WO2015098485A1 - ガラス - Google Patents

ガラス Download PDF

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Publication number
WO2015098485A1
WO2015098485A1 PCT/JP2014/082470 JP2014082470W WO2015098485A1 WO 2015098485 A1 WO2015098485 A1 WO 2015098485A1 JP 2014082470 W JP2014082470 W JP 2014082470W WO 2015098485 A1 WO2015098485 A1 WO 2015098485A1
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component
glass
content
sio
less
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PCT/JP2014/082470
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English (en)
French (fr)
Japanese (ja)
Inventor
浄行 桃野
依実奈 鳥谷
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株式会社オハラ
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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
    • C03C3/00—Glass compositions
    • C03C3/04—Glass compositions containing silica
    • C03C3/062—Glass compositions containing silica with less than 40% silica by weight
    • C03C3/064—Glass compositions containing silica with less than 40% silica by weight containing boron
    • C03C3/068—Glass compositions containing silica with less than 40% silica by weight containing boron containing rare earths
    • 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
    • C03C3/062—Glass compositions containing silica with less than 40% silica by weight
    • 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
    • C03C4/0092—Compositions for glass with special properties for glass with improved high visible transmittance, e.g. extra-clear glass
    • H—ELECTRICITY
    • H10—SEMICONDUCTOR DEVICES; ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
    • H10K—ORGANIC ELECTRIC SOLID-STATE DEVICES
    • H10K77/00—Constructional details of devices covered by this subclass and not covered by groups H10K10/80, H10K30/80, H10K50/80 or H10K59/80
    • H10K77/10—Substrates, e.g. flexible substrates

Definitions

  • the present invention relates to glass, and particularly to glass having a high refractive index suitable for optical glass and glass substrates for organic EL lighting.
  • Organic EL elements are light and thin, can be driven with low power consumption, and are characterized by surface light emission.
  • an organic light emitting layer is provided on the surface of a translucent glass substrate via a transparent electrode layer, and a counter electrode is provided on the surface of the organic light emitting layer.
  • the organic light emitting layer emits light.
  • the light emitted from the organic light emitting layer passes through the transparent electrode layer and the translucent substrate and is irradiated to the outside.
  • the translucent glass substrate since the refractive index of the organic light emitting layer and the transparent electrode layer is relatively high, the translucent glass substrate also has to be used at the interface between the organic light emitting layer or the transparent electrode layer and the glass substrate unless glass having a high refractive index is used. There is a problem that total reflection occurs and the light extraction efficiency decreases. Moreover, it is calculated
  • the conventional glass there is no glass having a viscosity that can be formed into a thin plate and having a high refractive index that solves the problem of total reflection. Also, in optical applications other than glass substrates for organic EL lighting, there is a demand for molding optical glass having a high refractive index into a thin plate at a low cost in the field of wafer level optics technology, for example.
  • Patent Document 1 discloses a glass having a refractive index nd of 1.74, but the refractive index nd of an organic light emitting layer or a transparent electrode is about 1.9, and a sufficiently high refractive index is realized. Absent.
  • the present invention has been made in view of the above problems, and its object is to obtain a glass having a high refractive index nd while having a viscosity capable of forming a thin plate.
  • the present inventors have conducted earnest test research, and as a result, having a specific composition can provide a glass having a viscosity suitable for thin plate molding and a high refractive index.
  • the headline and the present invention were completed. Specifically, the present invention provides the following.
  • (Configuration 1) In mass% in terms of oxide, 5% to 50% of SiO 2 component, 4% to 35% of La 2 O 3 component, 3% to 30% of TiO 2 component, ZrO 2 component from 0% to 20%, Contains 5% to 50% BaO component, The total content of La 2 O 3 component and BaO components, the mass ratio to the content of SiO 2 component values of (La 2 O 3 + BaO) / SiO 2 is a glass is 1.1 to 4.0.
  • (Configuration 2) The glass according to Configuration 1, having a refractive index nd of 1.75 or more.
  • (Configuration 3) In mass% in terms of oxide, Y 2 O 3 component from 0% to 40%, Nb 2 O 5 component from 0% to 20% The glass of the structure 1 or 2 to contain.
  • the content range of the B 2 O 3 component is 0% to 15% in terms of oxide% by mass, and the mass ratio of the total content of the SiO 2 component and the B 2 O 3 component to the content of the SiO 2 component ( glass according the configuration 1 the value of SiO 2 + B 2 O 3) / SiO 2 is 1.0 to 2.00 in any of the three.
  • (Configuration 5) Terms of% by mass on the oxide basis, of the content of Nb 2 O 5 component, either SiO 2 component mass ratio Nb 2 O 5 / SiO 2 values 4 from the configuration 1 is 0.60 or less to the content of Glass described in 1.
  • (Configuration 8) The glass according to any one of configurations 1 to 7, wherein the viscosity of the glass melt at the liquidus temperature is 10.0 dPa ⁇ s or more.
  • (Configuration 9) Glass in any one of the structures 1-8 whose glass transition point Tg is 625 degreeC or more.
  • (Configuration 10) Glass in any one of the structures 1-9 whose liquidus temperature is 1300 degrees C or less.
  • (Configuration 11) The glass substrate which consists of glass in any one of the structures 1-10.
  • (Configuration 12) The optical element which uses the glass in any one of the structures 1 to 10 as a base material.
  • a glass having a viscosity suitable for thin plate molding and a high refractive index can be obtained. That is, it is possible to obtain a glass having a viscosity of a glass melt at a liquidus temperature of 10.0 dPa ⁇ s or more and a refractive index nd of 1.75 or more.
  • Glass component The composition range of each component constituting the glass of the present invention is described below. Unless otherwise specified in the present specification, the contents of the respective components are all expressed in mass% with respect to the total mass of the glass in terms of oxide.
  • oxide equivalent composition means that the oxide, composite salt, metal fluoride, etc. used as a raw material of the glass component of the present invention are all decomposed and changed into an oxide when melted. It is the composition which described each component contained in glass by making the total mass of the said production
  • the SiO 2 component is an essential component that is indispensable as a glass-forming oxide.
  • the content of the SiO 2 component is preferably 5%, more preferably 6.7%, further preferably 10%, and most preferably 13%.
  • the upper limit of the content of the SiO 2 component is preferably 50%, more preferably 45%, still more preferably 40%, and most preferably 35%.
  • the La 2 O 3 component is an essential component that increases the refractive index of the glass.
  • the content of La 2 O 3 component is preferably 4%, more preferably 4.5%, still more preferably 5%, and most preferably 6%.
  • the content of La 2 O 3 component is preferably 35%, more preferably 32%, still more preferably 30%, and most preferably 28%.
  • the TiO 2 component is an essential component that increases the refractive index of the glass, adjusts the Abbe number to a low level, and increases the devitrification resistance while obtaining a desired viscosity suitable for thin plate molding. Therefore, the content of the TiO 2 component is preferably 3%, more preferably 5%, still more preferably 7%, and most preferably 8%. On the other hand, by making the content of TiO 2 30% or less, while obtaining a desired viscosity suitable for thin plate molding, it is possible to reduce the coloring of the glass and increase the visible light transmittance, and the TiO 2 component Devitrification due to excessive inclusion can be suppressed. Therefore, the upper limit of the content of the TiO 2 component is preferably 30%, more preferably 28%, still more preferably 25%, and most preferably 22%.
  • ZrO 2 component is an optional component that, when contained over 0%, can contribute to higher refractive index and lower dispersion of glass without deteriorating the transmittance in the visible region, and can enhance the devitrification resistance of glass. is there. Therefore, when the ZrO 2 component is contained, the content is more preferably 1%, further preferably 2.5%, and most preferably 5.1%. On the other hand, by making the ZrO 2 component 20% or less, it is possible to suppress a decrease in the devitrification resistance of the glass due to the excessive inclusion of the ZrO 2 component. Therefore, the upper limit of the content of the ZrO 2 component is preferably 20%, more preferably 15%, still more preferably 9.8%, still more preferably 8.5%, and most preferably 7.5%.
  • the BaO component is an essential component that can improve the meltability of the glass raw material and the devitrification resistance of the glass while obtaining a desired viscosity suitable for thin plate molding. Therefore, the content of the BaO component is preferably 5%, more preferably 7%, still more preferably 10.9%, and most preferably 15%. On the other hand, by setting the content of the BaO component to 50% or less, a decrease in refractive index and a decrease in devitrification resistance due to excessive inclusion of these components can be suppressed. Therefore, the upper limit of the content of the BaO component is preferably 50%, more preferably 45%, still more preferably 40%, and most preferably 38%.
  • the mass ratio of the total content of La 2 O 3 component and BaO component to the content of SiO 2 component (La 2 O 3 + BaO) / SiO 2 is 1.1 or more and 4.0. It is characterized by the following. By setting the value of this ratio to 1.1 or more and 4.0 or less, it is possible to suppress a decrease in refractive index and deterioration in devitrification resistance while obtaining a desired viscosity suitable for thin plate molding. Therefore, the value of (La 2 O 3 + BaO) / SiO 2 is preferably 1.1, more preferably 1.2, and most preferably 1.3. The value of (La 2 O 3 + BaO) / SiO 2 is preferably 4.0, more preferably 3.8, and most preferably 3.5.
  • the Y 2 O 3 component when ultra containing 0%, which is an optional component that can reduce a high refractive index and specific gravity.
  • the upper limit of the content of the Y 2 O 3 component is preferably 40%, more preferably 30%, still more preferably 15%, and most preferably 10%.
  • the Nb 2 O 5 component is an optional component that can increase the refractive index of the glass and increase the devitrification resistance when it exceeds 0%. Accordingly, the content of the Nb 2 O 5 component is preferably more than 0%, more preferably 1%, and even more preferably 1.7%. On the other hand, by reducing the content of the Nb 2 O 5 component to 20% or less, the devitrification resistance of the glass is reduced due to the excessive content of the Nb 2 O 5 component while suppressing the cost of the material, and the visible light A decrease in transmittance can be suppressed. Therefore, the content of the Nb 2 O 5 component is preferably 20%, more preferably 14%, and most preferably 9.8%.
  • the B 2 O 3 component is an optional component that can be contained as a glass-forming oxide when it contains more than 0%.
  • the devitrification resistance of the glass can be increased. Therefore, when the B 2 O 3 component is contained, the content thereof is more preferably 0.1%, further preferably 2.5%, and most preferably 5.0%.
  • the content of the B 2 O 3 component is preferably 15%, more preferably 10%, still more preferably 7.9%, and most preferably 8%.
  • the mass ratio of the total content of the SiO 2 component and the B 2 O 3 component to the content of the SiO 2 component (SiO 2 + B 2 O 3 ) / SiO 2 is 1.0 or more. It is preferable that it is 00 or less. By setting the value of this ratio to 1.0 or more and 2.00 or less, it is possible to obtain an effect excellent in durability while obtaining a desired viscosity suitable for thin plate molding. Therefore, the value of (SiO 2 + B 2 O 3 ) / SiO 2 is preferably 1.0, more preferably 1.1, and most preferably 1.2. The value of (SiO 2 + B 2 O 3 ) / SiO 2 is preferably 2.00, more preferably 1.90, and most preferably 1.80.
  • the sum of the contents of the SiO 2 component and the B 2 O 3 component is preferably 19% or more.
  • the sum of the contents of the SiO 2 component and the B 2 O 3 component is preferably 19% or more, more preferably 20% or more, and most preferably 21% or more.
  • the sum of the contents of the SiO 2 component and the B 2 O 3 component is preferably 50% or less, more preferably 45% or less, further preferably 40% or less, and 33% or less. Most preferably.
  • the value of the mass ratio Nb 2 O 5 / SiO 2 with respect to the content of the SiO 2 component of the content of the Nb 2 O 5 component is preferably 0.60 or less.
  • the value of this ratio is preferably 0.60, more preferably 0.56, still more preferably 0.53, and most preferably 0.50.
  • the value of Nb 2 O 5 / SiO 2 may be 0 as the lower limit.
  • the Gd 2 O 3 component is an optional component that can increase the refractive index of the glass when it exceeds 0%.
  • the glass material cost can be reduced by reducing the expensive Gd 2 O 3 component among the rare earth elements to 40.0% or less. Moreover, this can suppress the increase of the Abbe number of the glass more than necessary. Therefore, the content of the Gd 2 O 3 component is preferably 40.0%, more preferably 30.0%, still more preferably 10%, still more preferably 5%, and most preferably 3%.
  • the Al 2 O 3 component and the Ga 2 O 3 component are optional components that can increase the chemical durability of the glass and increase the devitrification resistance of the glass when the content exceeds 0%.
  • the content of each of Al 2 O 3 component and Ga 2 O 3 component is preferably 15%, more preferably 5.0%, and most preferably 3.0%.
  • the MgO component is an optional component that can enhance the meltability of the glass raw material and the devitrification resistance of the glass when it is contained in an amount exceeding 0%.
  • the upper limit of the content of the MgO component is preferably 15%, more preferably 12%, still more preferably 10%, and most preferably 5%.
  • the CaO component is an optional component that can improve the meltability of the glass raw material and the devitrification resistance of the glass when it contains more than 0%.
  • the upper limit of the CaO content is preferably 15%, more preferably 12%, and most preferably 10.3%.
  • the SrO component is an optional component that can enhance the meltability of the glass raw material and the devitrification resistance of the glass when it is contained in an amount exceeding 0%.
  • the content of the SrO component is preferably 15%, more preferably 12%, and most preferably 10%.
  • the total content (mass sum) of RO components (wherein R is one or more selected from the group consisting of Mg, Ca, Sr, and Ba) is preferably 50% or less.
  • the upper limit of the mass sum of the RO component is preferably 50%, more preferably 45%, and most preferably 40%.
  • the lower limit of the mass sum of the RO component is preferably more than 0%, more preferably 5%, still more preferably 7%, and still more preferably, from the viewpoint of enhancing the meltability of the glass raw material and the devitrification resistance of the glass. It may be 10.9%, more preferably 15%, and even more preferably 20%.
  • the Ta 2 O 5 component is an optional component that can increase the refractive index of the glass, increase the devitrification resistance, and increase the viscosity of the molten glass when it contains more than 0%.
  • the material cost of glass can be reduced by making the expensive Ta 2 O 5 component 10% or less. Accordingly, the content of the Ta 2 O 5 component is preferably 10%, more preferably 7%, and most preferably 5%.
  • the TeO 2 component is an optional component that can increase the refractive index and lower the glass transition point when it is contained in excess of 0%.
  • TeO 2 has a problem that it can be alloyed with platinum when a glass raw material is melted in a crucible made of platinum or a melting tank in which a portion in contact with molten glass is formed of platinum.
  • the content of the TeO 2 component is preferably 10%, more preferably 5%, most preferably 3%, and even more preferably not contained.
  • the WO 3 component is an optional component that can increase the refractive index and increase the devitrification resistance of the glass while reducing the coloring of the glass due to other high refractive index components when it contains more than 0%. Therefore, the content of the WO 3 component is more preferably more than 0%, and even more preferably 1.0%. On the other hand, by setting the content of the WO 3 component to 10% or less, the coloring of the glass by the WO 3 component can be reduced and the visible light transmittance can be increased. Accordingly, the upper limit of the content of the WO 3 component is preferably 10%, more preferably 5%, and most preferably 3%.
  • a Bi 2 O 3 component is an optional component that can increase the refractive index and lower the glass transition point when it exceeds 0%.
  • the upper limit of the content of the Bi 2 O 3 component is preferably 10%, more preferably 5%, and most preferably 3%.
  • the Yb 2 O 3 component is an optional component that can increase the refractive index of the glass and increase the Abbe number when it exceeds 0%.
  • the content of the Yb 2 O 3 component is preferably 5%, more preferably 2%, even more preferably 0.9%, still more preferably 0.5%, and no Yb 2 O 3 component is contained. Most preferred.
  • the Rn 2 O component (wherein Rn is one or more selected from the group consisting of Li, Na, K, and Cs) is a component that can be optionally added. However, if added excessively, the viscosity of the glass is lowered, making it difficult to obtain the desired viscosity, and it is difficult to obtain a high refractive index. Therefore, the content of the Rn 2 O component is preferably less than 4%, preferably 2% or less, and most preferably not contained.
  • the Li 2 O component is an optional component that can improve the meltability of the glass and lower the glass transition point when it contains more than 0%. However, if added excessively, the viscosity of the glass becomes low, it becomes difficult to obtain the desired viscosity, and it is difficult to obtain a high refractive index. Therefore, the content is preferably 2% or less, and not contained More preferred.
  • Na 2 O component, K 2 O component, and Cs 2 O component are optional components that can improve the meltability of glass, increase the devitrification resistance of glass, and lower the glass transition point when contained in excess of 0%.
  • the Na 2 O component, the K 2 O component, and the Cs 2 O component Each content is preferably 2% or less, and more preferably each component of Na 2 O, K 2 O and Cs 2 O is not contained.
  • the ZnO component is an optional component that can increase the refractive index and improve the chemical durability when it is contained in an amount of more than 0%. Therefore, the content of the ZnO component is preferably more than 0%, more preferably more than 1.0%. On the other hand, by setting the content of the ZnO component to 10% or less, a decrease in the refractive index of the glass and a decrease in the viscosity can be suppressed, and the occurrence of striae on the glass can be reduced. Therefore, the upper limit of the content of the ZnO component is preferably 10%, more preferably 8%, and most preferably 6%.
  • the P 2 O 5 component when ultra containing 0%, which is an optional component that enhances devitrification resistance of the glass.
  • the content of the P 2 O 5 component is preferably 10.0%, more preferably 5.0%, and still more preferably 3.0%.
  • the GeO 2 component is an optional component that can increase the refractive index of the glass and improve the devitrification resistance when it contains more than 0%.
  • the content of the GeO 2 component is preferably 10.0%, more preferably 8.0%, still more preferably 5.0%, and still more preferably 3.0%.
  • the SnO 2 component When the SnO 2 component is contained in an amount of more than 0%, the SnO 2 component is an optional component that can be refined by reducing the oxidation of the molten glass and can increase the visible light transmittance of the glass.
  • the content of the SnO 2 component is preferably 1.0%, more preferably 0.7%, and still more preferably 0.5%.
  • the Sb 2 O 3 component is an optional component that can degas the molten glass when it contains more than 0%.
  • the content of the Sb 2 O 3 component is preferably less than 0.5%, more preferably 0.4%.
  • the As 2 O 3 component is a component with a high environmental load, its content is preferably less than 0.5%, and more preferably not contained.
  • components defoamed fining glass is not limited to the above Sb 2 O 3 component, a known refining agents in the field of glass production, it is possible to use a defoamer or a combination thereof.
  • each transition metal component such as V, Cr, Mn, Fe, Co, Ni, Cu, Ag and Mo, excluding Ti, Zr, Nb, W, La, Gd, Y, Yb, and Lu, is independent of each other.
  • the glass is not substantially contained because the glass is colored and has absorption at a specific wavelength in the visible range.
  • lead compounds such as PbO are components having a high environmental load, it is desirable that they are not substantially contained, that is, not contained at all except for inevitable mixing.
  • each component of Th, Cd, Tl, Os, Be, and Se has tended to be refrained from being used as a harmful chemical material in recent years, and not only in the glass manufacturing process, but also in the processing process and disposal after commercialization. Until then, environmental measures are required. Therefore, when importance is placed on the environmental impact, it is preferable that these are not substantially contained.
  • the glass of the present invention is produced, for example, as follows. That is, the above raw materials are uniformly mixed so that each component is within a predetermined content range, and the prepared mixture is put into a platinum crucible, and 1100-1500 ° C. in an electric furnace depending on the difficulty of melting the glass composition. It is produced by melting in the temperature range of 2 to 5 hours, stirring and homogenizing, lowering to an appropriate temperature, casting into a mold, and slow cooling.
  • the glass of the present invention preferably has a high refractive index.
  • the refractive index (n d ) of the glass of the present invention is preferably 1.75, more preferably 1.76, and most preferably 1.77.
  • the upper limit of this refractive index is preferably 1.91, more preferably 1.90, and even more preferably 1.89.
  • the glass of the present invention preferably has high dispersion (low Abbe number).
  • the upper limit of the Abbe number ( ⁇ d ) of the glass of the present invention is preferably 45, more preferably 42, still more preferably 40, and most preferably 38.
  • the lower limit of the Abbe number may preferably be 20, more preferably 22, and even more preferably 25.
  • the glass of the present invention preferably has high devitrification resistance, more specifically, a low liquidus temperature. That is, the upper limit of the liquidus temperature of the glass of the present invention is preferably 1300 ° C, more preferably 1250 ° C, and still more preferably 1200 ° C. Thereby, even if the molten glass flows out at a lower temperature, crystallization of the produced glass is reduced, and thus devitrification can be reduced particularly when the glass is formed from the molten state. The influence on the optical characteristics of the optical element can be reduced. Moreover, since glass can be shape
  • the lower limit of the liquidus temperature of the glass of the present invention is not particularly limited, but the liquidus temperature of the glass obtained by the present invention is preferably 500 ° C, more preferably 600 ° C, and even more preferably 700 ° C. Good.
  • liquid phase temperature refers to a 30 ml cullet-shaped glass sample placed in a platinum crucible in a 50 ml capacity platinum crucible, completely melted at 1350 ° C., and cooled to a predetermined temperature. The glass surface and the presence or absence of crystals in the glass are observed immediately after taking out of the furnace and cooling, and indicates the lowest temperature at which no crystals are observed.
  • the predetermined temperature when the temperature is lowered is a temperature in increments of 10 ° C. up to 500 ° C.
  • the viscosity of the glass melt at the liquidus temperature is 10.0 dPa ⁇ s or more.
  • the viscosity of the glass melt at the liquidus temperature is preferably 10.0 dPa ⁇ s or more, more preferably 31.6 dPa ⁇ s or more, and 100.0 dPa ⁇ s or more. Most preferably.
  • the upper limit of the viscosity of the glass melt at the liquidus temperature is not particularly set, but the upper limit of the viscosity range that the glass of the present invention can take is 10 4.5 dPa ⁇ s.
  • the viscosity of the glass melt at the liquidus temperature should be measured by measuring the liquidus temperature of the target glass in advance, keeping the glass at that temperature, and measuring it with a ball pulling-up viscometer (manufactured by Opto Corporation). Can do.
  • the glass of the present invention has high visible light transmittance, in particular, high transmittance of light on the short wavelength side of visible light, and thereby less coloration.
  • the wavelength ( ⁇ 70 ) showing a spectral transmittance of 70% in a sample having a thickness of 10 mm is preferably 600 nm, more preferably 550 nm, still more preferably 500 nm, further preferably The upper limit is 470 nm.
  • the shortest wavelength ( ⁇ 5 ) having a spectral transmittance of 5% in a sample having a thickness of 10 mm is preferably 470 nm, more preferably 460 nm, and still more preferably 400 nm.
  • this glass is preferably used for an optical element that transmits light such as an organic EL lighting substrate or a lens. Can do.
  • the glass of the present invention preferably has a glass transition point (Tg) of 625 ° C. or higher. Thereby, it becomes easy to form the molten glass into a thin plate shape. Accordingly, the glass transition point of the optical glass of the present invention is preferably 625 ° C., more preferably 650 ° C., further preferably 700 ° C., and more preferably 710 ° C. The glass transition point of the present invention may preferably have an upper limit of 800 ° C.
  • the glass of the present invention Since the glass of the present invention has a liquidus temperature and viscosity suitable for forming molten glass into a thin plate shape, the molten glass can be directly formed into a thin plate shape by a known method. Examples of the method for forming the glass of the present invention into a thin plate include a float method, a downdraw method, a fusion method, and an aqua float method. Since the glass of the present invention can directly form molten glass into a thin plate shape, it is possible to produce organic EL lighting substrates and other thin plates for optical use at low cost. In addition, since the glass of the present invention has a high viscosity at the liquidus temperature, it can be formed into a thin plate using a direct press method.
  • the direct press method is a method in which molten glass is directly press-molded with at least two molds facing each other.
  • the direct press method produces, for example, a glass substrate for molding a molded product of an optical element group for wafer level optics or a molded product of an optical element group for wafer level optics by a reheat press method. It is possible to use it suitably when doing.
  • the glass of this invention can produce a glass molded object, for example using the means of grinding, a grinding
  • the means for producing the glass molded body is not limited to these means, and the direct press method or the reheat press method can also be used.
  • the glass molded body formed from the glass of the present invention is useful for various optical elements and optical designs, but it is particularly preferable to use them for optical elements such as lenses and prisms.
  • This makes it possible to form a glass molded body with a large diameter, so that the optical elements can be enlarged, but with high definition and high precision imaging characteristics and projection when used in optical equipment such as cameras and projectors. The characteristics can be realized.
  • composition of Examples of the Glass of the Present Invention Refractive Index (n d ), Abbe Number ( ⁇ d ), Wavelengths ( ⁇ 5 and ⁇ 70 ) with 5% and 70% Spectral Transmittance, Liquid Phase Tables 1 to 27 show the results of temperature and viscosity at the liquidus temperature and the glass transition point (Tg).
  • Tg glass transition point
  • the glasses of the examples of the present invention are used as ordinary optical glasses such as oxides, hydroxides, carbonates, nitrates, fluorides, hydroxides, metaphosphate compounds, etc., as raw materials for the respective components.
  • the high-purity raw materials are selected and weighed so as to have the composition ratio of each example shown in the table and mixed uniformly, and then put into a platinum crucible.
  • the melting difficulty of the glass composition After melting for 2 to 5 hours in a temperature range of 1100 to 1500 ° C., the mixture was homogenized with stirring, cast into a mold or the like, and slowly cooled to produce a glass.
  • the refractive index and the Abbe number of the glass of the example were measured based on the Japan Optical Glass Industry Association Standard JOGIS01-2003.
  • the refractive index and the Abbe number were determined by measuring the glass obtained at a slow cooling rate of -25 ° C./hr.
  • the transmittance of the glass of the example was measured in accordance with Japan Optical Glass Industry Association Standard JOGIS02-2003. Specifically, a face parallel polished product having a thickness of 10 ⁇ 0.1 mm was measured for a spectral transmittance of 200 to 800 nm in accordance with JISZ8722, and ⁇ 5 (wavelength when the transmittance was 5%) and ⁇ 70 (transmittance). Wavelength at 70%).
  • the liquid phase temperature of the glass of the example is 10 ° C. from 1300 ° C. to 500 ° C. by putting a 30 cc cullet-shaped glass sample into a platinum crucible in a platinum crucible having a capacity of 50 ml and completely melting at 1350 ° C. Decrease to any temperature set in steps and hold for 12 hours, take out outside the furnace and cool, immediately observe the glass surface and the presence or absence of crystals in the glass, find the lowest temperature where no crystals are observed It was.
  • the viscosity of the glass melt at the liquidus temperature of the glass of the example is determined by measuring the liquidus temperature of the target glass in advance and keeping the glass at that temperature, while the ball pulling-up viscometer (Opto Enterprise Co., Ltd.) Manufactured).
  • the glass transition point (Tg) of the glass of an Example was calculated
  • the sample used for the measurement was ⁇ 4.8 mm and a length of 50 to 55 mm, and the temperature elevation rate was 4 ° C./min.
  • the glasses of the examples of the present invention all have a refractive index nd of 1.75 or more, the viscosity of the glass melt at the liquidus temperature is 10.0 dPa ⁇ s or more, and the molten glass is formed into a thin plate shape. It became clear that it was easy. Moreover, the liquidus temperature of the glass of the Example of this invention was 1300 degrees C or less, and was in the desired range. For this reason, it became clear that the optical glass of the Example of this invention has low liquidus temperature, and high devitrification resistance.
  • the glass of the present invention is suitable for organic EL lighting substrate applications, and further suitable for lenses and other optical element applications.

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PCT/JP2014/082470 2013-12-27 2014-12-08 ガラス WO2015098485A1 (ja)

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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3441372A4 (en) * 2016-04-04 2019-07-31 Ohara Inc. OPTICAL GLASS, MANUFACTURING MATERIAL AND OPTICAL ELEMENT

Families Citing this family (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102016107934B4 (de) 2016-04-28 2023-07-13 Schott Ag Verfahren zur Herstellung hochbrechender Dünnglassubstrate
JP7545192B2 (ja) * 2016-10-03 2024-09-04 株式会社オハラ 光学ガラス、プリフォーム及び光学素子
JP7224099B2 (ja) * 2016-10-03 2023-02-17 株式会社オハラ 光学ガラス、プリフォーム及び光学素子
WO2020004141A1 (ja) * 2018-06-26 2020-01-02 日本電気硝子株式会社 ガラス板
JP7354109B2 (ja) * 2018-07-18 2023-10-02 株式会社オハラ 光学ガラス及び光学素子
CN109502964B (zh) * 2018-12-07 2023-03-28 成都光明光电股份有限公司 重镧火石玻璃及其预制件、光学元件和光学仪器
CN109665714B (zh) * 2019-02-28 2021-06-29 成都光明光电股份有限公司 光学玻璃、玻璃预制件、光学元件及光学仪器
CN110204199B (zh) * 2019-06-27 2022-05-17 成都光明光电股份有限公司 具有负向反常色散的玻璃
CN115072993A (zh) * 2019-06-27 2022-09-20 成都光明光电股份有限公司 光学玻璃、玻璃预制件、光学元件和光学仪器

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5950048A (ja) * 1982-09-16 1984-03-22 Ohara Inc 光学ガラス
JPS62132741A (ja) * 1985-11-29 1987-06-16 コ−ニング　グラス　ワ−クス 光学および眼用ガラス
JP2000344542A (ja) * 1999-05-06 2000-12-12 Carl Zeiss:Fa 無鉛光学ガラス
JP2006219365A (ja) * 2005-01-17 2006-08-24 Ohara Inc ガラス
JP2009263141A (ja) * 2008-03-31 2009-11-12 Ohara Inc 光学ガラス、光学素子及び光学機器

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4507393A (en) * 1983-08-11 1985-03-26 Schott Glass Technologies, Inc. Highly prefractive, low dispersion optical glass suitable for multifocal corrective lenses
JPS60264342A (ja) * 1984-06-09 1985-12-27 Ohara Inc 高屈折立光学ガラス
JPH0230640A (ja) * 1988-07-19 1990-02-01 Nippon Electric Glass Co Ltd ファイバープレート用芯ガラス
JP3238740B2 (ja) * 1992-03-17 2001-12-17 株式会社オハラ 光学ガラス
DE19848077C1 (de) * 1998-10-19 2000-01-27 Schott Glas Bleifreie optische Gläser
KR101276587B1 (ko) * 2009-07-08 2013-06-19 니폰 덴키 가라스 가부시키가이샤 유리판

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5950048A (ja) * 1982-09-16 1984-03-22 Ohara Inc 光学ガラス
JPS62132741A (ja) * 1985-11-29 1987-06-16 コ−ニング　グラス　ワ−クス 光学および眼用ガラス
JP2000344542A (ja) * 1999-05-06 2000-12-12 Carl Zeiss:Fa 無鉛光学ガラス
JP2006219365A (ja) * 2005-01-17 2006-08-24 Ohara Inc ガラス
JP2009263141A (ja) * 2008-03-31 2009-11-12 Ohara Inc 光学ガラス、光学素子及び光学機器

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3441372A4 (en) * 2016-04-04 2019-07-31 Ohara Inc. OPTICAL GLASS, MANUFACTURING MATERIAL AND OPTICAL ELEMENT
EP3677559A1 (en) * 2016-04-04 2020-07-08 Ohara Inc. Optical glass, preform material and optical element

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