to 13 hours.
  • Na ions replace part of Li ions in the glass or glass-ceramic, thereby forming a surface compression layer and exhibiting high mechanical properties.
  • the glass or glass-ceramic can be implemented by submerging in a salt bath that can melt K salt (such as KNO 3 ) at a temperature of about 400 ° C. to 450 ° C. for 1 to 8 hours. For ion exchange, the preferred time range is 2 to 4 hours.
  • the depth of the ion-exchange layer reaches 80 ⁇ m or more, preferably 85 ⁇ m or more by passing in a salt bath of molten Na salt (such as NaNO 3 ) at 450 ° C. for about 8 hours.
  • molten Na salt such as NaNO 3
  • an ion implantation method for implanting ions into the surface layer of glass or glass-ceramics there are an ion implantation method for implanting ions into the surface layer of glass or glass-ceramics, and a thermal tempering method of heating the glass or glass-ceramics and then rapidly cooling them.
  • the coefficient of thermal expansion ( ⁇ 20 °C -120 °C ) is tested according to the GB / T7962.16-2010 test method.
  • the refractive index (nd) is tested according to the method of GB / T7962.1-2010.
  • a haze tester EEL57D was used, prepared with 0.55mm thick glass samples, and tested with GB2410-80 as the standard.
  • the SEM scanning electron microscope was used for the measurement.
  • the glass-ceramics were subjected to surface treatment in HF acid, and then the surface of the glass-ceramics was sprayed with gold.
  • the surface was scanned under the SEM scanning electron microscope to determine the size of the crystal grains.
  • the sample was processed to a thickness of 1 mm and polished on the opposite surface in parallel, and the average light transmittance of 400 to 800 nm was measured with a Hitachi U-41000 spectrophotometer.
  • the sample was processed to a thickness of 0.55 mm and polished on the opposite surface in parallel, and the light transmittance at 550 nm was measured using a Hitachi U-41000 spectrophotometer.
  • the temperature coefficient of the refractive index is tested according to the method specified in GB / T 7962.4-2010, and the temperature coefficient of the refractive index of 20-40 ° C is determined.
  • the XRD diffraction peak is compared with the database pattern, the crystallinity is obtained by calculating the proportion of the crystalline phase diffraction intensity in the overall pattern intensity, and is internally calibrated by using pure quartz crystals.
  • the depth of the ion exchange layer was measured using the glass surface stress meter SLP-2000.
  • the refractive index of the sample was 1.54 and the optical elastic constant was 25.3 [(nm / cm) / Mpa].
  • the 132g steel ball is dropped from the specified height, and the maximum drop test height of the impact that the sample can withstand without breaking. Specifically, the test is carried out from the ball drop test height of 650 mm, and without breaking, the height is sequentially changed by 700 mm, 750 mm, 800 mm, 850 mm, and 900 mm and above.
  • the glass-ceramic product is the test object.
  • the test data recorded as 900 mm in the examples indicates that even if the steel ball is dropped from a height of 900 mm, the glass-ceramic product does not break and receives an impact.
  • the sample size is 2mm ⁇ 4mm ⁇ 20mm, after chamfering, grinding and polishing, after the sample preparation is completed, use a Vickers hardness indenter to add 49N to the sample and Maintain the time of 30s, after making the indentation, measure the breaking strength by three-point bending method.
  • the computer-controlled electronic universal testing machine CMT6502 is used, the glass size is 150 ⁇ 57 ⁇ 0.55mm, and the test is conducted in accordance with ASTM 158-2002.
  • the glass composition of the present invention has the following properties:
  • the coefficient of thermal expansion ( ⁇ 20 ° C-120 ° C ) is 45 ⁇ 10 -7 / K to 70 ⁇ 10 -7 / K, preferably 50 ⁇ 10 -7 / K to 70 ⁇ 10 -7 / K.
  • the refractive index (nd) is 1.500 to 1.530, preferably 1.510 to 1.525.
  • the glass-ceramic of the present invention has the following properties:
  • the haze with a thickness of 0.55 mm is 0.6% or less, preferably 0.5% or less, and more preferably 0.4% or less.
  • the crystal grain size is 100 nm or less, preferably 80 nm or less, more preferably 60 nm or less, further preferably 50 nm or less, still more preferably 40 nm or less.
  • the glass-ceramic of the present invention has a refractive index temperature coefficient of -0.5 ⁇ 10 -6 / ° C or lower, preferably -0.8 ⁇ 10 -6 / ° C or lower, more preferably -1.1 ⁇ 10 -6 / ° C or lower .
  • the crystallinity is 50% or more, preferably 65% or more, more preferably 70% or more, and still more preferably 75% or more.
  • the refractive index (nd) is 1.520 to 1.550, preferably 1.530 to 1.545.
  • the average light transmittance of 1 mm thickness 400-800 nm is 80% or more, preferably 85% or more, and more preferably 88% or more.
  • the light transmittance of 0.55 mm thickness 550 nm is 80% or more, preferably 85% or more, more preferably 88% or more, and still more preferably 91% or more.
  • the glass-ceramic product of the present invention has the following properties in addition to the above-mentioned glass-ceramic properties:
  • the surface stress is 200 MPa or more, preferably 250 MPa or more, and more preferably 300 MPa or more;
  • the four-point bending strength is 600 MPa or more, preferably 650 MPa or more, and more preferably 700 MPa or more;
  • the depth of the ion exchange layer is 30 ⁇ m or more, preferably 50 ⁇ m or more, more preferably 60 ⁇ m or more, further preferably 80 ⁇ m or more;
  • the height of the ball drop test is 700 mm or more, preferably 800 mm or more, more preferably 1000 mm or more, further preferably 1200 mm or more;
  • the fracture toughness is 1 MPa ⁇ m 1/2 or more, preferably 1.3 MPa ⁇ m 1/2 or more, and more preferably 1.5 MPa ⁇ m 1/2 or more.
  • the average light transmittance of 1 mm thickness 400-800 nm is 80% or more, preferably 85% or more, and more preferably 88% or more.
  • the light transmittance of 0.55 mm thickness 550 nm is 80% or more, preferably 85% or more, more preferably 88% or more, and still more preferably 91% or more.
  • the glass-ceramics and glass-ceramic products of the present invention can be widely made into glass cover plates or glass components due to the above-mentioned excellent properties; at the same time, the glass-ceramics, glass-ceramic products of the present invention, and the manufactured glass covers Board or glass components can also be used in electronic devices or display devices, such as mobile phones, watches, computers, touch screens, etc.

Abstract

一种电子设备盖板用微晶玻璃制品和微晶玻璃，该微晶玻璃的主要晶相含有硅酸锂和石英晶相，其组成按重量百分比表示，含有：SiO 2：65～85％、Al 2O 3：1～15％、Li 2O：5～15％、ZrO 2：0.1～10％、P 2O 5：0.1～10％、K 2O：0～10％、MgO：0～10％、ZnO：0～10％、Na 2O：0～5％，其中(SiO 2+Al 2O 3+Li 2O+ZrO 2)/P 2O 5为40～90，落球试验高度为700mm以上。该微晶玻璃和微晶玻璃制品具有优异的机械性能，以较低的成本获得了适用于电子设备的微晶玻璃或微晶玻璃制品。

Description

电子设备盖板用微晶玻璃制品和微晶玻璃 技术领域
本发明涉及一种微晶玻璃制品和微晶玻璃，尤其是涉及一种电子设备盖板用微晶玻璃制品、微晶玻璃、电子设备用玻璃盖板和电子设备。
背景技术
电子设备由于其内部具有许多精密的电子元器件，因此需要设置盖板或者外壳对内部的电子元器件加以保护。现有文献中公开的内容中，多用金属作为盖板材料，但金属存在着易氧化、对电磁信号有屏蔽等缺点；也有文献中公开采用玻璃作为盖板使用的，例如中国专利CN101508524A公开了一种化学强化玻璃，其抗跌落性能和断裂韧性等性能难以满足要求。
微晶玻璃是一种通过对玻璃进行热处理而在玻璃内部析出结晶的材料。微晶玻璃通过在内部分散的结晶，能够具备在玻璃中无法得到的物性值。例如，对于杨氏模量、断裂韧性等机械强度，对酸性或碱性药液的蚀刻特性，热膨胀系数等热性能，玻璃化转变温度的上升以及消失等。微晶玻璃具有更高的机械性能，并且由于在玻璃中形成微晶，其抗弯、耐磨性能等相对于一般的玻璃都有明显的优势。
基于以上因素，本发明人以期通过大量实验研究，研发出具有优异机械性能的微晶玻璃，适用于电子设备。
发明内容
本发明所要解决的技术问题是提供一种电子设备盖板用微晶玻璃制品，其具有优异的机械性能。
本发明解决技术问题所采用的技术方案是：
(1)电子设备盖板用微晶玻璃制品，其主要晶相含有硅酸锂和石英晶相，其组成按重量百分比表示，含有：SiO 2：65～85％、Al 2O 3：1～15％、Li 2O：5～15％、ZrO 2：0.1～10％、P 2O 5：0.1～10％、K 2O：0～10％、MgO：0～10％、ZnO：0～10％、Na 2O：0～5％，其中(SiO 2+Al 2O 3+Li 2O+ZrO 2)/P 2O 5为40～90，落球试验高度为700mm以上。
(2)电子设备盖板用微晶玻璃制品，其组成按重量百分比表示，含有：SiO 2：65～85％、Al 2O 3：1～15％、Li 2O：5～15％、ZrO 2：0.1～10％、P 2O 5：0.1～10％、K 2O：0～10％、MgO：0～10％、ZnO：0～10％、Na 2O：0～5％。
(3)根据(1)～(2)任一所述的电子设备盖板用微晶玻璃制品，其组成按重量百分比表示，还含有：SrO：0～5％、BaO：0～5％、TiO 2：0～5％、Y 2O 3：0～5％、B 2O 3：0～3％、澄清剂：0～2％。
(4)根据(1)～(3)任一所述的电子设备盖板用微晶玻璃制品，其中：(SiO 2+Li 2O)/Al 2O 3为6～15、(Al 2O 3+Li 2O)/P 2O 5为5～20、(SiO 2+Li 2O)/P 2O 5为40～80、(K 2O+MgO)/ZrO 2为0.6～1.2、或Li 2O/(K 2O+ZrO 2)为2.3～4.0。
(5)根据(1)～(4)任一所述的电子设备盖板用微晶玻璃制品，其中：(SiO 2+Li 2O)/Al 2O 3为8～13、(Al 2O 3+Li 2O)/P 2O 5为6～14、(SiO 2+Li 2O)/P 2O 5为40～70、(SiO 2+Al 2O 3+Li 2O+ZrO 2)/P 2O 5为45～85、 (K 2O+MgO)/ZrO 2为0.7～1.1、和Li 2O/(K 2O+ZrO 2)为2.5～3.5。
(6)根据(1)～(5)任一所述的电子设备盖板用微晶玻璃制品，其组成按重量百分比表示，含有：SiO 2：70～76％、Al 2O 3：4～10％、Li 2O：8～12.5％、ZrO 2：1～5％、P 2O 5：1～3％、K 2O：0～3％、MgO：0.3～2％、ZnO：0～3％、Na 2O：0～1％、Sb 2O 3：0～1％、SnO 2：0～1％、SnO：0～1％、或CeO 2：0～1％。
(7)根据(1)～(6)任一所述的电子设备盖板用微晶玻璃制品，其中：(Al 2O 3+Li 2O)/P 2O 5为8.5～14、(SiO 2+Li 2O)/P 2O 5为45～60、(SiO 2+Al 2O 3+Li 2O+ZrO 2)/P 2O 5为48～80、或(SiO 2+Li 2O)/Al 2O 3为8.5～12。
(8)根据(1)～(7)任一所述的电子设备盖板用微晶玻璃制品，其中：(K 2O+MgO)/ZrO 2为0.8～1.0、或Li 2O/(K 2O+ZrO 2)为2.8～3.3。
(9)根据(1)～(8)任一所述的电子设备盖板用微晶玻璃制品，其组成按重量百分比表示，含有：Li 2O：8～小于10％、不含有SrO、不含有BaO、不含有TiO 2、不含有Y 2O 3、不含有GeO 2、不含有CaO、不含有Cs 2O、不含有PbO、不含有B 2O 3、不含有As 2O 3、不含有La 2O 3、和不含有Tb 2O 3。
(10)根据(1)～(9)任一所述的电子设备盖板用微晶玻璃制品，结晶度为70％以上。
(11)根据(1)～(10)任一所述的电子设备盖板用微晶玻璃制品，落球试验高度为1000mm以上；或四点弯曲强度为650MPa以上； 或0.55mm厚度的雾度为0.5％以下；或折射率温度系数为-0.8×10 -6/℃以下；或0.55mm厚550nm波长的光透射率为88％以上。
本发明还提供一种微晶玻璃，其具有优异的机械性能。
本发明解决技术问题所采用的技术方案是：
(12)微晶玻璃，其主要晶相含有硅酸锂和石英晶相，其组成按重量百分比表示为：SiO 2：65～85％、Al 2O 3：1～15％、Li 2O：5～15％、ZrO 2：0.1～10％、P 2O 5：0.1～10％、K 2O：0～10％、MgO：0～10％、ZnO：0～10％、Na 2O：0～3％，Sb 2O 3：0～1％、SnO 2：0～1％、SnO：0～1％、CeO 2：0～1％，其中(SiO 2+Al 2O 3+Li 2O+ZrO 2)/P 2O 5为40～90，(K 2O+MgO)/ZrO 2为0.6～1.2，0.55mm厚度的雾度为0.5％以下。
(13)微晶玻璃，其主要晶相含有硅酸锂和石英晶相，其组成按重量百分比表示，含有：SiO 2：65～85％、Al 2O 3：1～15％、Li 2O：5～15％、ZrO 2：0.1～10％、P 2O 5：0.1～10％、K 2O：0～10％、MgO：0～10％、ZnO：0～10％，其中(SiO 2+Al 2O 3+Li 2O+ZrO 2)/P 2O 5为40～90。
(14)微晶玻璃，其组成按重量百分比表示，含有：SiO 2：65～85％、Al 2O 3：1～15％、Li 2O：5～15％、ZrO 2：0.1～10％、P 2O 5：0.1～10％、K 2O：0～10％、MgO：0～10％、ZnO：0～10％。
(15)根据(12)～(14)任一所述的微晶玻璃，其特征在于，其中：(SiO 2+Al 2O 3+Li 2O+ZrO 2)/P 2O 5为45～85、(SiO 2+Li 2O)/Al 2O 3为8～13、(Al 2O 3+Li 2O)/P 2O 5为6～14、(SiO 2+Li 2O)/P 2O 5为40～70、或Li 2O/(K 2O+ZrO 2)为2.5～3.5。
(16)根据(12)～(15)任一所述的微晶玻璃，其中SiO 2：70～ 76％、Al 2O 3：4～10％、Li 2O：8～12.5％、ZrO 2：1～5％、P 2O 5：1～3％、K 2O：0～3％、MgO：0.3～2％、ZnO：0～3％、Na 2O：0～1％。
(17)根据(12)～(16)任一所述的微晶玻璃，其中：(K 2O+MgO)/ZrO 2为0.8～1.0、或Li 2O/(K 2O+ZrO 2)为2.8～3.3。
(18)根据(12)～(17)任一所述的微晶玻璃，结晶度为70％以上；或晶粒尺寸为80nm以下；或折射率温度系数为-0.8×10 -6/℃以下；或1mm厚400～800nm波长的平均光透射率为85％以上。
本发明还提供一种电子设备用玻璃盖板：
(19)电子设备用玻璃盖板，含有(1)～(11)任一所述的电子设备盖板用微晶玻璃制品，或(12)～(18)任一所述的微晶玻璃。
本发明还提供一种电子设备：
(20)电子设备，含有(1)～(11)任一所述的电子设备盖板用微晶玻璃制品，或(12)～(18)任一所述的微晶玻璃，或(19)所述的电子设备用玻璃盖板。
本发明的有益效果是：通过合理的组分设计，使得本发明微晶玻璃和微晶玻璃制品具有优异的机械性能，适用于电子设备。
具体实施方式
本文以下内容中将电子设备盖板用微晶玻璃制品简称为“微晶玻璃制品”。
本发明的微晶玻璃和微晶玻璃制品是具有晶相和玻璃相的材料，其有别于非晶质固体。微晶玻璃和微晶玻璃制品的晶相可以通过X射线衍射分析的X射线衍射图案中出现的峰值角度以及通过TEMEDX进行 辨别，主要晶相由X射线衍射测得。
本发明的发明人经过反复试验和研究，对于构成微晶玻璃和微晶玻璃制品的特定成分，通过将其含量以及含量比例规定为特定值并使其析出特定的晶相，以较低的成本得到了本发明的微晶玻璃或微晶玻璃制品。
下面，对本发明玻璃组合物、微晶玻璃或微晶玻璃制品的各成分的组成范围进行说明。在本说明书中，如果没有特殊说明，各组分的含量全部采用相对于换算成氧化物的组成的玻璃物质总量的重量百分比表示。在这里，所述“换算成氧化物的组成”是指，作为本发明的玻璃组合物、微晶玻璃或微晶玻璃制品组成成分的原料而使用的氧化物、复合盐及氢氧化物等熔融时分解并转变为氧化物的情况下，将该氧化物的物质总量作为100％。此外，在本说明书中仅称为玻璃时为结晶化前的玻璃组合物，玻璃组合物结晶化后称为微晶玻璃，微晶玻璃制品是指经化学钢化后的微晶玻璃。
除非在具体情况下另外指出，本文所列出的数值范围包括上限和下限值，“以上”和“以下”包括端点值，在该范围内的所有整数和分数，而不限于所限定范围时所列的具体值。本文所使用的术语“约”指配方、参数和其他数量以及特征不是、且无需是精确的，如有需要，可以近似和/或更大或更低，这反映公差、换算因子和测量误差等。本文所称“和/或”是包含性的，例如“A和/或B”，是指只有A，或者只有B，或者同时有A和B。
本发明所述的玻璃、微晶玻璃和微晶玻璃制品可以概括的描述为 含锂的铝硅酸盐玻璃、微晶玻璃及微晶玻璃制品，包含SiO 2、Al 2O 3、和Li 2O，除此之外，还包括ZrO 2、P 2O 5等其他成分。在一些实施方式中，取决于玻璃的组成，微晶玻璃和微晶玻璃制品的第一主要晶相是硅酸锂；在一些实施方式中，第一主要晶相是透锂长石；在一些实施方式中，第一主要晶相是石英晶相(包括石英、石英及石英固溶体两种情况)。在一些实施方式中，主要晶相包括硅酸锂和石英晶相。在一些实施方式中，主要晶相包括硅酸锂和透锂长石。在一些实施方式中，第一晶相是硅酸锂，第二主要晶相是石英晶相；在一些实施方式中，第一晶相是石英晶相，第二主要晶相是硅酸锂；在一些实施方式中，第一晶相是硅酸锂，第二主要晶相是透锂长石；在一些实施方式中，第一晶相是透锂长石，第二主要晶相是硅酸锂。在一些实施方式中，主要晶相包括硅酸锂、透锂长石和石英晶相；在一些实施方式中，第一晶相是硅酸锂，第二主要晶相是透锂长石，第三主要晶相是石英晶相；在一些实施方式中，第一晶相是硅酸锂，第二主要晶相是石英晶相，第三主要晶相是透锂长石；在一些实施方式中，第一主要晶相是透锂长石，第二主要晶相是硅酸锂，第三主要晶相是石英晶相；在一些实施方式中，第一晶相是石英晶相，第二主要晶相是硅酸锂，第三主要晶相是透锂长石。在一些实施方式中，石英晶相为α-六方石英晶相；在一些实施方式中，硅酸锂为二硅酸锂；也可存在作为次要晶相的β-锂辉石ss、磷酸锂等。需要说明的是，本文所称的石英晶相包括仅含石英晶体、含有石英及石英固溶体两种情况。
在一些实施方式中，微晶玻璃及微晶玻璃制品中残留的玻璃相重 量百分含量为8～45％；在一些实施方式中，为10～40％；在一些实施方式中，为12～40％；在一些实施方式中，为15～40％；在一些实施方式中，为15～35％；在一些实施方式中，为15～32％；在一些实施方式中，为20～45％；在一些实施方式中，为20～40％；在一些实施方式中，为32～45％；在一些实施方式中，为32～40％；在一些实施方式中，为35～45％。
微晶玻璃主要晶相为石英晶相、硅酸锂及透锂长石其中之一或其组合时，微晶玻璃断裂韧性变高。微晶玻璃主要晶相为石英晶相、二硅酸锂时，微晶玻璃的折射率温度系数变低，断裂韧性变高；微晶玻璃制品的落球试验高度变大、四点弯曲强度变大。
本发明中主晶相占微晶玻璃或微晶玻璃制品的重量百分数达到50～92％；在一些实施方式中，重量百分数达到60～90％；在一些实施方式中，重量百分数达到65～85％；在一些实施方式中，重量百分数达到70～80％；在一些实施方式中，重量百分数达到80～92％。本文所称主晶相，是指具有比在微晶玻璃或微晶玻璃制品中存在的其它晶相更高重量百分数的晶相。
在一些实施方式中，微晶玻璃或微晶玻璃制品的石英晶相重量百分数在70％以下；在一些实施方式中，微晶玻璃或微晶玻璃制品的石英晶相重量百分数在65％以下；在一些实施方式中，微晶玻璃或微晶玻璃制品的石英晶相重量百分数在60％以下；在一些实施方式中，微晶玻璃或微晶玻璃制品的石英晶相重量百分数在55％以下；在一些实施方式中，微晶玻璃或微晶玻璃制品的石英晶相重量百分数在50％以 下；在一些实施方式中，微晶玻璃或微晶玻璃制品的石英晶相重量百分数在45％以下。
在一些实施方式中，微晶玻璃或微晶玻璃制品的硅酸锂晶相重量百分数在55％以下；在一些实施方式中，微晶玻璃或微晶玻璃制品的硅酸锂晶相重量百分数在50％以下；在一些实施方式中，微晶玻璃或微晶玻璃制品的硅酸锂晶相重量百分数在45％以下；在一些实施方式中，微晶玻璃或微晶玻璃制品的硅酸锂晶相重量百分数在40％以下。
在一些实施方式中，微晶玻璃或微晶玻璃制品的透锂长石晶相重量百分数在40％以下；在一些实施方式中，微晶玻璃或微晶玻璃制品的透锂长石晶相重量百分数在35％以下；在一些实施方式中，微晶玻璃或微晶玻璃制品的透锂长石晶相重量百分数在30％以下；在一些实施方式中，微晶玻璃或微晶玻璃制品的透锂长石晶相重量百分数在25％以下；在一些实施方式中，微晶玻璃或微晶玻璃制品的透锂长石晶相重量百分数小于20％；在一些实施方式中，微晶玻璃或微晶玻璃制品的透锂长石晶相重量百分数在15％以下。
SiO 2是本发明的玻璃组合物的基础成分，可用于稳定玻璃和微晶玻璃网络结构，其是结晶化后形成硅酸锂、石英晶相和透锂长石的成分之一，如果SiO 2的含量在65％以下，在微晶玻璃中形成晶体会变少并且晶体容易变粗，影响微晶玻璃和微晶玻璃制品的雾度，以及微晶玻璃制品的落球试验高度等性能，因此，SiO 2含量的下限优选为65％，优选为70％；如果SiO 2含量在85％以上，玻璃熔化温度高，化料困难，并且不容易成型，影响玻璃的一致性，因此，SiO 2含量的上限优选为 85％，优选为80％，进一步优选为76％。在一些实施方式中，可包含约66％、67％、68％、69％、70％、71％、72％、73％、74％、75％、76％、77％、78％、79％、80％、81％、82％、83％、84％的SiO 2。
Al 2O 3是形成玻璃网状结构的组分，其是有助于稳定玻璃成型、提高化学稳定性的重要成分，还可改善玻璃的机械性能，增加微晶玻璃制品离子交换层深度和表面应力，但如果其含量不足1％，则效果不佳，因此，Al 2O 3含量的下限为1％，优选为4％。另一方面，如果Al 2O 3的含量超过15％，则玻璃的熔融性与耐失透性降低，并且晶化时晶体容易增大，降低微晶玻璃和微晶玻璃制品的强度，因此，Al 2O 3含量的上限为15％，优选为12％，更优选为10％。在一些实施方式中，可包含约1％、2％、3％、4％、5％、6％、7％、8％、9％、10％、11％、12％、13％、14％、15％的Al 2O 3。
Li 2O是通过晶化后成为晶相组成的必要成分，有助于形成硅酸锂和透锂长石等含锂晶相，也是化学强化必要成分。但如果其含量不足5％，则效果不佳，因此，Li 2O含量的下限为5％，优选为7％，更优选8％，在一些实施方式中，进一步优选为9％；另一方面，如果过多地含有Li 2O，则很容易使玻璃的化学稳定性降低，且会使微晶玻璃和微晶玻璃制品的光透射率劣化，因此，Li 2O含量的上限优选为15％，更优选为12.5％，在一些实施方式中，进一步优选为小于10％。在一些实施方式中，可包含约5％、6％、7％、8％、9％、9.8％、10％、11％、12％、13％、14％、15％的Li 2O。
本发明人大量实验研究发现，通过控制SiO 2、Li 2O和Al 2O 3以一定 的比例引入，可影响玻璃的热膨胀系数、微晶玻璃和微晶玻璃制品的雾度和晶粒大小，尤其是(SiO 2+Li 2O)/Al 2O 3为6～15的范围内时，可使玻璃具有较低的热膨胀系数，并在晶化后获得较小的晶粒，提高微晶玻璃和微晶玻璃制品的机械强度，在一些实施方式中，优选(SiO 2+Li 2O)/Al 2O 3为8～13，更优选为8～12.5，还可获得较低的雾度，使微晶玻璃及微晶玻璃制品具有优异的光透射率；进一步优选(SiO 2+Li 2O)/Al 2O 3为8.5～12，效果尤其明显。在一些实施方式中，(SiO 2+Li 2O)/Al 2O 3的值可为6、6.5、7、7.5、8、8.5、9、9.5、10、10.5、11、11.5、12、12.5、13、13.5、14、14.5、15。
P 2O 5是有助于提高玻璃的低温熔化性的可选成分，能够在玻璃中进行分相形成晶核，提高玻璃在晶化过程中的热膨胀稳定性，P 2O 5含量的下限优选为0.1，更优选为0.5％，进一步优选为1％；但如果过多地含有P 2O 5，则很容易使玻璃产生耐失透性降低及玻璃的分相，且玻璃机械性能有劣化的趋势。因此，P 2O 5含量的上限为10％，优选为5％，更优选为3％。在一些实施方式中，可包含约0％，0.1％、0.3％、0.5％、1％、2％、3％、4％、5％、6％、7％、8％、9％、10％的P 2O 5。
本发明中通过控制(SiO 2+Li 2O)/P 2O 5的值在40～80范围内，可优化微晶玻璃制品的离子交换层深度，尤其是(SiO 2+Li 2O)/P 2O 5的值在40～70范围内，更优选(SiO 2+Li 2O)/P 2O 5的值为42～60，进一步优选为45～60，微晶玻璃制品可以获得更深的离子交换层；在一些实施方式中，使(SiO 2+Li 2O)/P 2O 5的值在40～70范围内，更优选(SiO 2+Li 2O)/P 2O 5的值为42～60，进一步优选为45～60内时，晶化过程对形成石英晶相和二 硅酸锂有利，还可使微晶玻璃和微晶玻璃制品具有优异的折射率温度系数，使其可达-0.5×10 -6/℃以下，优选-0.8×10 -6/℃以下，更优选-1.1×10 -6/℃以下，降低微晶玻璃和微晶玻璃制品中玻璃相与各晶相之间因温度差异所带来的折射率变化差异，避免微晶玻璃或微晶玻璃制品因温差变化而使光透射率降低。在一些实施方式中，(SiO 2+Li 2O)/P 2O 5的值可为40、41、42、43、44、45、46、47、48、49、50、51、52、53、54、55、56、57、58、59、60、61、62、63、64、65、66、67、68、69、70。
经发明人大量实验研究发现，Al 2O 3、Li 2O和P 2O 5为在玻璃中的引入比例，对微晶玻璃和微晶玻璃制品的表面应力和四点弯曲强度有重要影响，尤其是(Al 2O 3+Li 2O)/P 2O 5为5～20范围内时，可提高微晶玻璃和微晶玻璃制品的表面应力，优选(Al 2O 3+Li 2O)/P 2O 5为6～14时，在一些实施方式中，更优选(Al 2O 3+Li 2O)/P 2O 5为8～14，进一步优选(Al 2O 3+Li 2O)/P 2O 5为8.5～14，较易形成石英晶相和二硅酸锂，并使微晶玻璃和微晶玻璃制品的四点弯曲强度提升明显，在一些实施方式中，微晶玻璃和微晶玻璃制品的四点弯曲强度为600MPa以上，优选为650MPa以上，更优选为700MPa以上。在一些实施方式中，(Al 2O 3+Li 2O)/P 2O 5的值可为5、5.5、6、6.5、7、7.5、8、8.5、9、9.5、10、10.5、11、11.5、12、12.5、13、13.5、14、14.5、15、15.5、16、16.5、17、17.5、18、18.5、19、19.5、20。
ZrO 2具有结晶析出形成晶核的作用，同时有助于提高玻璃的化学稳定性的可选成分，研究发现，ZrO 2还可通过在形成过程中显著降低 玻璃失透以及降低液相线温度，来提高Li 2O-Al 2O 3-SiO 2-P 2O 5玻璃的稳定性。本发明中ZrO 2含量的下限优选为0.1，更优选为0.5％，进一步优选为1％；但如果过多地含有ZrO 2，则玻璃的耐失透性很容易降低，同时玻璃晶化过程控制难度增加，因此，ZrO 2含量的上限为10％，优选为6％，更优选为5％。在一些实施方式中，可包含约0％、0.1％、0.3％、0.5％、1％、2％、3％、4％、5％、6％、7％、8％、9％、10％的ZrO 2。
在大量实验研究过程中，本发明人发现，通过控制SiO 2、Al 2O 3、Li 2O和ZrO 2的合计含量与P 2O 5引入量的比值(SiO 2+Al 2O 3+Li 2O+ZrO 2)/P 2O 5在40～90范围内，可使微晶玻璃制品经受700mm以上的落球冲击，优选(SiO 2+Al 2O 3+Li 2O+ZrO 2)/P 2O 5为45～85；尤其在一些实施方式中，(SiO 2+Al 2O 3+Li 2O+ZrO 2)/P 2O 5在46～80范围内时，较易形成二硅酸锂和石英晶相，且微晶玻璃制品较易获得优异的断裂韧性，断裂韧性可为1MPa·m 1/2以上，优选为1.3MPa·m 1/2以上，更优选为1.5MPa·m 1/2以上；同时进一步优化落球试验高度的承受能力，进一步优选(SiO 2+Al 2O 3+Li 2O+ZrO 2)/P 2O 5为48～80，落球试验高度为700mm以上，优选为800mm以上，更优选为1000mm以上，进一步优选为1200mm以上。在一些实施方式中，(SiO 2+Al 2O 3+Li 2O+ZrO 2)/P 2O 5可为40、41、42、43、44、45、46、47、48、49、50、51、52、53、54、55、56、57、58、59、60、61、62、63、64、65、66、67、68、69、70、71、72、73、74、75、76、77、78、79、80、81、82、83、84、85、86、87、88、89、90。
K 2O是有助于提高玻璃的低温熔融性与成形性的可选成分，但如 果过多地含有K 2O，则很容易产生玻璃化学稳定性的降低以及平均线膨胀系数的升高。因此，K 2O的含量为0～10％，优选为0～5％，更优选为0～3％。在一些实施方式中，可包含约0％、大于0％、0.1％、0.3％、0.5％、1％、2％、3％、4％、5％、6％、7％、8％、9％、10％的K 2O。
本发明中，当控制Li 2O与K 2O和ZrO 2的合计含量(K 2O+ZrO 2)的引入量比例Li 2O/(K 2O+ZrO 2)为2.3～4.0范围内时，可优化微晶玻璃的晶化性能，使微晶玻璃和微晶玻璃制品具有合适量的结晶度，从而使微晶玻璃及微晶玻璃制品具有优异的性能；优选Li 2O/(K 2O+ZrO 2)为2.5～3.5，更优选为2.8～3.3，微晶玻璃和微晶玻璃制品落球试验高度变大，在一些实施方式中，球试验高度优选为800mm以上，更优选为1000mm以上，进一步优选为1200mm以上。在一些实施方式中，Li 2O/(K 2O+ZrO 2)的值可为2.3、2.4、2.5、2.6、2.7、2.8、2.9、3.0、3.1、3.2、3.3、3.4、3.5、3.6、3.7、3.8、3.9、4.0。
ZnO可提高玻璃的熔化性能，改善玻璃的化学稳定性，晶化时细化晶粒，将ZnO含量的上限控制在10％以下，可以抑制失透性降低，因此，ZnO含量的上限为10％，优选为5％，更优选为3％。在一些实施方式中，可包含约0％、大于0％、0.1％、0.5％、1％、2％、3％、4％、5％、6％、7％、8％、9％、10％的ZnO。
MgO有助于降低玻璃的粘度、成型时抑制玻璃析晶和晶化时细化晶粒，还具有提高低温熔化性的效果，MgO在本发明中是可选成分，优选含量在0.3％以上；但如果MgO含量过高，可能会引起耐失透性下降，在晶化后会得到不理想的晶体，导致微晶玻璃好微晶玻璃制品的 性能下降，因此，MgO含量的上限为10％，优选为5％，更优选为2％。在一些实施方式中，可包含约0％、大于0％、0.5％、1％、2％、3％、4％、5％、6％、7％、8％、9％、10％的MgO。
通过本发明人大量实验研究发现，当控制K 2O和MgO的合计含量K 2O+MgO与ZrO 2的引入量比例(K 2O+MgO)/ZrO 2在0.6～1.2范围内时，可与Li 2O发生协同作用，促使微晶玻璃和微晶玻璃制品具有合适量的结晶度，使微晶玻璃及微晶玻璃制品具有优异的性能；同时研究发现，通过优选控制(K 2O+MgO)/ZrO 2为0.7～1.1，可细化晶粒，并使其光透射率和机械强度更优异，更优选(K 2O+MgO)/ZrO 2为0.8-1.0时，在一些实施方式中，微晶玻璃和微晶玻璃制品四点弯曲强度变大，四点弯曲强度优选为650MPa以上，更优选为700MPa以上。在一些实施方式中，(K 2O+MgO)/ZrO 2可为0.6、0.65、0.7、0.75、0.8、0.85、0.9、0.95、1.0、1.05、1.1、1.15、1.2。
SrO是提高玻璃的低温熔化性和抑制成型析晶的可选成分，本发明中优选控制SrO在5％以下，可以使微晶玻璃和微晶玻璃制品较易获得优异的晶粒大小，优选其含量在1％以下，在一些实施方式中，优选为不引入。在一些实施方式中，可包含约0％、大于0％、0.3％、0.5％、1％、2％、3％、4％、5％的SrO。
BaO是有助于提高玻璃的成玻性能的可选成分，当其含量超过5％时，玻璃的耐失透性降低，因此本发明中BaO含量优选控制在5％以下，更优选为1％以下，在一些实施方式中，优选不引入。在一些实施方式中，可包含约0％、大于0％、0.3％、0.5％、1％、2％、3％、4％、5％的BaO。
TiO 2是一种有助于降低玻璃的熔化温度、提高化学稳定性的可选成分，本发明中引入5％以下的，可以使玻璃晶化过程变得容易控制，优选为1％以下，在一些实施方式中，优选不引入。在一些实施方式中，可包含约0％、大于0％、0.3％、0.5％、1％、2％、3％、4％、5％的TiO 2。
Y 2O 3是提高玻璃的硬度、化学稳定性的可选成分，但其含量过多则容易引起玻璃析晶，其含量为5％以下，优选为1％以下，在一些实施方式中，优选不引入。在一些实施方式中，可包含约0％、大于0％、0.3％、0.5％、1％、2％、3％、4％、5％的Y 2O 3。
Na 2O是提高玻璃的熔融性的任意成分，如果含量高，则容易引起为了在晶化过程中析出晶相增大或析出结晶相变化，因此，可在不会有损本发明微晶玻璃和微晶玻璃制品性能的情况下，在微晶玻璃制品中可优选含有5％以下的Na 2O，更优选3％以下的Na 2O，进一步优选1％以下的Na 2O；在玻璃和微晶玻璃中可优选含有3％以下的Na 2O，更优选1％以下的Na 2O，在一些实施方式中，优选为不含有Na 2O。在一些实施方式中，可包含约0％、大于0％、0.1％、0.2％、0.3％、0.4％、0.5％、0.6％、0.7％、0.8％、0.9％、1.0％、1.1％、1.2％、1.3％、1.4％、1.5％、1.6％、1.7％、1.8％、1.9％、2.0％、2.1％、2.2％、2.3％、2.4％、2.5％、2.6％、2.7％、2.8％、2.9％、3.0％、3.1％、3.2％、3.3％、3.4％、3.5％、3.6％、3.7％、3.8％、3.9％、4.0％、4.1％。4.2％、4.3％、4.4％、4.5％、4.6％、4.7％、4.8％、4.9％、5.0％的Na 2O。
B 2O 3有助于提供具有低熔融温度的玻璃，当其含量高时，玻璃化学稳定性降低，因此B 2O 3含量为3％以下，在一些实施方式中，优选为 0.1～2％，在一些实施方式中，优选不引入B 2O 3。在一些实施方式中，可包含约0％、大于0％、0.1％、0.2％、0.3％、0.4％、0.5％、0.6％、0.7％、0.8％、0.9％、1.0％、1.1％、1.2％、1.3％、1.4％、1.5％、1.6％、1.7％、1.8％、1.9％、2.0％、2.1％、2.2％、2.3％、2.4％、2.5％、2.6％、2.7％、2.8％、2.9％、3.0％的B 2O 3。
Sb 2O 3、SnO 2、SnO、CeO 2中的一种或几种组分作为澄清剂加入，Sb 2O 3含量上限为2％，优选为1％，更优选为0.5％。SnO 2、SnO、CeO 2各自的含量上限分别为2％，优选为1％，更优选为0.5％。在一些实施方式中，以上4种澄清剂中的一种或一种以上的含量约为0％、大于0％、0.1％、0.2％、0.3％、0.4％、0.5％、0.6％、0.7％、0.8％、0.9％、1.0％、1.1％、1.2％、1.3％、1.4％、1.5％、1.6％、1.7％、1.8％、1.9％、2.0％。
在一些实施方式中，还可以用As 2O 3、Cl的化合物、Br的化合物等作为澄清剂，其含量分别为2％以下，优选为1％以下，更优选为0.5％以下。
本发明中为获得合适的晶粒尺寸和晶相种类，因此在一些实施方式中优选不引入La 2O 3、Cs 2O、Tb 2O 3、GeO 2和CaO等成分；PbO和As 2O 3是有毒物质，即使少量的加入也不符合环保的要求，因此本发明在一些实施方式中不含有PbO和As 2O 3。
本文所记载的“不引入”“不含有”“0％”是指没有故意将该化合物、分子或元素等作为原料添加到本发明玻璃、微晶玻璃或微晶玻璃制品中；但作为生产玻璃、微晶玻璃和微晶玻璃制品的原材料和/或设备，会存在某些不是故意添加的杂质或组分，会在最终的玻璃组合 物、微晶玻璃和微晶玻璃制品中少量或痕量含有，此种情形也在本发明专利的保护范围内。
本发明的一些实施方式中，微晶玻璃和微晶玻璃制品中主要晶相包括硅酸锂和石英晶相,硅酸锂分为二硅酸锂(Li 2Si 2O 5)和偏硅酸锂(Li 2SiO 3)，在一些实施方式中优选以二硅酸锂和石英晶相和/或透锂长石作为主要晶相，在一些实施方式中优选以二硅酸锂和石英晶相作为主要晶相，在一些优选实施方式中，以二硅酸锂和α-石英晶相作为主要晶相，从而获得本发明中较为优异的性能。
为本发明微晶玻璃提供优异的机械性能，同时还可进行离子交换以获得额外的机械强度。本发明通过合理的组分设计，可使本发明微晶玻璃和微晶玻璃制品获得合适的晶粒大小；同时本发明中微晶玻璃和微晶玻璃制品具有良好的结晶度，使本发明微晶玻璃和微晶玻璃制品具有优异的机械性能。本文所称的结晶度是指结晶的完整程度，结晶完整的晶体内部质点的排列比较规则，衍射线强、尖锐且对称，衍射峰的半高宽接近仪器测量的宽度；结晶度差的晶体晶体中有位错等缺陷，使衍射线峰形宽而弥散。结晶度越差，衍射能力越弱，衍射峰越宽，直到消失在背景之中。
本发明微晶玻璃或微晶玻璃制品的晶粒尺寸和雾度会影响微晶玻璃或微晶玻璃制品的透明度，即影响光透射率，晶粒越小透明度越高，雾度越小，透明度越高。在一些实施方式中，0.55mm厚度的雾度为0.6％以下，优选为0.5％以下，更优选为0.4％以下。在一些实施方式中，晶粒尺寸为100nm以下，优选为80nm以下，更优选为60nm 以下，进一步优选为50nm以下，更进一步优选为40nm以下。另一方面，通过研究发现，微晶玻璃中晶相与玻璃相的折射率差距越小，微晶玻璃或微晶玻璃制品的透明度越高。
在一些实施方式中，微晶玻璃或微晶玻璃制品在可见光范围中呈现高的透明度(即微晶玻璃或微晶玻制品是透明度的)。在一些实施方式中1mm厚度400～800nm的平均光透射率为80％以上，优选为85％以上，更优选为88％以上。在一些优选的实施方式中，0.55mm厚度550nm的光透射率为80％以上，优选为85％以上，更优选为88％以上，进一步优选为91％以上。
在一些实施方式中，可将抗微生物成分添加到玻璃、微晶玻璃或微晶玻璃制品中。
本发明的玻璃组合物、微晶玻璃和微晶玻璃制品可以通过如下方法进行生产和制造：
生成玻璃组合物：按照组成比例范围将原料混合均匀，将均匀的混合物放入铂制或石英制的坩埚中，根据玻璃组成的熔化难易度，在电炉或燃气炉中在1250～1650℃的温度范围内进行5～24小时熔化，搅拌使其均匀后，降至适当的温度并浇铸到模具中，缓慢冷却而成。
本发明的玻璃组合物可以通过众所周知的方法进行成型。在一些实施方式中，本发明玻璃组合物的折射率(nd)为1.500～1.530，优选为1.510～1.525。
本发明的玻璃组合物，在成型后或成型加工后通过晶化工艺进行晶化处理，在玻璃内部均匀地析出结晶。该晶化处理可以通过1个阶 段进行，也可以通过2个阶段进行，但优选采用2个阶段进行晶化处理。在第1温度下进行成核工艺的处理，然后在比成核工艺温度高的第2温度下进行晶体生长工艺的处理。将在第1温度下进行的晶化处理称为第1晶化处理，将在第2温度下进行的晶化处理称为第2晶化处理。
为了使微晶玻璃得到所期望的物理性质，优选的晶化工艺为：
上述通过1个阶段进行晶化处理，可以连续地进行核形成工艺与结晶生长工艺。即，升温至规定的晶化处理温度，在达到热处理温度之后，将其温度保持一定的时间，然后再进行降温。该晶化处理的温度优选为在490～800℃，为了能够析出所期望的晶相，更优选为550～750℃，在晶化处理温度下的保持时间，优选为0～8小时，更优选为1～6小时。
上述通过2个阶段进行晶化处理时，第1温度优选为490～650℃，第2温度优选为600～850℃。在第1温度下的保持时间，优选为0～24小时，更优选为2～15小时。在第2温度下的保持时间，优选为0～10小时，更优选为0.5～6小时。
上述保持时间0小时，是指在达到其温度后不到1分钟又开始降温或升温。
在一些实施方式中，本发明通过晶化工艺所得到的微晶玻璃的折射率(nd)为1.520～1.550，优选为1.530～1.545。
在一些实施方式中，可通过各种工艺将本文所述的玻璃组合物或微晶玻璃制造成成形体，所述成形体包括但不限于片材，所述工艺包括但不限于狭缝拉制、浮法、辊压和本领域公知的其他形成片材的工 艺。或者，可通过本领域所公知的浮法或辊压法来形成玻璃组合物或微晶玻璃。
本发明的玻璃组合物或微晶玻璃，可以采用研磨或抛光加工等方法制造片材的玻璃成形体，但制造玻璃成形体的方法，并不限定于这些方法。
本发明的玻璃或微晶玻璃成形体，可以在一定温度下采用热弯或压型等方法制备形成各种形状，并不限定于这些方法。
本发明所述的玻璃组合物、微晶玻璃和微晶玻璃制品可具有合理有用的任何厚度。
本发明的微晶玻璃除了通过析出结晶提高机械特性之外，还可以通过形成压缩应力层获得更高的强度，从而制成微晶玻璃制品。
在一些实施方式中，可将玻璃组合物或微晶玻璃加工成片材，和/或造型(如打孔、热弯等)，定形后抛光和/或扫光，再通过化学钢化工艺进行化学钢化。
本发明所述的化学钢化，即是离子交换法。本发明的玻璃、微晶玻璃都是可通过本技术领域所公知的方法进行离子交换。在离子交换过程中，玻璃或微晶玻璃中的较小的金属离子被靠近玻璃或微晶玻璃的具有相同价态的较大金属离子置换或“交换”。用较大的离子置换较小的离子，在玻璃或微晶玻璃中构建压缩应力，形成压缩应力层。
在一些实施方式中,金属离子是单价碱金属离子(例如Na +、K +、Rb +、Cs +等),离子交换通过将玻璃或微晶玻璃浸没在包含较大的金属离子的至少一种熔融盐的盐浴中来进行，该较大的金属离子用于置换 玻璃中的较小的金属离子。或者，其他单价金属离子例如Ag +、Tl +、Cu +等也可用于交换单价离子。用来化学钢化玻璃或微晶玻璃的一种或更多种离子交换过程可包括但不限于：将其浸没在单一盐浴中，或者将其浸没在具有相同或不同组成的多个盐浴中，在浸没之间有洗涤和/或退火步骤。
在一些实施方式中,玻璃或微晶玻璃可通过在浸没于约430℃～470℃的温度的熔融Na盐(如NaNO 3)的盐浴中约6～20小时来进行离子交换，优选温度范围为435℃～460℃，优选时间范围为8～13小时。在这种实施方式中,Na离子置换玻璃或微晶玻璃中的部分Li离子，从而形成表面压缩层且呈现高机械性能。在一些实施方式中，玻璃或微晶玻璃可通过在浸没于可通过浸没于约400℃～450℃的温度下熔融K盐(如KNO 3)的盐浴中1～8小时小时来对实施方式进行离子交换，优选时间范围为2～4小时。
在一些优选实施方式中，通过在450℃的熔融Na盐(如NaNO 3)的盐浴中约8小时，离子交换层深度达80μm以上，优选为85μm以上。
在一些实施方式中，还有向玻璃或微晶玻璃的表层注入离子的离子注入法，以及对玻璃或微晶玻璃进行加热，然后快速冷却的热钢化法。
本发明玻璃组合物、微晶玻璃和/或微晶玻璃制品各项性能指标采用以下方法测试：
[热膨胀系数]
热膨胀系数(α 20℃-120℃)按照GB/T7962.16-2010测试方法进行测 试。
[折射率]
折射率(nd)按照GB/T7962.1-2010方法测试。
[雾度]
采用雾度测试仪EEL57D，以0.55mm厚玻璃样品制备，以GB2410-80为标准进行测试。
[晶粒尺寸]
利用SEM扫描电镜进行测定，微晶玻璃通过在HF酸中进行表面处理，再对微晶玻璃表面进行喷金，在SEM扫描电镜下进行表面扫描，确定其晶粒的大小。
[光透射率]
将样品加工成1mm厚度并进行相对面平行抛光，利用日立U-41000形分光光度计测定400～800nm的平均光透射率。
将样品加工成0.55mm厚度并进行相对面平行抛光，利用日立U-41000形分光光度计测定550nm的光透射率。
[折射率温度系数]
折射率温度系数按照GB/T 7962.4—2010规定方法测试，测定20～40℃的折射率温度系数。
[结晶度]
将XRD衍射峰与数据库图谱进行对比，结晶度是通过计算结晶相衍射强度在整体图谱强度中所占比例所得，并且通过使用纯石英晶体进行内部标定。
[表面应力]和[离子交换层深度]
利用玻璃表面应力仪FSM-6000LEUV进行表面应力测定。
利用玻璃表面应力仪SLP-2000进行离子交换层深度测定。
作为测定条件以样品的折射率为1.54、光学弹性常数为25.3[(nm/cm)/Mpa]进行计算。
[落球试验高度]
对150×57×0.55mm的样品两表面进行抛光后放置在橡胶片上，使132g的钢球从规定高度落下，样品不发生断裂而能够承受的冲击的最大落球试验高度。具体地说，试验从落球试验高度650mm开始实施，在不发生断裂的情况下，通过700mm、750mm、800mm、850mm和900mm及以上依次改变高度。对于具有“落球试验高度”的实施例，以微晶玻璃制品为试验对象。在实施例中记录为900mm的试验数据，表示即使从900mm的高度使钢球落下微晶玻璃制品也不发生断裂而承受了冲击。
[断裂韧性]
使用直接测量压痕扩展裂纹尺寸的方法，试样规格为2mm×4mm×20mm，经过倒角、磨平和抛光，试样制备完成后，用维氏硬度压头在试样上加49N的力并维持30s的时间，打出压痕后，用三点弯曲的方法测定其断裂强度。
[四点弯曲强度]
采用微机控制电子万能试验机CMT6502，玻璃规格150×57×0.55mm，以ASTM C 158-2002为标准进行测试。
本发明玻璃组合物具有以下性能：
1)在一些实施方式中，热膨胀系数(α 20℃-120℃)为45×10 -7/K～ 70×10 -7/K，优选为50×10 -7/K～70×10 -7/K。
2)在一些实施方式中，折射率(nd)为1.500～1.530，优选为1.510～1.525。
本发明微晶玻璃具有以下性能：
1)在一些实施方式中，0.55mm厚度的雾度为0.6％以下，优选为0.5％以下，更优选为0.4％以下。
2)在一些实施方式中，晶粒尺寸为100nm以下，优选为80nm以下，更优选为60nm以下，进一步优选为50nm以下，更进一步优选为40nm以下。
3)在一些实施方式中，本发明微晶玻璃折射率温度系数为-0.5×10 -6/℃以下，优选-0.8×10 -6/℃以下，更优选-1.1×10 -6/℃以下。
4)在一些实施方式中，结晶度为50％以上，优选为65％以上，更优选为70％以上，进一步优选为75％以上。
5)在一些实施方式中，折射率(nd)为1.520～1.550，优选为1.530～1.545。
6)在一些实施方式中，1mm厚度400～800nm的平均光透射率为80％以上，优选为85％以上，更优选为88％以上。
7)在一些实施方式中，0.55mm厚度550nm的光透射率为80％以上，优选为85％以上，更优选为88％以上，进一步优选为91％以上。
本发明微晶玻璃制品除具有上述微晶玻璃的性能外，还具有以下性能：
1)在一些实施方式中，表面应力为200MPa以上，优选为250MPa 以上，更优选为300MPa以上；
2)在一些实施方式中，四点弯曲强度为600MPa以上，优选为650MPa以上，更优选为700MPa以上；
3)在一些实施方式中，离子交换层深度为30μm以上，优选为50μm以上，更优选60μm以上，进一步优选80μm以上；
4)在一些实施方式中，落球试验高度为700mm以上，优选为800mm以上，更优选为1000mm以上，进一步优选为1200mm以上；
5)在一些实施方式中，断裂韧性为1MPa·m 1/2以上，优选为1.3MPa·m 1/2以上，更优选为1.5MPa·m 1/2以上。
6)在一些实施方式中，1mm厚度400～800nm的平均光透射率为80％以上，优选为85％以上，更优选为88％以上。
7)在一些实施方式中，0.55mm厚度550nm的光透射率为80％以上，优选为85％以上，更优选为88％以上，进一步优选为91％以上。
本发明的微晶玻璃和微晶玻璃制品由于具有上述优异的性能，可广泛制作成玻璃盖板或玻璃元器件；同时，本发明微晶玻璃、微晶玻璃制品，以及所制成的玻璃盖板或玻璃元器件还可应用于电子设备或显示设备中，如手机、手表、电脑、触摸显示屏等。
实施例
为了进一步清楚地阐释和说明本发明的技术方案，提供以下的非限制性实施例。本发明实施例经过诸多努力以确保数值(例如数量、温度等)的精确性，但是必须考虑到存在一些误差和偏差。组成自身 基于氧化物以重量％给出，且已标准化成100％。
以下表1～3中所示为玻璃组合物实施例
表1.
Figure PCTCN2018112078-appb-000001
表2.
Figure PCTCN2018112078-appb-000002
Figure PCTCN2018112078-appb-000003
表3.
Figure PCTCN2018112078-appb-000004
Figure PCTCN2018112078-appb-000005
以下表4～6中所示为微晶玻璃实施例
表4.
Figure PCTCN2018112078-appb-000006
Figure PCTCN2018112078-appb-000007
表5.
Figure PCTCN2018112078-appb-000008
Figure PCTCN2018112078-appb-000009
表6.
Figure PCTCN2018112078-appb-000010
Figure PCTCN2018112078-appb-000011
以下表7～9中所示为微晶玻璃制品实施例
表7.
Figure PCTCN2018112078-appb-000012
Figure PCTCN2018112078-appb-000013
表8.
Figure PCTCN2018112078-appb-000014
Figure PCTCN2018112078-appb-000015
表9.
Figure PCTCN2018112078-appb-000016
Figure PCTCN2018112078-appb-000017

Claims (17)

  1. 电子设备盖板用微晶玻璃制品，其特征在于，其主要晶相含有硅酸锂和石英晶相，其组成按重量百分比表示，含有：SiO 2：65～85％、Al 2O 3：1～15％、Li 2O：5～15％、ZrO 2：0.1～10％、P 2O 5：0.1～10％、K 2O：0～10％、MgO：0～10％、ZnO：0～10％、Na 2O：0～5％，其中(SiO 2+Al 2O 3+Li 2O+ZrO 2)/P 2O 5为40～90，落球试验高度为700mm以上。
  2. 如权利要求1所述的电子设备盖板用微晶玻璃制品，其特征在于，其组成按重量百分比表示，还含有：SrO：0～5％、BaO：0～5％、TiO 2：0～5％、Y 2O 3：0～5％、B 2O 3：0～3％、澄清剂：0～2％。
  3. 如权利要求1或2任一权利要求所述的电子设备盖板用微晶玻璃制品，其特征在于，其中：(SiO 2+Li 2O)/Al 2O 3为6～15、(Al 2O 3+Li 2O)/P 2O 5为5～20、(SiO 2+Li 2O)/P 2O 5为40～80、(K 2O+MgO)/ZrO 2为0.6～1.2、或Li 2O/(K 2O+ZrO 2)为2.3～4.0。
  4. 如权利要求1或2任一权利要求所述的电子设备盖板用微晶玻璃制品，其特征在于，其中：(SiO 2+Li 2O)/Al 2O 3为8～13、(Al 2O 3+Li 2O)/P 2O 5为6～14、(SiO 2+Li 2O)/P 2O 5为40～70、(SiO 2+Al 2O 3+Li 2O+ZrO 2)/P 2O 5为45～85、(K 2O+MgO)/ZrO 2为0.7～1.1、和Li 2O/(K 2O+ZrO 2)为2.5～3.5。
  5. 如权利要求1或2任一权利要求所述的电子设备盖板用微晶玻璃制品，其特征在于，其组成按重量百分比表示，含有：SiO 2：70～76％、Al 2O 3：4～10％、Li 2O：8～12.5％、ZrO 2：1～5％、P 2O 5：1～3％、K 2O：0～3％、MgO：0.3～2％、ZnO：0～3％、Na 2O：0～1％、Sb 2O 3：0～1％、SnO 2：0～1％、SnO：0～1％、或CeO 2：0～1％。
  6. 如权利要求1或2任一权利要求所述的电子设备盖板用微晶玻璃制品，其特征在于，其中：(Al 2O 3+Li 2O)/P 2O 5为8.5～14、(SiO 2+Li 2O)/P 2O 5为45～60、(SiO 2+Al 2O 3+Li 2O+ZrO 2)/P 2O 5为48～80、或(SiO 2+Li 2O)/Al 2O 3为8.5～12。
  7. 如权利要求1或2任一权利要求所述的电子设备盖板用微晶玻璃制品，其特征在于，其中：(K 2O+MgO)/ZrO 2为0.8～1.0、或Li 2O/(K 2O+ZrO 2)为2.8～3.3。
  8. 如权利要求1或2任一权利要求所述的电子设备盖板用微晶玻璃制品，其特征在于，其组成按重量百分比表示，含有：Li 2O：8～小于10％、不含有SrO、不含有BaO、不含有TiO 2、不含有Y 2O 3、不含有GeO 2、不含有CaO、不含有Cs 2O、不含有PbO、不含有B 2O 3、不含有As 2O 3、不含有La 2O 3、和不含有Tb 2O 3。
  9. 如权利要求1或2任一权利要求所述的电子设备盖板用微晶玻璃制品，其特征在于，结晶度为70％以上。
  10. 如权利要求1或2任一权利要求所述的电子设备盖板用微晶玻璃制品，其特征在于，落球试验高度为1000mm以上；或四点弯曲强度为650MPa以上；或0.55mm厚度的雾度为0.5％以下；或折射率温度系数为-0.8×10 -6/℃以下；或0.55mm厚550nm波长的光透射率为88％以上。
  11. 微晶玻璃，其特征在于，其主要晶相含有硅酸锂和石英晶相，其组成按重量百分比表示为：SiO 2：65～85％、Al 2O 3：1～15％、Li 2O：5～15％、ZrO 2：0.1～10％、P 2O 5：0.1～10％、K 2O：0～10％、MgO：0～ 10％、ZnO：0～10％、Na 2O：0～3％，Sb 2O 3：0～1％、SnO 2：0～1％、SnO：0～1％、CeO 2：0～1％，其中(SiO 2+Al 2O 3+Li 2O+ZrO 2)/P 2O 5为40～90，(K 2O+MgO)/ZrO 2为0.6～1.2，0.55mm厚度的雾度为0.5％以下。
  12. 如权利要求11所述的微晶玻璃，其特征在于，其中：(SiO 2+Al 2O 3+Li 2O+ZrO 2)/P 2O 5为45～85、(SiO 2+Li 2O)/Al 2O 3为8～13、(Al 2O 3+Li 2O)/P 2O 5为6～14、(SiO 2+Li 2O)/P 2O 5为40～70、或Li 2O/(K 2O+ZrO 2)为2.5～3.5。
  13. 如权利要求11所述的微晶玻璃，其特征在于，其中SiO 2：70～76％、Al 2O 3：4～10％、Li 2O：8～12.5％、ZrO 2：1～5％、P 2O 5：1～3％、K 2O：0～3％、MgO：0.3～2％、ZnO：0～3％、Na 2O：0～1％。
  14. 如权利要求11所述的微晶玻璃，其特征在于，其中：(K 2O+MgO)/ZrO 2为0.8～1.0、或Li 2O/(K 2O+ZrO 2)为2.8～3.3。
  15. 如权利要求11所述的微晶玻璃，其特征在于，结晶度为70％以上；或晶粒尺寸为80nm以下；或折射率温度系数为-0.8×10 -6/℃以下；或1mm厚400～800nm波长的平均光透射率为85％以上。
  16. 电子设备用玻璃盖板，其特征在于，含有权利要求1～10任一权利要求所述的电子设备盖板用微晶玻璃制品，或权利要求11～15任一权利要求所述的微晶玻璃。
  17. 电子设备，其特征在于，含有权利要求1～10任一权利要求所述的电子设备盖板用微晶玻璃制品，或权利要求11～15任一权利要求所述的微晶玻璃，或权利要求16所述的电子设备用玻璃盖板。
PCT/CN2018/112078 2018-10-26 2018-10-26 电子设备盖板用微晶玻璃制品和微晶玻璃 WO2020082328A1 (zh)

Priority Applications (8)

Application Number Priority Date Filing Date Title
KR1020207033502A KR102294910B1 (ko) 2018-10-26 2018-10-26 전자기기 커버판 용 결정화 유리 제품 및 결정화 유리
JP2020567227A JP7048767B2 (ja) 2018-10-26 2018-10-26 電子デバイスカバープレート用ガラスセラミック物品およびガラスセラミック
CN201880090187.5A CN111936439B (zh) 2018-10-26 2018-10-26 电子设备盖板用微晶玻璃制品和微晶玻璃
KR1020217025914A KR102609966B1 (ko) 2018-10-26 2018-10-26 전자기기 커버판 용 결정화 유리 제품 및 결정화 유리
PCT/CN2018/112078 WO2020082328A1 (zh) 2018-10-26 2018-10-26 电子设备盖板用微晶玻璃制品和微晶玻璃
EP18937644.5A EP3808711A4 (en) 2018-10-26 2018-10-26 MICROCRYSTALLINE GLASS AND MICROCRYSTALLINE GLASS PRODUCT FOR ELECTRONIC EQUIPMENT COVER PLATE
US16/223,918 US10676390B2 (en) 2018-10-26 2018-12-18 Glass-ceramic article and glass-ceramic for electronic device cover plate
US16/859,527 US10913681B2 (en) 2018-10-26 2020-04-27 Glass-ceramic article and glass-ceramic for electronic device cover plate

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
PCT/CN2018/112078 WO2020082328A1 (zh) 2018-10-26 2018-10-26 电子设备盖板用微晶玻璃制品和微晶玻璃

Related Child Applications (1)

Application Number Title Priority Date Filing Date
US16/223,918 Continuation US10676390B2 (en) 2018-10-26 2018-12-18 Glass-ceramic article and glass-ceramic for electronic device cover plate

Publications (1)

Publication Number Publication Date
WO2020082328A1 true WO2020082328A1 (zh) 2020-04-30

Family

ID=70326412

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/CN2018/112078 WO2020082328A1 (zh) 2018-10-26 2018-10-26 电子设备盖板用微晶玻璃制品和微晶玻璃

Country Status (6)

Country Link
US (2) US10676390B2 (zh)
EP (1) EP3808711A4 (zh)
JP (1) JP7048767B2 (zh)
KR (2) KR102609966B1 (zh)
CN (1) CN111936439B (zh)
WO (1) WO2020082328A1 (zh)

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111807706A (zh) * 2020-06-29 2020-10-23 成都光明光电股份有限公司 微晶玻璃和微晶玻璃制品
CN112125526A (zh) * 2020-09-26 2020-12-25 湖北蓝晶元光电科技发展有限公司 一种微晶玻璃盖板及其制备方法
CN113880438A (zh) * 2020-07-01 2022-01-04 华为技术有限公司 微晶玻璃和终端
CN114890679A (zh) * 2022-06-02 2022-08-12 咸宁南玻光电玻璃有限公司 强化玻璃、分相玻璃及其制备方法与应用

Families Citing this family (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2019105250A1 (zh) * 2017-12-01 2019-06-06 成都光明光电股份有限公司 微晶玻璃及其基板
CN112794646B (zh) * 2018-10-26 2022-04-19 成都光明光电股份有限公司 微晶玻璃、微晶玻璃制品及其制造方法
KR102130995B1 (ko) * 2018-12-27 2020-07-09 (주)유티아이 광학 필터용 글라스 기판의 강도 개선 방법 및 이에 의한 강화 글라스 기반 광학 필터
CN116693202A (zh) * 2019-02-08 2023-09-05 Ａｇｃ株式会社 微晶玻璃、化学强化玻璃和半导体支撑基板
CN113423671A (zh) * 2019-03-22 2021-09-21 日本电气硝子株式会社 Li2O－Al2O3－SiO2系结晶化玻璃
CN112321162B (zh) * 2020-11-13 2023-05-30 重庆鑫景特种玻璃有限公司 蓝紫光低透过率玻璃陶瓷及其制备方法、玻璃制品
CN112592065B (zh) * 2020-12-31 2021-12-07 成都光明光电股份有限公司 微晶玻璃、微晶玻璃制品及其制造方法
CN116553830B (zh) * 2021-01-30 2024-01-30 华为技术有限公司 3d微晶玻璃及其制备方法和电子设备
CN113402172B (zh) * 2021-08-06 2023-09-22 成都光明光电有限责任公司 玻璃陶瓷和玻璃陶瓷制品
CN114671616B (zh) * 2022-04-01 2024-02-23 河北省沙河玻璃技术研究院 一种高强度透明微晶玻璃及制备方法
CN116002980A (zh) * 2022-12-28 2023-04-25 河南旭阳光电科技有限公司 微晶玻璃及其制备方法和应用

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN1283596A (zh) * 1999-08-10 2001-02-14 株式会社小原 用作滤光器的玻璃陶瓷及滤光器
CN101508524A (zh) 2009-03-31 2009-08-19 成都光明光电股份有限公司 适于化学钢化的玻璃及其化学钢化玻璃
CN104926135A (zh) * 2015-06-10 2015-09-23 成都光明光电有限责任公司 微晶玻璃以及多层无机膜滤波器
CN108640526A (zh) * 2018-06-26 2018-10-12 成都光明光电有限责任公司 微晶玻璃

Family Cites Families (20)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3788865A (en) * 1964-07-31 1974-01-29 C Babcock Crystallized glass ceramics and process for forming same
JP3440214B2 (ja) * 1998-03-23 2003-08-25 株式会社オハラ 情報記憶媒体用ガラスセラミックス基板
JP2000143290A (ja) * 1998-11-09 2000-05-23 Ngk Insulators Ltd 結晶化ガラス、磁気ディスク用基板、磁気ディスクおよび結晶化ガラスの製造方法
JP4158282B2 (ja) * 1999-07-06 2008-10-01 コニカミノルタオプト株式会社 磁気ディスク用結晶化ガラス基板
JP2001019469A (ja) * 1999-07-06 2001-01-23 Minolta Co Ltd ガラス組成
JP2001035417A (ja) * 1999-07-21 2001-02-09 Ohara Inc Ｃｒｔ用ガラスセラミックス
US6677259B2 (en) * 1999-08-10 2004-01-13 Kabushiki Kaisha Ohara Glass-ceramics for a light filter
JP2001097740A (ja) * 1999-09-29 2001-04-10 Ngk Insulators Ltd 結晶化ガラス、磁気ディスク用基板および磁気ディスク
JP3600548B2 (ja) * 2001-04-26 2004-12-15 株式会社オハラ 光フィルター用ガラスセラミックスおよび光フイルター
JP2007223884A (ja) * 2005-10-07 2007-09-06 Ohara Inc 無機組成物
TW200724506A (en) * 2005-10-07 2007-07-01 Ohara Kk Inorganic composition
JP4976058B2 (ja) * 2006-06-06 2012-07-18 株式会社オハラ 結晶化ガラスおよび結晶化ガラスの製造方法
JP4467597B2 (ja) * 2007-04-06 2010-05-26 株式会社オハラ 無機組成物物品
JP5070006B2 (ja) * 2007-11-02 2012-11-07 株式会社オハラ 結晶化ガラス
JP5053948B2 (ja) * 2007-12-21 2012-10-24 株式会社オハラ 結晶化ガラス
CN102089252A (zh) * 2008-07-03 2011-06-08 康宁股份有限公司 用于电子设备的耐用玻璃陶瓷机壳/封罩
KR102620832B1 (ko) * 2014-10-08 2024-01-03 코닝 인코포레이티드 페탈라이트 및 리튬 실리케이트 구조를 갖는 고강도 유리-세라믹
CN107915412A (zh) * 2017-12-01 2018-04-17 成都光明光电股份有限公司 微晶玻璃及其基板
CN107840578B (zh) * 2017-12-01 2021-06-11 成都光明光电股份有限公司 微晶玻璃及其基板
CN110492613B (zh) * 2019-08-23 2021-03-02 中国能源建设集团广东省电力设计研究院有限公司 一种断面失步解列判别控制系统及方法

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN1283596A (zh) * 1999-08-10 2001-02-14 株式会社小原 用作滤光器的玻璃陶瓷及滤光器
CN101508524A (zh) 2009-03-31 2009-08-19 成都光明光电股份有限公司 适于化学钢化的玻璃及其化学钢化玻璃
CN104926135A (zh) * 2015-06-10 2015-09-23 成都光明光电有限责任公司 微晶玻璃以及多层无机膜滤波器
CN108640526A (zh) * 2018-06-26 2018-10-12 成都光明光电有限责任公司 微晶玻璃

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP3808711A4

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111807706A (zh) * 2020-06-29 2020-10-23 成都光明光电股份有限公司 微晶玻璃和微晶玻璃制品
CN113880438A (zh) * 2020-07-01 2022-01-04 华为技术有限公司 微晶玻璃和终端
CN112125526A (zh) * 2020-09-26 2020-12-25 湖北蓝晶元光电科技发展有限公司 一种微晶玻璃盖板及其制备方法
CN112125526B (zh) * 2020-09-26 2022-10-14 湖北蓝晶元光电科技发展有限公司 一种微晶玻璃盖板及其制备方法
CN114890679A (zh) * 2022-06-02 2022-08-12 咸宁南玻光电玻璃有限公司 强化玻璃、分相玻璃及其制备方法与应用
CN114890679B (zh) * 2022-06-02 2023-08-25 咸宁南玻光电玻璃有限公司 强化玻璃、分相玻璃及其制备方法与应用

Also Published As

Publication number Publication date
CN111936439A (zh) 2020-11-13
US20200131080A1 (en) 2020-04-30
JP2021527019A (ja) 2021-10-11
US10913681B2 (en) 2021-02-09
EP3808711A1 (en) 2021-04-21
KR20210106576A (ko) 2021-08-30
KR102294910B1 (ko) 2021-08-27
KR20210014104A (ko) 2021-02-08
US10676390B2 (en) 2020-06-09
EP3808711A4 (en) 2021-07-21
US20200277221A1 (en) 2020-09-03
KR102609966B1 (ko) 2023-12-04
CN111936439B (zh) 2022-07-29
JP7048767B2 (ja) 2022-04-05

Similar Documents

Publication Publication Date Title
TWI782239B (zh) 微晶玻璃、微晶玻璃製品及其製造方法
CN111268913B (zh) 电子设备盖板用微晶玻璃制品和微晶玻璃
KR102294910B1 (ko) 전자기기 커버판 용 결정화 유리 제품 및 결정화 유리
CN111099829B (zh) 透明微晶玻璃、微晶玻璃制品及其制备方法
TWI806355B (zh) 微晶玻璃、微晶玻璃製品及其製造方法
CN112456806B (zh) 微晶玻璃、微晶玻璃制品及其制造方法
CN113402173B (zh) 微晶玻璃、微晶玻璃制品及其制造方法
CN113402172B (zh) 玻璃陶瓷和玻璃陶瓷制品
WO2022142526A1 (zh) 微晶玻璃、微晶玻璃制品及其制造方法
WO2023246365A1 (zh) 微晶玻璃、微晶玻璃制品及其制造方法
RU2778750C1 (ru) Изделие из стеклокристаллического материала и стеклокристаллический материал для закрывающей пластины электронного устройства

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 18937644

Country of ref document: EP

Kind code of ref document: A1

ENP Entry into the national phase

Ref document number: 2020567227

Country of ref document: JP

Kind code of ref document: A

ENP Entry into the national phase

Ref document number: 2018937644

Country of ref document: EP

Effective date: 20210112

NENP Non-entry into the national phase

Ref country code: DE