WO2011118524A1 - ディスプレイ用カバーガラスおよびディスプレイ - Google Patents
ディスプレイ用カバーガラスおよびディスプレイ Download PDFInfo
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- WO2011118524A1 WO2011118524A1 PCT/JP2011/056556 JP2011056556W WO2011118524A1 WO 2011118524 A1 WO2011118524 A1 WO 2011118524A1 JP 2011056556 W JP2011056556 W JP 2011056556W WO 2011118524 A1 WO2011118524 A1 WO 2011118524A1
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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
- C03C3/076—Glass compositions containing silica with 40% to 90% silica, by weight
- C03C3/095—Glass compositions containing silica with 40% to 90% silica, by weight containing rare earths
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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
- 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
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- C—CHEMISTRY; METALLURGY
- C09—DYES; PAINTS; POLISHES; NATURAL RESINS; ADHESIVES; COMPOSITIONS NOT OTHERWISE PROVIDED FOR; APPLICATIONS OF MATERIALS NOT OTHERWISE PROVIDED FOR
- C09K—MATERIALS FOR MISCELLANEOUS APPLICATIONS, NOT PROVIDED FOR ELSEWHERE
- C09K2323/00—Functional layers of liquid crystal optical display excluding electroactive liquid crystal layer characterised by chemical composition
- C09K2323/03—Viewing layer characterised by chemical composition
- C09K2323/033—Silicon compound, e.g. glass or organosilicon
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/26—Web or sheet containing structurally defined element or component, the element or component having a specified physical dimension
- Y10T428/266—Web or sheet containing structurally defined element or component, the element or component having a specified physical dimension of base or substrate
Definitions
- the present invention relates to a cover glass for a display and a display provided with the cover glass.
- a protective plate is provided to prevent an impact or external force from being applied to the display (for example, Patent Document 1). .
- Patent Document 1 a protective plate using chemically strengthened glass that has strength even if it is a thin plate has been proposed with a reduction in thickness of portable terminal devices and portable devices (for example, Patent Document 2).
- Patent Documents 1 and 2 The entire description of Patent Documents 1 and 2 is specifically incorporated herein by reference.
- the protective plate When using glass as the protective plate, the protective plate is called a cover glass. As described above, the cover glass has been made thinner, but it is considered that an ultra-thin plate having a thickness of 1.0 mm or less will be required in the future.
- the present invention has been made in order to solve the above-mentioned problems caused by the thinning of the cover glass, and provides a high-quality and high mechanical strength thin cover glass and a display including the cover glass. With the goal.
- the present invention provides a means for solving the above-described problems, (1)
- a cover glass used to transmit an image displayed by the image display unit while covering the image display unit of the display Converted to oxide standards and expressed in mol%, SiO 2 60-75%, Al 2 O 3 0-12% (However, the total content of SiO 2 and Al 2 O 3 is 68% or more), B 2 O 3 0-10%, 5 to 26% in total of Li 2 O and Na 2 O, K 2 O 0-8% (However, the total content of Li 2 O, Na 2 O and K 2 O is 26% or less), MgO, CaO, SrO, BaO and ZnO in total 0 to 18%, ZrO 2 , TiO 2 and HfO 2 in total 0 to 5%,
- the content of Sn oxide and Ce oxide is 0.1 to 3.5% by mass, and the ratio of the content of Sn oxide to the total content of Sn oxide and Ce oxide Glass with (Sn oxide content / (Sn oxide content + Ce oxide
- a cover glass having a high mechanical strength and a plate thickness of 1.0 mm or less and a display including the cover glass can be provided.
- the present invention is converted to oxide standards, in mol% display, SiO 2 60-75%, Al 2 O 3 0-12% (However, the total content of SiO 2 and Al 2 O 3 is 68% or more), B 2 O 3 0-10%, 5 to 26% in total of Li 2 O and Na 2 O, K 2 O 0-8% (However, the total content of Li 2 O, Na 2 O and K 2 O is 26% or less), MgO, CaO, SrO, BaO and ZnO in total 0 to 18%, ZrO 2 , TiO 2 and HfO 2 in total 0 to 5%,
- the content of Sn oxide and Ce oxide is 0.1 to 3.5% by mass, and the ratio of the content of Sn oxide to the total content of Sn oxide and Ce oxide Glass with (Sn oxide content / (Sn oxide content + Ce oxide content)) of 0.01 to 0.99 and Sb oxide content of 0 to
- Sn has a strong action of actively releasing oxygen gas in the temperature range of about 1400-1600 ° C and promoting clarification
- Ce is oxygen in the glass melt at a temperature range of 1200-1400 ° C. It works to take in gas and fix it as a glass component.
- the viscosity of the glass at 1400 ° C. where the clarification temperature range of Sn and the clarification temperature range of Ce are in contact has a great influence on the clarification efficiency.
- the viscosity at 1400 ° C. is high, the movement of bubbles in the glass melt tends to be inhibited, and the clarification efficiency tends to decrease. Therefore, it is desired to adjust the glass composition so that the viscosity at 1400 ° C. is 5 ⁇ 10 3 dPa ⁇ s or less, more preferably 1 ⁇ 10 3 dPa ⁇ s or less. From such a viewpoint, the composition of the glass A is suitable.
- the glass A is an amorphous glass and has excellent visible light transmittance and workability compared to crystallized glass. It is also a glass suitable for chemical strengthening while having excellent chemical durability.
- the composition of the glass A will be described in detail.
- the contents of the Sn oxide, Ce oxide, and Sb oxide are the externally added amounts (except for the Sn oxide, Ce oxide, and Sn oxide described later).
- the total content of the glass components is 100% by mass, the addition amount is expressed by mass%), and the component content and total content are expressed in mol%. To do.
- SiO 2 is a glass network-forming component and is an essential component that functions to improve glass stability, chemical durability, and particularly acid resistance. If the content of SiO 2 is less than 60%, the above function cannot be obtained sufficiently, and if it exceeds 75%, undissolved material is generated in the glass, or the viscosity of the glass at the time of clarification becomes too high, resulting in bubble breakage. It becomes insufficient. In a glass containing unmelted material, the undissolved material becomes a light scattering source, which deteriorates the image quality of the display. As for the glass containing bubbles, the bubbles serve as a light scattering source to reduce the image quality and reduce the mechanical strength of the glass. From the above, the SiO 2 content is set to 60 to 75%. A preferable range of the content of SiO 2 is 60 to 70%, a more preferable range is 62 to 68%, and a further preferable range is 63 to 67%.
- Al 2 O 3 also contributes to the formation of a glass network, improving the glass stability and chemical durability, and increasing the ion exchange rate during chemical strengthening.
- the content of Al 2 O 3 exceeds 12%, the meltability of the glass is lowered and unmelted products are likely to be generated. Therefore, the content of Al 2 O 3 is 0 to 12%.
- a preferred range for the content of Al 2 O 3 is 0.5 to 11%, and a more preferred range is 4 to 11%.
- the total content of SiO 2 and Al 2 O 3 is set to 68% or more.
- a preferable range of the total content of SiO 2 and Al 2 O 3 is 70% or more.
- B 2 O 3 functions to reduce brittleness and improve meltability.
- the content of B 2 O 3 is set to 0 to 10%.
- the preferable range of the content of B 2 O 3 is 0 to 5%, more preferable range is 0 to 2%, still more preferably 0 to 1%, and no further introduction. preferable.
- Li 2 O and Na 2 O function to improve the meltability and moldability of glass among alkali metal oxides. Moreover, when it is set as the glass for chemical strengthening, it is also a component which bears the ion exchange at the time of chemical strengthening. If the total content of Li 2 O and Na 2 O is less than 5%, the above function cannot be obtained sufficiently. In particular, as described above, when relatively large amounts of SiO 2 and Al 2 O 3 are introduced to improve chemical durability, the total content of Li 2 O and Na 2 O is less than 5%. If it exists, the viscosity of the glass at the time of clarification is too high, so that a sufficient clarification effect cannot be obtained.
- the total content of Li 2 O and Na 2 O exceeds 26%, chemical durability, particularly acid resistance, is lowered. Therefore, the total content of Li 2 O and Na 2 O is in the range of 5 to 26%.
- a preferable range of the total content of Li 2 O and Na 2 O is 10 to 25%, a more preferable range is 15 to 25%, and a further preferable range is 20 to 24%.
- K 2 O also works to improve the meltability and formability of the glass. However, when the content of K 2 O exceeds 8%, chemical durability, particularly acid resistance is lowered. Therefore, the content of K 2 O is 0 to 8%. A preferable range of the content of K 2 O is 0 to 5%, and a more preferable range is 0 to 2%.
- MgO, CaO, SrO, BaO and ZnO work to improve the meltability, moldability and glass stability of the glass and increase the thermal expansion coefficient.
- the total content of MgO, CaO, SrO, BaO and ZnO is set to 0 to 18%.
- a preferable range of the total content of MgO, CaO, SrO, BaO and ZnO is 0 to 15%. Since MgO, CaO, SrO, BaO and ZnO have the effect of reducing the ion exchange rate during chemical strengthening, it is desirable to keep the content of these components low when emphasizing the efficiency of chemical strengthening. In that case, a preferable range of the total content of MgO, CaO, SrO, BaO and ZnO is 0 to 7%, and a more preferable range is 0 to 5%.
- the total content of MgO and CaO is preferably in the range of 4 to 14%.
- the preferable range of the MgO content is 2 to 7%
- the preferable range of the CaO content is 2 to 9%.
- ZrO 2 , TiO 2 , and HfO 2 function to increase rigidity and fracture toughness and improve chemical durability, particularly alkali resistance, but when introduced excessively, meltability is reduced. Therefore, the total content of ZrO 2 , TiO 2 and HfO 2 is set to 0 to 5%.
- a preferable range of the total content of ZrO 2 , TiO 2 and HfO 2 is 1 to 5%, and a more preferable range is 1 to 4%.
- ZrO 2 has a large effect of improving chemical durability and is also excellent in enhancing ion exchange efficiency during chemical strengthening, so it is preferable to contain ZrO 2 .
- a preferable range of the content of ZrO 2 is 1 to 5%, more preferably 1 to 4%. Since TiO 2 produces a deposit on the glass surface when the glass is immersed in water, the content of TiO 2 is preferably in the range of 0-2%, more preferably in the range of 0-1%. Preferably, no introduction is more preferable.
- HfO 2 is a rare component, and in terms of cost, its content is preferably in the range of 0 to 2%, more preferably in the range of 0 to 1%, and even more preferably not introduced.
- P 2 O 5 can also be introduced in a small amount within a range that does not impair the object of the invention.
- the content is preferably 0 to 1%, preferably 0 to 0.5%. % Is more preferable, 0 to 0.3% is more preferable, and introduction is not more preferable.
- Glass A containing a relatively large amount of SiO 2 and Al 2 O 3 contains an alkali metal component but has a high glass temperature during clarification.
- Sb oxide is inferior in fining effect as compared with Sn oxide and Ce oxide, and rather in glass added with Sn oxide, the fining effect is rather lowered. If the Sb oxide content exceeds 0.1%, residual bubbles in the glass rapidly increase in the coexistence with Sn oxide. Therefore, the Sb oxide content is limited to 0.1% or less.
- the preferable range of the content of Sb oxide is 0 to 0.05%, the more preferable range is 0 to 0.01%, the more preferable range is 0 to 0.001%, and no Sb oxide is added (containing Sb Glass) is particularly preferred.
- the Sb oxide means an oxide such as Sb 2 O 3 or Sb 2 O 5 dissolved in the glass regardless of the valence of Sb.
- Sb oxide has a larger environmental impact than Sn oxide and Ce oxide, so it is preferable from the viewpoint of reducing the environmental impact by reducing the use amount of Sb oxide to zero.
- halogen other than F that is, Cl, Br, or I
- F halogen other than F
- halogens also volatilize from the molten glass, causing striae, and reducing the image quality of the display.
- glass A Pb, Cd, etc. are substances that adversely affect the environment, so it is preferable to avoid introducing them.
- ⁇ Glass containing no Sb or As can be well formed by the down draw method or the float method.
- Glass A is made through a process of melting a glass raw material, a process of refining the molten glass obtained by melting, a process of homogenizing the clarified molten glass, and a process of flowing out and forming the homogenized molten glass. .
- the clarification process is performed at a relatively high temperature
- the homogenization process is performed at a relatively low temperature.
- bubbles are actively generated in the glass, and fine bubbles contained in the glass are taken in to form large bubbles, thereby facilitating clarification.
- a technique of eliminating bubbles by incorporating oxygen present as a gas in the glass as a glass component is effective.
- Sn oxide is excellent in the function of promoting clarification by releasing oxygen gas at a high temperature and taking in the fine bubbles contained in the glass to make it easier to float.
- Ce oxide has an excellent function of eliminating bubbles by incorporating oxygen present as a gas in glass at low temperature as a glass component.
- Sn oxide has a strong effect of removing relatively large bubbles and extremely small bubbles.
- Ce oxide is added together with Sn oxide, the density of large bubbles of about 50 ⁇ m to 0.3 mm is drastically reduced to several tenths.
- the coexistence of Sn oxide and Ce oxide can enhance the glass refining effect in a wide temperature range from high temperature to low temperature, and the introduction of Sb oxide, As, and F was restricted. Even with glass, sufficient bubbles can be removed.
- the total content of Sn oxide and Ce oxide is set to 0.1 to 3.5%.
- a preferable range of the total content of Sn oxide and Ce oxide is 0.1 to 2.5%, a more preferable range is 0.1 to 1.5%, and a further preferable range is 0.5 to 1.5%.
- the ratio of the Sn oxide content to the total content of Sn oxide and Ce oxide is 0.01.
- the range is up to 0.99.
- a preferable range of the ratio is 0.02 or more, a more preferable range is 1/3 or more, a further preferable range is 0.35 to 0.99, a more preferable range is 0.45 to 0.99, a still more preferable range is 0.45 to 0.98, and an even more preferable range is 0.45 to 0.85.
- the ratio is less than 0.01 or exceeds 0.99, it becomes difficult to obtain a synergistic effect of the clarification action of Sn oxide at a high temperature and the clarification action of Ce oxide at a low temperature.
- the addition is biased to either Sn oxide or Ce oxide, the oxide that is introduced in a large amount among Sn oxide and Ce oxide is likely to remain undissolved, and undissolved material is contained in the glass. It tends to occur.
- Sn has the property of absorbing infrared light in glass, and when used as a cover glass, it absorbs heat rays, for example, infrared light components in sunlight, and damages due to heat ray irradiation inside the display. Also works to reduce.
- Ce uses an ultraviolet lamp and emits blue fluorescence when irradiated with high-intensity ultraviolet light. Fluorescence is generated by irradiating glass A containing Ce with ultraviolet light, and glass A and Ce-free glass that have the same appearance and are difficult to distinguish visually by the presence or absence of blue fluorescence. Can do.
- the cover glass and glass base material which consist of glass A or glass A have an identification function.
- this identification function it is not necessary to analyze the composition of the glass in the cover glass production process and display production process in which a plurality of types of glass are mixed, and it is possible to quickly determine whether the cover glass is made of glass A. It can be inspected and contamination between glass A and other glasses can be avoided.
- the glass can be easily identified, so that the cause of the trouble and the problem can be solved quickly.
- UV light is emitted as described above, and the fluorescence emitted by Ce is used.
- the edge part of a cover glass can be detected and the position alignment operation
- the Sn oxide content is preferably 0.1% or more from the viewpoint of obtaining the above-mentioned clarification effect and infrared light absorption effect. However, if it exceeds 3.5%, it precipitates as a foreign substance in the glass and deteriorates the image quality of the display. It becomes a factor to make. Therefore, the Sn oxide content is preferably 0.1 to 3.5%. From the above viewpoint, a more preferable range of the Sn content is 0.1 to 2.5%, a further preferable range is 0.1 to 1.5%, and a still more preferable range is 0.5 to 1.0%.
- the Sn oxide means an oxide such as SnO or SnO 2 dissolved in the glass regardless of the valence of Sn.
- the content of Sn oxide is the total content of oxides such as SnO and SnO 2 .
- the Ce oxide is preferably 0.1% or more, but if it exceeds 3.5%, the reaction with the refractory or platinum constituting the melting vessel or The reaction with the molding tool for molding the glass increases, the impurities increase, and the internal quality of the glass tends to decrease or the coloration tends to increase. Further, the excessive addition of Ce oxide absorbs visible light, particularly light in the visible short wavelength region, and the glass tends to be colored by Ce itself. Therefore, the Ce oxide content is preferably 0.1 to 3.5%. A more preferable range of the Ce content is 0.5 to 2.5%, a more preferable range is 0.5 to 1.5%, and a further preferable range is 0.5 to 1.0%.
- the Ce oxide means an oxide such as CeO 2 or Ce 2 O 3 dissolved in the glass regardless of the valence of Ce. The content of Ce oxide is the total content of oxides such as CeO 2 and Ce 2 O 3 .
- the forming of the sheet glass that is the base material of the cover glass is performed by, for example, a down draw method or a float method.
- Glass A containing Sn oxide is preferable in that it is stably formed into a thin plate by the above method.
- heat radiation is emitted from the molten glass in a high temperature state, but Sn in the glass absorbs infrared light, so the heat radiation is absorbed in the glass, and the cooling speed by the heat radiation is reduced. Viscosity increase speed is slightly reduced, which is advantageous for thinning.
- a sulfate can be added to glass A in the range of 0 to 1% as a fining agent.
- mirabilite Na 2 SO 4
- K 2 SO 4 Li 2 SO 4
- MgSO 4 MgSO 4
- CaSO 4 CaSO 4
- the viscosity at 1400 ° C. is preferably 10 3 dPa ⁇ s or less, and more preferably 10 2.7 dPa ⁇ s or less, in order to further enhance the clarification effect.
- the density of residual bubbles contained in the unit mass of glass is 60 pieces / kg or less, preferably 40 pieces / kg or less, more preferably 20 pieces / kg or less, and even more preferably 10 pieces / kg.
- it can be more preferably 2 pieces / kg or less, and still more preferably 0 pieces / kg. Therefore, glass suitable for the cover glass can be mass-produced with high productivity.
- a glass raw material is prepared by weighing and mixing oxides, carbonates, nitrates, sulfates, hydroxides, and clarifying agents such as SnO 2 and CeO 2 so that glass A is obtained.
- a glass raw material is melted, and the obtained molten glass is clarified and formed to obtain glass A.
- a preferred embodiment of the glass A production method is a method in which the molten glass is held at 1400 to 1600 ° C., then cooled to 1200 to 1400 ° C., and then molded.
- the viscosity of the glass is lowered to make the bubbles in the glass easy to float, and the clarification promoting effect by releasing oxygen of Sn is obtained.
- By lowering the temperature and maintaining the temperature at 1200 to 1400 ° C. it is possible to dramatically improve bubble breakage by utilizing the oxygen uptake of Ce.
- 1400 viscosity at °C is 5 ⁇ 10 3 dPa ⁇ s or less, and characteristics of the glass that more preferably 1 ⁇ 10 3 dPa ⁇ s or less, Sn and Ce Due to the synergistic effect of the coexistence of bubbles, the bubble breakage is remarkably improved.
- TL / TH is preferably 0.5 or less, and more preferably 0.2 or less.
- TL / TH is preferably larger than 0.01, more preferably larger than 0.02, still more preferably larger than 0.03, and larger than 0.04. It is even more preferable.
- the temperature difference when the temperature is lowered from the range of 1400 to 1600 ° C to the range of 1200 to 1400 ° C is preferably set to 30 ° C or more, and is preferably set to 50 ° C or more from the standpoint of enhancing the foaming effect of each of Sn and Ce. More preferably, it is more preferably 80 ° C. or more, further preferably 100 ° C. or more, and further preferably 150 ° C. or more.
- the upper limit of the temperature difference is 400 ° C.
- the addition amount of Sn and Ce so that the density of residual bubbles in the glass is 60 pieces / kg or less.
- the viscosity at 1400 ° C. is 10 3 dPa ⁇ s or less
- the density of residual bubbles in the glass can be further reduced.
- it is preferable to determine the addition amount of Sn and Ce so that the density of residual bubbles in the glass is 40 pieces / kg or less, and to determine the addition amount of Sn and Ce so as to be 20 pieces / kg or less.
- the addition amount of Sn and Ce is more preferably determined to be 10 pieces / kg or less, more preferably the addition amount of Sn and Ce is set to 2 pieces / kg or less, more preferably 0 piece / kg. It is particularly preferable to determine the addition amount of Sn and Ce so as to be kg. Even if residual bubbles are present, the size of all the bubbles can be reduced to 0.3 mm or less.
- a melting tank for heating and vitrifying a glass raw material a clarification tank is composed of a refractory material such as an electroformed brick or a fired brick, and a connection pipe for connecting the work tank, the clarification tank and the work tank, or
- the outflow pipe is preferably composed of platinum or a platinum alloy (referred to as platinum-based material).
- platinum-based material Both the melt in the melting tank in which the raw material is vitrified and the molten glass in the clarification tank that is at the highest temperature during the glass production process exhibit high erodibility.
- the platinum-based material exhibits excellent corrosion resistance, when it comes into contact with highly corrosive glass, it is corroded by the glass and mixed into the glass as a platinum solid.
- platinum solids exhibit erosion resistance, platinum once mixed in the glass as a solid does not completely dissolve in the glass but remains as a foreign substance in the molded glass.
- the refractory is corroded and mixed in the glass, it dissolves in the glass and hardly remains as a foreign substance. Therefore, it is desired that the melting tank and the clarification tank be made of refractory.
- the work tank is made of refractory, the surface of the refractory melts into the molten glass, causing striae in the glass being homogenized, resulting in inhomogeneity.
- the work tank, connecting pipe, and outflow pipe are composed of platinum-based materials that are difficult to dissolve in the glass. It is desirable that the stirrer for stirring and homogenizing the molten glass is also made of a platinum-based material.
- the cover glass of the present invention is produced by, for example, heating and melting a glass raw material, forming it into a sheet shape by a downdraw method, a float method or the like to obtain a glass base material, and then processing the glass base material. Can do.
- the melting of the glass is as described in the manufacturing method of the glass A.
- a bowl-shaped body made of a ZrO 2 refractory having a groove for guiding molten glass at the top is used. And by making molten glass overflow from the said groove
- the glass in the form of a sheet is joined so as not to interfere with the downward movement of the glass, in order to improve the flatness of the sheet glass.
- the main surface of the glass base material formed by the downdraw method since the surface in contact with the molded body is bonded by the glass merging below the molded body, the trace of contact with the molded body disappears, and such a trace does not occur on the main surface of the sheet glass. Therefore, even if the main surface of the glass base material formed by the downdraw method is not polished, it is possible to cut a glass having a required shape from the glass base material by etching or the like as will be described later to make a cover glass. However, the main surface of the glass base material may be appropriately polished.
- molten glass is poured onto a molten metal in a float bath and pulled into a horizontal direction to form a sheet.
- the float method may be locally cooled by sandwiching both sides of the glass being formed by a pair of knurled rolls.
- the sheet-shaped glass is continuously moved from the forming zone to the annealing zone to perform annealing.
- a continuous long sheet glass from forming to annealing is cut to a required length after annealing and sent to a subsequent process.
- the sheet glass whose distortion is reduced by annealing is cut into a size that can be easily processed into a cover glass, if necessary.
- the glass plate thus obtained is called a glass base material.
- the cover glass contour shape is not necessarily composed only of straight lines, but is often composed of complex contour lines such as shapes including curves. Moreover, since the thickness is as thin as 1.0 mm or less, there is a problem that it is easily damaged when a large force is applied in the processing step. In order to cope with such a problem, a method of cutting out a cover glass from a glass base material by etching is preferable. For this purpose, first, a resist is used to expose a portion of the glass surface corresponding to the contour of the cover glass to be obtained on the main surface of the glass base material by a known method, and the region surrounded by the contour is formed of the resist. Make it covered. After the resist pattern is formed in this way, the glass base material is etched with an etchant using this pattern as a mask, and the cover glass is cut out from the glass base material.
- the end face of the cut cover glass can be suppressed from being roughened by etching, and the surface roughness (arithmetic average roughness Ra) of the end face can be 10 nm or less. it can.
- the end face of the cover glass has very high smoothness, and microcracks formed such as mechanical cutting do not occur.
- the microcracks on the end face are often the starting point of fracture, and the mechanical strength can be increased by smoothing the end.
- the method for etching the glass base material may be either wet etching (wet etching) or dry etching (dry etching). Wet etching is preferable from the viewpoint of reducing the processing cost.
- Any etchant can be used for wet etching as long as it can etch a glass substrate.
- an acidic solution containing hydrofluoric acid as a main component or a mixed acid containing at least one acid among sulfuric acid, nitric acid, hydrochloric acid, and silicic acid can be used.
- the etchant used for dry etching is not particularly limited as long as it can etch a glass substrate.
- a fluorine-based gas can be used.
- the cover glass can be processed by known laser cutting and machining.
- glass cut into a predetermined shape by water jet, sand blasting, laser and mechanical scribe is ground using, for example, a grindstone electrodeposited with diamond of about # 400 to 800 to obtain a desired shape. it can.
- Innumerable microcracks remain on the processed surface of these lasers and machined glass, and these glass substrates are etched by removing the microcracks by performing the above wet etching. Similar mechanical strength can be obtained.
- the cover glass of the present invention has a thickness of 1.0 mm or less, preferably 0.8 mm or less, more preferably 0.5 mm or less.
- the lower limit of the thickness of the cover glass of the present invention can be appropriately set in consideration of the mechanical strength and application of the cover glass of the present invention. For example, it is 0.1 mm or more, preferably 0.2 mm or more, more preferably It is 0.25 mm or more, more preferably 0.3 mm or more.
- Glass A is suitable as a chemical strengthening glass.
- the chemical strengthening of the glass A is performed, for example, by immersing the glass A processed into a desired cover glass shape in an alkali molten salt.
- As the molten salt sodium nitrate molten salt, potassium nitrate molten salt, or a mixture of the two kinds of molten salts can be used.
- Glass A contains at least one of Li 2 O and Na 2 O as a glass component.
- the glass A contains Li 2 O component is chemically strengthened using sodium molten salt or sodium molten salt and potassium molten salt, if the glass A does not contain Li 2 O, i.e., Li 2 O, Na When only Na 2 O is contained in 2 O, it may be chemically strengthened using potassium molten salt.
- the chemical strengthening treatment refers to a part of the ions contained in the glass from the ions contained in the chemical strengthening treatment liquid by bringing the glass surface into contact with the chemical strengthening treatment liquid (molten salt). It is also intended to chemically strengthen the glass substrate by replacing it with larger ions.
- the molten salt temperature at the time of chemical strengthening is higher than the strain point of glass and lower than the glass transition temperature, and is in a temperature range in which the molten salt is not thermally decomposed.
- the concentration of each alkali ion in the molten salt gradually changes, and glass components other than Li and Na are dissolved in a minute amount. As a result, the processing conditions deviate from the optimum range as described above.
- the variation in chemical strengthening due to the change over time of the molten salt can be reduced by adjusting the composition of the glass A as described above, but also by setting the concentration of K ions in the molten salt high, The variation can be reduced.
- the chemical strengthening treatment is performed by observing and confirming the cross section of the glass (the surface to cut the treatment layer) by the Babinet method, alkali ions (for example, Li + , Na + , K + ) This can be confirmed by a method of measuring the distribution in the depth direction (Sernamon method) or the like.
- the cover glass of the present invention has an extremely thin thickness of 1.0 mm or less, preferably 0.8 mm or less, more preferably 0.5 mm or less, the residual foam at the time of glass melting is suppressed to an extremely low level.
- the compressive stress layer formed by chemical strengthening may be 5 ⁇ m or more.
- a preferable range of the thickness of the compressive stress layer is 50 ⁇ m or more, and a more preferable range is 100 ⁇ m or more.
- the upper limit of the thickness of the compressive stress layer may be determined based on the plate thickness.
- the compressive stress layer of the cover glass has the same thickness on both the front and back sides, but if there is no tensile stress layer between the compressive stress layers, it will not be chemically strengthened, so the upper limit of the thickness of the compressive stress layer should be determined based on the plate thickness Good.
- the compressive stress is preferably 300 MPa or more, more preferably 600 MPa or more, and particularly preferably 800 MPa or more.
- Such a large value of compressive stress can be formed by adjusting the conditions such as chemical strengthening time, alkali molten salt composition, concentration, and temperature.
- the cover glass of the present invention contains Ce, it emits blue fluorescence when irradiated with strong ultraviolet light using an ultraviolet lamp or the like.
- an ultraviolet lamp or the like By utilizing this phenomenon, it is possible to easily discriminate between a glass base material or cover glass made of glass A that has the same appearance and is difficult to distinguish visually, and a glass base material or cover glass made of Ce-free glass. . That is, by irradiating with ultraviolet light and confirming the presence or absence of fluorescence, it is possible to confirm whether it is a glass base material made of glass A or a cover glass without analyzing the glass composition.
- the above inspection is preferably performed in a dark room state.
- a commercially available ultraviolet lamp may be used.
- the glass surface when the glass surface is observed in a dark room state by irradiating with strong ultraviolet light, the presence or absence of foreign matter on the glass surface can be easily inspected by the fluorescence emitted by Ce.
- cover glass with anti-scattering film One aspect of the cover glass of the present invention is a cover glass having a scattering prevention film on the surface. As the cover glass becomes thinner, it is not easy to recognize the end position of the cover glass. For example, when the anti-scattering film is bonded to the cover glass surface, the film is positioned and bonded to the glass edge. When performing such an operation, the alignment is facilitated by raising the outline of the cover glass by irradiating the glass with ultraviolet light to generate Ce fluorescence.
- the display of the present invention is a display that includes the cover glass of the present invention and is equipped with the cover glass of the present invention so as to cover the display screen.
- a preferred embodiment of the display of the present invention is a display excellent in portability or used outdoors, such as a portable information terminal, a mobile phone, and a car navigation system.
- the cover glass attached to the present invention is as thin as 1.0 mm or less, preferably 0.8 mm or less, more preferably 0.5 mm or less, and is excellent in mechanical strength. Suitable for the display used in the environment.
- the surface of the cover glass is easily damaged when handled by a portable information terminal or a mobile phone, and a touch panel type display presses or rubs the cover glass surface every time it is operated.
- a touch panel type display presses or rubs the cover glass surface every time it is operated.
- some types of cellular phones such as a foldable type and an openable type, an impact or an external force is applied each time the phone is folded or opened.
- a heavy impact is applied to the cover glass, and the cover glass surface is subject to friction. Even in such applications, the display of the present invention exhibits excellent durability.
- the chemically strengthened one further increases the bending strength and further improves the fracture resistance.
- FIG. 1 is a sectional view showing a part of a portable display equipped with the cover glass of the present invention.
- a cover glass 1 is disposed above the liquid crystal display panel 2 with a gap D.
- the liquid crystal display panel 2 is configured by a pair of glass substrates 21 and 22 sandwiching a liquid crystal layer 23.
- other members normally used for the liquid crystal display panel such as a backlight light source, are omitted.
- a white LED, a combination of a near-ultraviolet LED and a phosphor, an EL element, or the like can be used.
- the cover glass of the present invention contains Sn oxide that absorbs infrared light and Ce oxide that absorbs ultraviolet light, it has a function of cutting ultraviolet light and infrared light. Therefore, even if the display screen is exposed to sunlight or other light containing ultraviolet light or infrared light, the cover glass absorbs ultraviolet light and infrared light, reducing the internal wear of the display due to ultraviolet light and infrared light irradiation. Can do.
- An embodiment of the display according to the present invention which includes an image display unit and an image sensor as in a camera-equipped mobile phone, and the image display unit and the imaging lens are covered with a cover glass,
- the cover glass functions as an ultraviolet light and infrared light absorption filter, so that a sharp image can be photographed.
- the clarification effect can be remarkably enhanced by lowering (falling) the temperature of the molten glass and holding it in the range of 1200-1400 ° C. for 1 hour.
- the molten glass in which Sn and Ce coexist it was confirmed as described above that such a clarification effect is extremely remarkable.
- the glass compositions shown in Tables 1 and 2 are based on the composition expressed in mol% of the oxide (however, fining agents such as SnO 2 and CeO 2 are displayed in mass% by external addition).
- the surfaces of the obtained 288 types of glass were polished flat and smooth, and the inside of the glass was magnified and observed with an optical microscope (40 to 100 times) from the polished surface, and the number of residual bubbles was counted.
- the density of the residual bubbles was determined by dividing the number of residual bubbles counted by the mass of the glass corresponding to the region observed in an enlarged manner.
- Residual foam with 0-2 pcs / kg is rank A
- residual foam is 3-10 pcs / kg with rank B
- residual foam with 11-20 pcs / kg is rank C
- residual foam is 21- 40 D / kg for rank D, 41 to 60 l / kg for residual foam, rank E, l l for 61 to 100 l / kg, for rank F, 101 l / kg for residual bubbles Is rank G
- Table 2 shows the corresponding ranks with the basic composition 1 of each glass as a representative example. Even if the basic composition was different, almost the same results were obtained as long as the amounts of SnO 2 and CeO 2 added externally were the same.
- the residual bubbles in each glass were all 0.3 mm or less in size.
- a glass was prepared by the same method as described above except that the molten glass held at 1400-1600 ° C. for 15 hours was cooled and held at 1200-1400 ° C. for 1-2 hours and then molded.
- the density and size of residual bubbles, the presence or absence of crystals, and the presence or absence of unmelted raw materials were examined, the same results as above were obtained.
- TL / TH is preferably 0.5 or less in any of the above methods, and 0.2 or less. Is more preferable.
- TL / TH is preferably larger than 0.01, more preferably larger than 0.02, still more preferably larger than 0.03, and larger than 0.04. It is even more preferable.
- the temperature difference when the temperature is lowered from the range of 1400 to 1600 ° C to the range of 1200 to 1400 ° C is preferably set to 30 ° C or higher in order to enhance the effect of blowing bubbles of Sn and Ce, and is preferably set to 50 ° C or higher More preferably, it is more preferably 80 ° C. or higher, further preferably 100 ° C. or higher, and further preferably 150 ° C. or higher.
- the upper limit of the temperature difference is 400 ° C.
- the viscosity at 1400 ° C. of each glass having the basic composition 1 to 8 was measured by a viscosity measurement method using a JIS standard Z8803, a coaxial double cylindrical rotational viscometer. The measurement results are shown in Table 1. The viscosity of the glass at 1400 ° C. hardly changes even when SnO 2 and CeO 2 in the range shown in Table 2 are added.
- the amount of CeO 2 added is preferably 0.1% by mass or more, more preferably 0.2% by mass or more, and 0.3% by mass or more. Is more preferable.
- the amount of CeO 2 added is outside the above range, sufficient fluorescence intensity cannot be obtained, and the discrimination and inspection become difficult.
- each glass was molded into a sheet by the overflow down draw method or the float method. In either method, the glass was annealed after molding to remove strain, and a flat and uniform thickness (0.5 mm) sheet-like glass base material was obtained.
- surface roughness (arithmetic mean roughness Ra) of the glass base material formed by the downdraw method was examined with an atomic force microscope, it was as extremely smooth as 0.2 nm, and breakage such as microcracks There were no starting defects.
- the etched regions of the glass base material were etched from both main surface sides, and the cover glass was cut out. Thereafter, the hydrofluoric acid resistant resist remaining on the glass was swollen using a NaOH solution, and then peeled off and rinsed.
- the surface roughness (arithmetic average roughness Ra) of the main surface of the obtained cover glass was measured with an atomic force microscope, it was 0.2 nm, which was high, unchanged from the surface state immediately after being formed by the downdraw method. It had smoothness. Further, the surface roughness (arithmetic mean roughness Ra) of the end face of the cover glass was measured with an atomic force microscope, and found to be 1.2 to 1.3 nm over the entire outer shape. The reason why the surface roughness of the end face can be reduced in this way is due to processing by etching.
- a cover glass in which Sn and Ce were added to basic compositions 5 to 8 was immersed in a potassium nitrate (KNO 3 ) treatment bath, subjected to ion exchange treatment, and subjected to chemical strengthening. It confirmed that the compressive-stress layer was formed like the said glass on the cover glass surface.
- KNO 3 potassium nitrate
- the surface roughness of the main surface and the end surface of the cover glass after chemical strengthening was measured and found to be 0.3 nm and 1.4 to 1.5 nm, respectively. Further, no microcracks were observed on the end face.
- Cover glass mechanical strength evaluation test The cover glass is set on a support base that comes into contact with the outer peripheral edge 3 mm of the main surface of the cover glass, and the center of the cover glass starts from the opposite main surface side that comes into contact with the support base.
- a static pressure strength test was conducted by pressing the part with a pressure member.
- the pressurizing member was made of a stainless alloy having a tip of ⁇ 5 mm.
- thermosetting ink is used for printing, but the ink before drying can be easily removed, but it is difficult to remove the ink layer after a heating drying process called baking treatment. It becomes.
- the ink layers are to be applied in layers, a drying process is performed after forming one ink layer, then a second ink layer is formed, and the same operation is repeated to form a multi-layer ink layer. At that time, it is possible to easily check whether ink has adhered to unnecessary portions of the glass surface using fluorescence, or whether the adhered ink has been completely removed. Can be improved.
- the cover glass is irradiated with ultraviolet light emitted from an ultraviolet lamp, and the blue fluorescence emitted from the cover glass is observed.
- the illumination in the visible range is turned off, the outline of the cover glass becomes clear due to the contrast of the cover glass emitting blue fluorescence and the back.
- the scattering prevention film is aligned with the cover glass and attached to the surface. By such an operation, the scattering prevention film could be bonded relatively easily to an extremely thin cover glass having a thickness of 0.5 mm or less.
- the scattering prevention film is transparent and transmits an image displayed on the display.
- FIG. 1 schematically shows a partial cross section of a display panel of a portable information terminal.
- the cover glass 1 is attached to a liquid crystal display panel having two glass substrates arranged so as to sandwich the liquid crystal layer 3 and the liquid crystal panel so as to cover the entire panel surface with a space D.
- the cover glass cuts ultraviolet light and infrared light, and a sharp image could be taken.
- Each display has excellent strength and durability despite its small size. It was also confirmed that the display image on the display had no distortion and high image quality.
- a cover glass that is attached to a mobile terminal device such as a mobile phone or a PDA (Personal Digital Assistant) or other mobile device and protects the display screen.
- a mobile terminal device such as a mobile phone or a PDA (Personal Digital Assistant) or other mobile device and protects the display screen.
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Abstract
Description
(1)ディスプレイの画像表示部をカバーしつつ、前記画像表示部が表示する画像を透過するために用いるカバーガラスにおいて、
酸化物基準に換算し、モル%表示にて、
SiO2 60~75%、
Al2O3 0~12%
(ただし、SiO2およびAl2O3の合計含有量が68%以上)、
B2O3 0~10%、
Li2OおよびNa2Oを合計で5~26%、
K2O 0~8%
(ただし、Li2O、Na2OおよびK2Oの合計含有量が26%以下)、
MgO、CaO、SrO、BaOおよびZnOを合計で0~18%、
ZrO2、TiO2およびHfO2を合計で0~5%、
を含み、さらに、Sn酸化物およびCe酸化物を外割り合計含有量で0.1~3.5質量%含み、Sn酸化物とCe酸化物の合計含有量に対するSn酸化物の含有量の比(Sn酸化物の含有量/(Sn酸化物の含有量+Ce酸化物の含有量))が0.01~0.99であり、Sb酸化物の含有量が0~0.1%であるガラスにより構成され、板厚が1.0mm以下であることを特徴とするカバーガラス、
(2)前記カバーガラスは表面に圧縮応力層を有する上記(1)項に記載のカバーガラス。
(3)前記圧縮応力層は化学強化により形成されたものである上記(2)項に記載のカバーガラス、
(4)表面に飛散防止フィルムを備える上記(1)項~(3)項のいずれか1項に記載のカバーガラス、
(5)上記(1)項~(4)項のいずれか1項に記載のカバーガラスを備え、表示画面をカバーするように前記カバーガラスが装着されているディスプレイ、
を提供するものである。
SiO2 60~75%、
Al2O3 0~12%
(ただし、SiO2およびAl2O3の合計含有量が68%以上)、
B2O3 0~10%、
Li2OおよびNa2Oを合計で5~26%、
K2O 0~8%
(ただし、Li2O、Na2OおよびK2Oの合計含有量が26%以下)、
MgO、CaO、SrO、BaOおよびZnOを合計で0~18%、
ZrO2、TiO2およびHfO2を合計で0~5%、
を含み、さらに、Sn酸化物およびCe酸化物を外割り合計含有量で0.1~3.5質量%含み、Sn酸化物とCe酸化物の合計含有量に対するSn酸化物の含有量の比(Sn酸化物の含有量/(Sn酸化物の含有量+Ce酸化物の含有量))が0.01~0.99であり、Sb酸化物の含有量が0~0.1%であるガラスにより構成され、板厚が1.0mm以下であることを特徴とする。
以下、本発明のカバーガラスを構成するガラスをガラスAと呼ぶ。
まず、ガラスAが得られるように、酸化物、炭酸塩、硝酸塩、硫酸塩、水酸化物などと、SnO2、CeO2などの清澄剤を秤量、混合して、ガラス原料を調合し、前記ガラス原料を熔融し、得られた熔融ガラスを清澄、成形してガラスAを得る。
本発明のカバーガラスは、例えば、ガラス原料を加熱、熔融し、ダウンドロー法、フロート法などによりシート形状に成形し、ガラス母材を得た後、このガラス母材を加工して作製することができる。ここでガラスの熔融については、ガラスAの製法において説明したとおりである。
アニールによって歪を低減したシート状ガラスを、必要に応じてカバーガラスに加工しやすい大きさに切断する。このようにして得たガラス板をガラス母材と呼ぶ。
ガラスAは化学強化用ガラスとして好適である。ガラスAの化学強化は、例えば所望のカバーガラス形状に加工したガラスAをアルカリ熔融塩に浸漬することにより行う。熔融塩としては、硝酸ナトリウム熔融塩、硝酸カリウム熔融塩、または前記2種の熔融塩を混合したものを使用することができる。ガラスAは、ガラス成分として、Li2OまたはNa2Oの少なくとも一方を含む。ガラスAがLi2O成分を含む場合は、ナトリウム熔融塩、あるいはナトリウム熔融塩とカリウム熔融塩を使用して化学強化し、ガラスAがLi2Oを含まない場合、すなわち、Li2O、Na2OのうちNa2Oのみ含む場合は、カリウム熔融塩を使用して化学強化すればよい。
前述のように、本発明のカバーガラスは、Ceを含むため、紫外光ランプなどを用いて強い紫外光を照射すると青色の蛍光を発生する。この現象を利用し、同一の外観を呈し、目視では判別困難なガラスAからなるガラス母材あるいはカバーガラスと、Ce非添加ガラスからなるガラス母材あるいはカバーガラスとを容易に判別することができる。すなわち、紫外光を照射し、蛍光発生の有無を確認することで、ガラス組成を分析するまでもなく、ガラスAからなるガラス母材あるいはカバーガラスかどうかを確認することができる。蛍光発生の有無を容易に確認するため、上記検査は暗室状態で行うことが好ましい。紫外光ランプは市販品を使用すればよい。
本発明のカバーガラスの一態様は、表面に飛散防止フィルムを備えたカバーガラスである。カバーガラスの超薄板化に伴い、カバーガラスの端部位置の認識が容易でなくなってきている。例えば、カバーガラス表面に飛散防止フィルムの貼りあわせる際、ガラス端部に上記フィルムを位置合わせし、貼り合わせる。このような作業を行う際、ガラスに紫外光を照射してCeによる蛍光を発生させることにより、カバーガラスの輪郭を浮き立たせることにより上記位置合わせが容易になる。
本発明のディスプレイは、上記本発明のカバーガラスを備え、表示画面をカバーするように上記本発明のカバーガラスが装着されているディスプレイである。
表1に示す基本組成1~8の各組成に、表2のNo.1~No.36に示す各量のSnO2、CeO2を外割り添加した組成のガラスが得られるように酸化物、炭酸塩、硝酸塩、水酸化物などの原料とSnO2、CeO2などの清澄剤を秤量し、混合して288種のガラスを得るための調合原料とした。この原料を熔融容器に投入して1400~1600℃の範囲で6時間、加熱、熔融し、清澄、攪拌して泡、未熔解物を含まない均質な熔融ガラスを作製した。未熔解物を含まない均質な熔融ガラスを作製した。上記1400~1600℃の範囲に6時間保持した後、熔融ガラスの温度を低下(降温)させて1200~1400℃の範囲に1時間保持することにより、清澄効果を格段に高めることができる。特にSnおよびCeが共存する熔融ガラスにおいて、こうした清澄効果は極めて顕著であることを上記のように確認した。なお、表1、表2に示すガラス組成は、酸化物のモル%表示(ただし、SnO2、CeO2などの清澄剤は外割り添加による質量%表示)した組成が基準である。
次に、上記各ガラスをオーバーフローダウンドロー法またはフロート法によりシート状に成形した。いずれの方法においても、成形に引き続きガラスをアニールして歪を除き、平坦かつ均一な厚さ(0.5mm)のシート状のガラス母材を得た。なお、ダウンドロー法により成形したガラス母材の主表面の表面粗さ(算術平均粗さRa)を、原子間力顕微鏡により調べたところ0.2nmと極めて平滑であり、マイクロクラックなどの破壊の起点となる欠陥も認められなかった。
次にガラス母材の両主表面上にネガ型の耐フッ酸性レジストを厚さ30μmでコーティングし、この耐フッ酸性レジストに対して150℃で30分のベーキング処理を施した。次いで、カバーガラスの輪郭形状に相当するパターンを有するフォトマスクを介してレジストに対し両面から露光し、その後、レジストを現像液(Na2CO3溶液)を用いて現像してガラス母材上の被エッチング領域以外の領域にレジストが残存するようにレジストパターンを形成した。
次に上記カバーガラスのうち、基本組成1~4に表2のNo.1~36のいずれかの量のSn、Ceを添加した144種類のカバーガラスを385~405℃に保った硝酸カリウム(KNO3)60%と硝酸ナトリウム(NaNO3)40%の混合溶融塩の処理浴中に4時間浸漬して、イオン交換処理し、化学強化を施した。カバーガラス表面に形成された圧縮応力層の深さ(厚さ)は、バビネ法により測定した結果、概ね150μm前後であった。また、圧縮応力は350MPaであった。
カバーガラスの主表面における外周縁部3mmで当接する支持台にカバーガラスをセットし、支持台に当接した反対側の主表面側から、カバーガラスの中心部に対して加圧部材で押圧させて静圧強度試験を行った。加圧部材は、先端がφ5mmのステンレス合金からなるものを使用した。
上記の化学強化した各カバーガラス表面に印刷を行う前、ガラス表面に異物の付着がないか、暗室にてカバーガラス表面に紫外線ランプを用いて紫外線を照射し、蛍光によって照らし出されるガラス表面を観察した。このような検査により、表面が清浄であることを確認した後、カバーガラス表面にインク層を形成した印刷する。
上記の化学強化した各カバーガラス表面に飛散防止フィルムを貼り付ける前、ガラス表面に異物の付着がないか、暗室にてカバーガラスに紫外光ランプを用いて紫外光を照射し、蛍光によって照らし出されるガラス表面を観察した。このような検査により、表面が清浄であることを確認した後、カバーガラス表面に飛散防止フィルムを貼り付けた。
このようにして作製した各種カバーガラスを、携帯情報端末(PDA)の表示パネルをカバーするように装着し、携帯情報端末を作製した。図1に携帯情報端末の表示パネルの一部の断面を模式的に示す。カバーガラス1は、液晶層3とこの液晶パネルを挟むように配置された2枚のガラス基板を有する液晶表示パネルと間隔Dのスペースを隔ててパネル表面全体を覆うように装着する。なお、図1には示さない撮像レンズも覆うようにカバーガラスを設けてもよい。このような装置では、カバーガラスが紫外光および赤外光をカットしてシャープな画像を撮影することができた。
2 液晶表示パネル
21,22 ガラス基板
23 液晶層
Claims (5)
- ディスプレイの画像表示部をカバーしつつ、前記画像表示部が表示する画像を透過するために用いるカバーガラスにおいて、
酸化物基準に換算し、モル%表示にて、
SiO2 60~75%、
Al2O3 0~12%
(ただし、SiO2およびAl2O3の合計含有量が68%以上)、
B2O3 0~10%、
Li2OおよびNa2Oを合計で5~26%、
K2O 0~8%
(ただし、Li2O、Na2OおよびK2Oの合計含有量が26%以下)、
MgO、CaO、SrO、BaOおよびZnOを合計で0~18%、
ZrO2、TiO2およびHfO2を合計で0~5%、
を含み、さらに、Sn酸化物およびCe酸化物を外割り合計含有量で0.1~3.5質量%含み、Sn酸化物とCe酸化物の合計含有量に対するSn酸化物の含有量の比(Sn酸化物の含有量/(Sn酸化物の含有量+Ce酸化物の含有量))が0.01~0.99であり、Sb酸化物の含有量が0~0.1%であるガラスにより構成され、板厚が1.0mm以下であることを特徴とするカバーガラス。 - 前記カバーガラスは表面に圧縮応力層を有する請求項1に記載のカバーガラス。
- 前記圧縮応力層は化学強化により形成されたものである請求項2に記載のカバーガラス。
- 表面に飛散防止フィルムを備える請求項1~3のいずれか1項に記載のカバーガラス。
- 請求項1~4のいずれか1項に記載のカバーガラスを備え、表示画面をカバーするように前記カバーガラスが装着されているディスプレイ。
Priority Applications (2)
Application Number | Priority Date | Filing Date | Title |
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US13/636,275 US20130034670A1 (en) | 2010-03-24 | 2011-03-18 | Display cover glass and display |
CN201180015008XA CN102811963A (zh) | 2010-03-24 | 2011-03-18 | 显示器用防护玻璃及显示器 |
Applications Claiming Priority (2)
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JP2010-068655 | 2010-03-24 | ||
JP2010068655A JP2011201711A (ja) | 2010-03-24 | 2010-03-24 | ディスプレイ用カバーガラスおよびディスプレイ |
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WO2011118524A1 true WO2011118524A1 (ja) | 2011-09-29 |
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PCT/JP2011/056556 WO2011118524A1 (ja) | 2010-03-24 | 2011-03-18 | ディスプレイ用カバーガラスおよびディスプレイ |
Country Status (4)
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US (1) | US20130034670A1 (ja) |
JP (1) | JP2011201711A (ja) |
CN (1) | CN102811963A (ja) |
WO (1) | WO2011118524A1 (ja) |
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EP2920668B1 (en) * | 2012-11-14 | 2021-11-03 | GTAT Corporation | A mobile electronic device comprising an ultrathin sapphire cover plate |
WO2014093221A1 (en) * | 2012-12-10 | 2014-06-19 | Gt Crystal Systems, Llc | A mobile electronic device comprising a multilayer sapphire cover plate |
US9655293B2 (en) | 2012-12-10 | 2017-05-16 | Gtat Corporation | Mobile electronic device comprising a multilayer sapphire cover plate |
CN104556685A (zh) * | 2013-10-24 | 2015-04-29 | 中国南玻集团股份有限公司 | 铝硅酸盐玻璃及强化玻璃 |
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CN111132942A (zh) * | 2017-12-26 | 2020-05-08 | 日本电气硝子株式会社 | 盖玻璃 |
Also Published As
Publication number | Publication date |
---|---|
CN102811963A (zh) | 2012-12-05 |
US20130034670A1 (en) | 2013-02-07 |
JP2011201711A (ja) | 2011-10-13 |
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