Patent Application
20090105061
The present invention relates to glass compositions. The present invention also relates to glass spacers formed using the glass compositions, particularly glass spacers that are used suitably for electron beam-excited displays.
A self-luminous electron beam-excited display forms an image by irradiating phosphors with an electron beam emitted from an electron beam source and thereby allowing them to generate fluorescence. Recently, the self-luminous electron beam-excited display is used widely and practically as a flat display. As compared to a liquid crystal display, the electron beam-excited display is characterized by obtaining bright images and having a wide viewing angle.
Since the flat electron beam-excited display forms an image by irradiating phosphors with an electron beam, it is necessary to incorporate an electron beam source, phosphors, and other components into a vacuum container with an atmosphere having a pressure of approximately 10−3 Pa or lower. For instance, a vacuum container with an atmospheric pressure resistant structure described in JP 7 (1995)-230776 A has been proposed.
Glass spacers 5 are provided inside the vacuum container 10. In order to form the vacuum container 10 into an atmospheric pressure resistant structure, a required number of glass spacers 5 are disposed at required intervals. Glass spacers include a flat-plate glass spacer that is referred to as a rib and a pillar-shaped glass spacer that is referred to as a pillar. In
The following method has been proposed in JP 2000-203857 A as a method of producing a glass spacer with high precision. That is, a glass preform whose cross-sectional shape is substantially a similar figure to a desired cross-sectional shape of the glass spacer is prepared, and this glass preform is drawn while being heated so that the viscosity thereof reaches 105 dPa·sec to 109 dPa·sec (105 poise to 109 poise). This method also is referred to as a “redraw method”. This method makes it possible to improve the degree of similarity in cross-sectional shape between the glass preform and drawn glass and thereby to produce a glass spacer with a desired shape easily.
Furthermore, for example, a columnar glass spacer also can be produced with high precision by a method in which a glass material melted in a refractory container provided with a nozzle is withdrawn through the nozzle. This method also is referred to as a direct spinning method. The direct spinning method makes it possible to produce large amounts of glass spacers continuously at a time and is the method that allows columnar glass spacers to be produced with the highest precision.
As prior art relating to glass spacers, a glass spacer described in JP 2003-526187 A is mentioned. This document describes a glass spacer with a volume resistivity of 105 to 1013 Ω·cm. Furthermore, it recommends that the glass spacer contain 25 to 75 mol % of SiO2 and 1 to 30 mol % of transition element compound and further contain 5 to 10 mol % of alkali metal compound. Similarly in the examples described therein, spacers containing alkali metal compounds are used.
A glass spacer for an electron beam-excited display device serves to keep the space between both the front panel and the rear panel of a vacuum container constant. This glass spacer is exposed to electron-emitting elements. Therefore, when a large amount of alkali metal oxide is contained in glass that forms the glass spacer, there is a problem that bias voltage scatters alkali metal ions and thereby electric-field breakdown is caused. Furthermore, when a large amount of alkali metal oxide is contained, glass with a high Young's modulus cannot be obtained. Moreover, the heat resistance of the glass also is deteriorated.
JP 2002-104839 A describes, as a glass spacer that is free of alkali metal oxide, a glass spacer for an electron beam-excited display device that has a composition substantially free of alkali metal oxide and also free of oxide of transition metal that is present in a plurality of oxidation states.
JP 2004-43288 A describes glass having a composition in which the content of (TiO2+Nb2O5+SnO2+Ta2O5+WO3+CeO2) is at least 10 mol % and a field emission display device including a spacer formed of the glass. In the examples described in this document, the glass spacers contain at least 15 mol % of Nb2O5.
JP 2004-71158 A describes a glass spacer for an electron beam excitation display that has a composition containing 30 to 80 mol % of SiO2 and 10 to 40 mol % of oxide of transition metal.
JP 2005-263613 A describes a glass spacer in which the total content of SiO2 and TiO2 is 50 to 80 mol %, specifically, the content of SiO2 is 20 to 50 mol % and the content of TiO2 is 25 to 45 mol %, and a method of producing the same as well as a field emission display.
In these glass spacers, the electric-field breakdown is prevented and the quality thereof was satisfactory. However, the glass spacers are produced with tensile force applied thereto as described above and those glass spacers may be difficult to form during production thereof. Thus, there has been room for improvement in formability.
An object of the present invention is to provide a glass composition that has good formability and tends not to cause electric-field breakdown when formed into a spacer for an electron beam-excited display. Another object of the present invention is to provide a glass spacer composed of the glass composition and an electron beam-excited display including the same.
The present invention relates to a glass composition that contains the following components, in terms of mass %:
that is substantially free of alkali metal oxide.
The present invention also relates to a glass spacer composed of this glass composition.
Furthermore, the present invention relates to an electron beam-excited display including a vacuum container as well as electron-emitting elements and a glass spacer that are disposed inside the vacuum container, wherein the glass spacer is composed of the aforementioned glass composition.
The glass composition according to the present invention tends not to cause electric-field breakdown and has good formability. Therefore, a glass spacer formed from the glass composition is suitable for an electron beam-excited display. An electron beam-excited display provided with the glass spacer tends not to cause electric-field breakdown in the glass spacer.
Hereinafter, embodiments of the present invention are described.
First, a glass composition according to the present invention is described below in detail. The unit “%” indicated in this specification denotes “mass %” unless otherwise specified.
Silicon dioxide (SiO2) is an essential main component forming the skeleton of glass. It also is a component that adjusts the devitrification temperature and viscosity of glass and further is a component that improves among chemical durability, particularly acid resistance. When the SiO2 content is less than 20%, the devitrification temperature increases and thereby it becomes difficult to form the glass into the shape of a glass spacer. Furthermore, similarly in the case where the content is 40% or more, the devitrification temperature increases and thereby it becomes difficult to form the glass into the shape of a glass spacer.
Accordingly, the lower limit of SiO2 is at least 20%, preferably at least 23%, more preferably at least 25%, and most preferably at least 27%. On the other hand, the upper limit of SiO2 is lower than 40% and preferably 35% or lower.
Boron trioxide (B2O3) is a component forming the skeleton of glass. It also is a component that adjusts the devitrification temperature and viscosity of glass. Furthermore, it also is used as a glass melting aid. When the B2O3 content is 6% or less, B2O3 cannot provide the effect as a glass melting aid. On the other hand, when the B2O3 content exceeds 30%, the glass tends to undergo phase separation, and further the chemical durability of the glass also is deteriorated.
Accordingly, the lower limit of B2O3 is higher than 6%, preferably at least 8%, and more preferably at least 10%. The upper limit of B2O3 is 30% or lower, preferably 25% or lower, and more preferably 20% or lower.
Aluminum oxide (Al2O3) is a component forming the skeleton of glass. It also is a component that adjusts the devitrification temperature and viscosity of glass and further is a component that improves, among chemical durability, particularly water resistance. On the other hand, Al2O3 also is a component that deteriorates, among chemical durability, acid resistance. When the Al2O3 content exceeds 20%, the melting point of glass increases and thereby it becomes difficult to melt the raw material uniformly. Furthermore, since the devitrification temperature increases, it becomes difficult to form the glass into the shape of a glass spacer.
Accordingly, Al2O3 does not need to be contained but preferably it is contained. The lower limit thereof is preferably at least 3% and more preferably at least 5%. The upper limit of Al2O3 is 20% or lower, preferably 15% or lower, more preferably 12% or lower, and most preferably 10% or lower.
SiO2, B2O3 and Al2O3 are components forming the skeleton of glass and the total content (SiO2+Al2O3) thereof is important for the formability of the glass.
When the total content (SiO2+B2O3+Al2O3) is less than 45%, the devitrification temperature increases and thereby it becomes difficult to form the glass into a glass spacer. Furthermore, the chemical durability of the glass is deteriorated. On the other hand, when the total content exceeds 74%, the melting point of the glass increases and thereby it becomes difficult to melt the raw material uniformly. Moreover, the devitrification temperature increases and thereby it becomes difficult to form the glass into a glass spacer.
Accordingly, the lower limit of (SiO2+B2O3+Al2O3) is at least 45% and preferably at least 48%. The upper limit of (SiO2+B2O3+Al2O3) is 74% or lower, preferably 70% or lower, more preferably 65% or lower, and most preferably 60% or lower.
Alkaline earth oxides (MgO, CaO, SrO, and BaO) are components that adjust the devitrification temperature and viscosity of glass and also improve the thermal expansion coefficient and Young's modulus of glass. Particularly, strontium oxide (SrO) and barium oxide (BaO) are highly effective in decreasing the devitrification temperature of glass.
When the content of magnesium oxide (MgO) exceeds 15%, the devitrification temperature increases and thereby it becomes difficult to form the glass into the shape of a glass spacer.
Therefore, MgO does not need to be contained, and the upper limit of MgO is 15% or lower, preferably 10% or lower, and more preferably 5% or lower.
When the content of calcium oxide (CaO) is less than 5%, it cannot be sufficiently effective in adjusting the devitrification temperature and viscosity of glass. On the other hand, when the content of calcium oxide exceeds 40%, the devitrification temperature increases and thereby it becomes difficult to form the glass into the shape of a glass spacer.
Accordingly, the lower limit of CaO is at least 5% and preferably exceeds 10%. On the other hand, the upper limit of CaO is 40% or lower and preferably lower than 30%.
When the content of strontium oxide (SrO) exceeds 30%, the devitrification temperature increases and thereby it becomes difficult to form a glass spacer.
Accordingly, SrO does not need to be contained but preferably is contained. The lower limit thereof is preferably at least 5%. On the other hand, the upper limit of SrO is 30% or lower and preferably 20% or lower.
When the content of barium oxide (BaO) is at least 25%, the devitrification temperature increases and thereby it becomes difficult to form a glass spacer.
Therefore, BaO does not need to be contained, and the upper limit of BaO is lower than 25%, preferably 20% or lower, and more preferably 15% or lower.
SrO and BaO are components that adjust the devitrification temperature and viscosity of glass, and the total content (SrO+BaO) thereof is important for the formability of the glass.
When SrO and BaO are not contained, the devitrification temperature and viscosity cannot be adjusted sufficiently. On the other hand, when (SrO+BaO) exceeds 50%, the devitrification temperature increases and thereby it becomes difficult to form the glass into the shape of a glass spacer.
Accordingly, either SrO or BaO must be contained and it is preferable that the lower limit of (SrO+BaO) be at least 5%. On the other hand, the upper limit of (SrO+BaO) is 50% or lower, preferably 30% or lower, more preferably lower than 25%, and most preferably 20% or lower.
When the total content (MgO+CaO+SrO+BaO) of alkaline earth metal oxides (MgO, CaO, SrO, and BaO) is less than 20%, the devitrification temperature and viscosity cannot be adjusted sufficiently. On the other hand, when the total content (MgO+CaO+SrO+BaO) exceeds 60%, the devitrification temperature increases and thereby it becomes difficult to form the glass into the shape of a glass spacer.
Accordingly, the lower limit of (MgO+CaO+SrO+BaO) is at least 20% and preferably at least 25%. On the other hand, the upper limit of (MgO+CaO+SrO+BaO) is 60% or lower, preferably 50% or lower, more preferably 45% or lower, and most preferably 40% or lower.
Zinc oxide (ZnO) is a component that adjusts the devitrification temperature and viscosity of glass. When the ZnO content exceeds 10%, the devitrification temperature increases and thereby it becomes difficult to form the glass into the shape of a glass spacer.
Accordingly, ZnO does not need to be contained, and the upper limit of ZnO is 10% or lower and preferably 5% or lower.
Alkali metal oxide contained in glass may cause electric-field breakdown in an electron beam-excited display. Therefore the glass composition of the present invention is substantially free of alkali metal oxide.
Zirconium dioxide (ZrO2) improves the chemical durability of glass. Furthermore, it also improves the heat resistance properties of glass. However, when the ZrO2 content is 10% or more, the devitrification temperature of the glass increases and thereby it becomes difficult to form the glass into the shape of a glass spacer.
Accordingly, ZrO2 does not need to be contained, and the upper limit of ZrO2 is lower than 10% and preferably 5% or lower.
Lanthanum oxide (La2O3) is a component that adjusts the devitrification temperature and viscosity of glass and improves the Young's modulus of glass. When the La2O3 content exceeds 20%, the devitrification temperature increases and thereby it becomes difficult to form the glass into the shape of a glass spacer.
Accordingly, La2O3 does not need to be contained but preferably it is contained. The upper limit of La2O3 is 20% or lower, preferably 15% or lower, more preferably 12% or lower, and most preferably 10% or lower.
Yttrium oxide (Y2O3) is a component that adjusts the devitrification temperature and viscosity of glass and improves the Young's modulus of glass. When the Y2O3 content exceeds 10%, the devitrification temperature increases and thereby it becomes difficult to form the glass into the shape of a glass spacer.
Accordingly, Y2O3 does not need to be contained, and the upper limit of Y2O3 is 10% or lower and preferably 5% or lower.
Conventional glass spacers contain oxides of transitional metals, for example, Ti, V, Cr, Mn, Fe, Ni, Cu, and Nb, that are present in a plurality of oxidation states, so as to be provided with electron conductivity. However, when glass contains a large amount of, for example, oxides of these transition metals, the devitrification temperature of the glass increases and thereby it becomes difficult to form a glass spacer. In the present invention, therefore, the content of iron oxide is adjusted and the contents of oxides of transition metals other than Fe are limited.
Titanium oxide (TiO2) is a component that adjusts the electrical properties of glass and also adjusts the devitrification temperature and viscosity of glass. When the TiO2 content exceeds 3%, the devitrification temperature of glass increases and thereby it becomes difficult to form the glass into the shape of a glass spacer.
Accordingly, TiO2 does not need to be contained, and the upper limit of TiO2 is 3% or lower, preferably 2% or lower, and more preferably 1% or lower, and most preferably glass is substantially free of TiO2.
Generally, iron (Fe) contained in glass is a component that adjusts the electrical properties of glass and also adjusts the devitrification temperature and viscosity of glass. When the content of iron (Fe) in terms of Fe2O3 is less than 1%, the glass does not exhibit sufficiently high electron conductivity. On the other hand, when the content of iron (Fe) in terms of Fe2O3 exceeds 12%, the devitrification temperature of the glass increases and thereby it becomes difficult to form the glass into the shape of a glass spacer.
Accordingly, the lower limit of iron (Fe) is at least 1%, preferably at least 2%, and more preferably at least 3%, in terms of Fe2O3. On the other hand, the upper limit of Fe2O3 is 12% or lower, preferably lower than 10%, more preferably 9% or lower, and most preferably 8% or lower.
Niobium pentoxide (Nb2O5) is a component that adjusts the devitrification temperature and viscosity of glass and improves the Young's modulus of glass. Furthermore, it also is a component that adjusts the electrical properties of glass. When the Nb2O5 content exceeds 10%, the devitrification temperature increases and thereby it becomes difficult to form the glass into the shape of a glass spacer.
Accordingly, Nb2O5 does not need to be contained, and the upper limit of Nb2O5 is 10% or lower, preferably 8% or lower, more preferably 6% or lower, and most preferably 5% or lower.
Tantalum pentoxide (Ta2O5) is a component that adjusts the devitrification temperature and viscosity of glass and improves the Young's modulus of glass. Furthermore, it also is a component that adjusts the electrical properties of glass. When the Ta2O5 content exceeds 10%, the devitrification temperature increases and thereby it becomes difficult to form the glass into the shape of a glass spacer.
Accordingly, Ta2O5 does not need to be contained, and the upper limit of Ta2O5 is 10% or lower, preferably 8% or lower, more preferably 6% or lower, and most preferably 5% or lower.
TiO2, Fe2O3, Nb2O5, and Ta2O5 whose total content is described as (TiO2+Fe2O3+Nb2O5+Ta2O5) are components that adjust the electrical properties of glass and also adjust the devitrification temperature and viscosity of glass. When (TiO2+Fe2O3+Nb2O5+Ta2O5) is less than 1%, the glass does not exhibit sufficiently high electron conductivity. On the other hand, when (TiO2+Fe2O3+Nb2O5+Ta2O5) exceeds 12%, the devitrification temperature of the glass increases and thereby it becomes difficult to form the glass into the shape of a glass spacer.
Accordingly, the lower limit of (TiO2+Fe2O3+Nb2O5+Ta2O5) is at least 1%, preferably at least 2%, and more preferably at least 3%. On the other hand, the upper limit of (TiO2+Fe2O3+Nb2O5+Ta2O5) is 12% or lower, preferably lower than 10%, more preferably 9% or lower, and most preferably 8% or lower.
Furthermore, the raw material of vanadium pentoxide (V2O5) may need to be handled with care. Preferably, glass is substantially free of V2O5.
Furthermore, the raw material of manganese oxide (MnO) may need to be handled with care. Preferably, glass is substantially free of MnO.
Since fluorine (F) and phosphorus pentoxide (P2O5) tend to volatilize, they may evaporate while being melted. In the present invention, it is preferable that glass be substantially free of them.
Moreover, the raw material of lead oxide (PbO) may need to be handled with care. Preferably, glass is substantially free of PbO.
In the present invention, the expression “substantially free of a substance” denotes that the substance is not allowed to be contained intentionally except in the case where it is mixed unavoidably, for example, by contamination from industrial raw materials. Specifically, it denotes a content of less than 0.1%, preferably less than 0.05%, and more preferably less than 0.03%.
The glass composition of the present invention can be obtained by mixing known glass materials, melting the mixture by heating it, and then cooling it according to a common procedure. In this case, it is advantageous to carry out, for example, formation and pulverization suitably according to the intended use of the glass composition.
The glass composition of the present invention is useful particularly for glass spacers used for electron beam-excited displays. The glass composition of the present invention exhibits excellent formability in a method of manufacturing glass spacers, such as a direct spinning method. Furthermore, glass spacers for electron beam-excited displays that are formed of the glass composition of the present invention tend not to cause electric-field breakdown.
The glass spacer of the present invention is formed of the aforementioned glass composition. The respective properties of the glass spacer according to the present invention are described in detail below.
When a glass spacer is manufactured by the direct spinning method, the glass temperature is adjusted so that the molten glass has a viscosity of 100 dPa·sec to 1000 dPa·sec (100 poise to 1000 poise) during spinning. In this case, if the temperature at which the glass has a viscosity of 100 dPa·sec is lower than the devitrification temperature, devitrification (white turbidity caused by crystals generated and grown in the molten glass material) tends to occur during glass formation. The presence of generated crystals in the glass spacer is not preferable in terms of dimensional accuracy and characteristics of the glass spacer. Furthermore, it also adversely affects the formability. Therefore, it is preferable that the temperature difference obtained when the devitrification temperature of the aforementioned glass composition is subtracted from the temperature at which the aforementioned glass composition has a viscosity of 100 dPa·sec be at least 0° C. In this case, devitrification tends not to be caused during glass formation and more homogeneous glass spacers can be manufactured with high yield. The temperature difference is more preferably at least 10° C., further preferably at least 20° C., and most preferably at least 30° C. The temperature at which the glass has a viscosity of 100 dPa·sec can be determined by, for example, a platinum ball pulling method. The devitrification temperature can be determined as, for example, the highest temperature among the temperatures of an electric furnace with temperature gradient at positions where crystals appeared when glass is heated with the electric furnace.
Furthermore, as the glass transition point of the glass spacer increases, the heat resistance thereof becomes higher and therefore the glass spacer becomes more difficult to be deformed in the processing accompanied by high-temperature heating. When the glass transition point is at least 550° C., the shape is not changed by high-temperature heating in a step of producing a display glass. Accordingly, the glass transition point of the glass composition is preferably at least 550° C., more preferably at least 580° C., and further preferably at least 600° C. The highest temperature value among the glass transition points of the glass composition within the aforementioned glass composition range is the upper limit of the glass transition point. The glass transition point can be determined by, for example, thermomechanical analysis (TMA).
The glass spacer becomes more difficult to be separated from a display substrate with a decrease in the difference between the average linear expansion coefficient of the glass spacer and the thermal expansion coefficient of a display glass substrate. Generally, the average linear expansion coefficient of the display glass substrate at 50 to 350° C. is 80 to 90×10−7/° C. Accordingly, the lower limit of the average linear expansion coefficient of the glass spacer at 50 to 350° C. is preferably at least 70×10−7/° C., more preferably at least 75×10−7/° C., and further preferably at least 80×10−7/° C. Moreover, the upper limit of the average linear expansion coefficient of the glass spacer at 50 to 350° C. is preferably 100×10−7/° C. or lower, more preferably 95×10−7/° C. or lower, and further preferably 90×10−7/° C. or lower. The average linear expansion coefficient can be determined by, for example, the thermomechanical analysis (TMA).
The glass spacer can provide an electron beam-excited display with sufficiently high mechanical strength as the Young's modulus thereof increases. The Young's modulus of the glass composition is preferably at least 85 GPa, more preferably at least 90 GPa, further preferably at least 95 GPa, and most preferably at least 100 GPa. The highest value among the Young's moduli of glass compositions within the aforementioned glass composition range is the upper limit of the Young's modulus. The Young's modulus can be determined by, for example, the ultrasonic method.
Furthermore, in the glass spacer, excessively low volume resistivity results in excessive electron flow. On the other hand, when the volume resistivity is excessively high, the glass spacer tends to be electrically-charged. The lower limit of the volume resistivity of the glass spacer at 25° C. is preferably at least 1011 Ω·cm, more preferably at least 1012 Ω·cm, further preferably at least 1013 Ω·cm, and most preferably at least 1014 Ω·cm. On the other hand, the upper limit of the volume resistivity of the glass spacer at 25° C. is preferably 1016 Ω·cm or lower and more preferably 1015 Ω·cm or lower. The volume resistivity can be determined by, for example, the three terminal method according to JIS C 2141 (1992).
A glass spacer of the present invention can be manufactured using the aforementioned glass composition, by a known method such as the redraw method or the direct spinning method. Particularly, the direct spinning method is suitable from the viewpoints of formability of the aforementioned glass composition and dimensional accuracy of a resultant spacer. Specifically, a preform can be produced first by melting a glass material composed of the aforementioned glass composition in a refractory container provided with a nozzle and drawing the molten glass material directly through the nozzle. Thereafter, the preform is cut precisely into a predetermined length and thereby a glass spacer is obtained.
Since the aforementioned glass composition has excellent formability, this manufacturing method can achieve a higher yield than that of a conventional manufacturing method. Furthermore, the resultant glass spacer tends not to cause electric-field breakdown when used for an electron beam-excited display.
The glass spacer according to the present invention is particularly suitable for electron beam-excited displays. The shape thereof is not particularly limited and can be a columnar shape or a flat plate shape. The shape of the glass spacer according to the present invention is preferably a columnar shape (see the glass spacer 5 shown in
An electron beam-excited display of the present invention includes a vacuum container as well as electron-emitting elements and glass spacers that are disposed inside the vacuum container, with the glass spacers being formed of the aforementioned glass composition. Specifically, the electron beam-excited display of the present invention can be configured, with, for example, the glass spacers 5 of the electron beam-excited display having the configuration shown in
Hereinafter, the present invention is described in further detail using Examples 1 to 21 and Comparative Examples 1 to 18.
Common glass raw materials such as silica sand were mixed together in such a manner that the compositions indicated in Tables 1A, 2A, 3A, 4A, and 5A, respectively, were obtained, and thereby batches of the respective examples and comparative examples were prepared. Each of the batches was melted by heating it to 1200-1500° C. using an electric furnace and maintained in that condition for approximately four hours until the composition was homogenized. Thereafter, the molten glass was poured onto an iron plate and was cooled gradually in the electric furnace to normal temperature. Thus, a glass sample was obtained. All values of the glass compositions indicated in the tables are indicated in “mass %”.
On the other hand, the respective compositions of Examples 1 to 21 and Comparative Examples 1 to 18 are indicated in “mol %” in Tables 1B, 2B, 3B, 4B, and 5B. These examples were conceived based on the compositions indicated in mol %. In prior art documents, however, many glass compositions are indicated in mass % (wt %). Accordingly, with consideration given to ease of comparison therewith, the present specification is based on the indication in mass %. Compositions indicated in mol % would allow the intentions of these examples to be understood easily.
With respect to each glass thus produced, the average linear expansion coefficient and glass transition point thereof were determined from a thermal expansion curve. Furthermore, the velocities of longitudinal wave and transverse wave that propagate in the glass were determined by a sing-around method, while the Young's modulus was determined from the glass density measured by the Archimedes method. Furthermore, the relationship between the viscosity and temperature was examined by the common platinum ball pulling method, and from this result, the temperature at which the glass had a viscosity of 100 dPa·sec was determined. Thereafter, glass pulverized into a particle size of 1.0 mm to 2.8 mm was placed in a platinum boat and was heated for two hours in an electric furnace with temperature gradient (900° C. to 1400° C.), and thereby the devitrification temperature was determined from the highest temperature of the parts of the electric furnace corresponding to the positions where crystals appeared. The volume resistivity was determined by a three terminal method according to JIS C 2141 (1992).
These measurement results are indicated together in Tables 1A, 2B, 3A, 4A, and 5A.
The glass produced in Example 1 has a composition containing SiO2, B2O3, and Al2O3 as glass skeleton components, MgO, CaO, and SrO as alkaline earth metal oxides, and further ZnO, ZrO2, La2O3, and Fe2O3.
The glasses produced in Examples 2, 3, and 4 each have a composition obtained by adjusting the contents of SiO2, B2O3, and Al2O3 used in Example 1.
The glasses produced in Examples 5, 6, 7, 8, and 9 each have a composition obtained by adjusting the contents of SiO2, B2O3, and alkaline earth metal oxides of the glass according to Example 1.
The glass produced in Example 10 has a composition obtained by excluding ZnO from the glass of Example 1. Furthermore, the glass produced in Example 11 has a composition obtained by excluding ZrO2 from the glass of Example 1. Moreover, the glass produced in Example 12 has a composition obtained by excluding La2O3 from the glass of Example 1 and adjusting the contents of SiO2 and Fe2O3 of the glass of Example 1.
The glass produced in Example 13 has a composition containing Y2O3 added to the glass of Example 1. Furthermore, the glass produced in Example 14 has a composition containing TiO2 added to the glass of Example 1.
The glass produced in Example 15 has a composition obtained by, adjusting the contents of SiO2, B2O3, Al2O3, and Fe2O3 used in Example 1.
The glass produced in Example 16 has a composition containing Nb2O5 added to the glass of Example 1. Furthermore, the glass produced in Example 17 has a composition containing Ta2O5 added to the glass of Example 1.
The glasses produced in Examples 18, 19, and 20 each have a composition obtained by adjusting the content of Fe2O3 of the glass according to Example 1. The volume resistivities were 1.1×1014 Ω·cm to 1.3×1015 Ω·cm at 25° C. This indicates that an increase in the content of Fe2O3 results in a decrease in the volume resistivity.
The glass produced in Example 21 has a composition containing SiO2, B2O3, Al2O3 as glass skeleton components, CaO, SrO, and BaO as alkaline earth metal oxides, and further La2O3 and Fe2O3.
The glass produced in Comparative Example 1 has a composition obtained by excluding V2O5 from the glass composition described in Example 4 in JP 2003-526187 A, which is a glass composition outside the scope of the present invention. The temperature difference obtained by subtracting the devitrification temperature of the glass from the temperature at which the glass had a viscosity of 100 dPa·sec was −95° C., which was lower than those of the examples according to the present invention.
The glass produced in Comparative Example 2 has the glass composition described in Example D in JP 2004-43288 A, which is a glass composition outside the scope of the present invention. The Young's modulus was 87 GPa, which was smaller than those of the examples according to the present invention. The temperature difference obtained by subtracting the devitrification temperature of the glass from the temperature at which the glass had a viscosity of 100 dPa·sec was −77° C., which was lower than those of the examples according to the present invention.
The glass produced in Comparative Example 3 has the glass composition described in Example 5 in JP 2004-71158 A, which is a glass composition outside the scope of the present invention. The average linear expansion coefficient was 67×10−7/° C., which was smaller than those of the examples according to the present invention. Moreover, the temperature difference obtained by subtracting the devitrification temperature of the glass from the temperature at which the glass had a viscosity of 100 dPa·sec was −145° C., which was lower than those of the examples according to the present invention.
The glass produced in Comparative Example 4 has the glass composition described in Example 8 in JP 2005-263613 A, which is a glass composition outside the scope of the present invention. The temperature difference obtained by subtracting the devitrification temperature of the glass from the temperature at which the glass had a viscosity of 100 dPa·sec was −132° C., which was lower than those of the examples according to the present invention.
The glass produced in Comparative Example 5 is composed of a composition in which the B2O3 content is outside the range of the present invention. The temperature difference obtained by subtracting the devitrification temperature of the glass from the temperature at which the glass had a viscosity of 100 dPa·sec was −3° C., which was lower than those of the examples according to the present invention.
The glass produced in Comparative Example 6 is composed of a composition in which the Al2O3 content is outside the range of the present invention. The temperature difference obtained by subtracting the devitrification temperature of the glass from the temperature at which the glass had a viscosity of 100 dPa·sec was −85° C., which was lower than those of the examples according to the present invention.
The glass produced in Comparative Example 7 is composed of a composition in which the contents of MgO and CaO are outside the range of the present invention. The average linear expansion coefficient was 62×10−7/° C., which was smaller than those of the examples according to the present invention. Furthermore, the temperature difference obtained by subtracting the devitrification temperature of the glass from the temperature at which the glass had a viscosity of 100 dPa·sec was −128° C., which was lower than those of the examples according to the present invention.
The glass produced in Comparative Example 8 is composed of a composition in which the contents of (SiO2+B2O3+Al2O3), CaO, and SrO are outside the range of the present invention. The temperature difference obtained by subtracting the devitrification temperature of the glass from the temperature at which the glass had a viscosity of 100 dPa·sec was −12° C., which was lower than those of the examples according to the present invention.
The glass produced in Comparative Example 9 is composed of a composition in which the contents of (SiO2+B2O3+Al2O3) and BaO are outside the range of the present invention. The temperature difference obtained by subtracting the devitrification temperature of the glass from the temperature at which the glass had a viscosity of 100 dPa·sec was −123° C., which was lower than those of the examples according to the present invention.
The glass produced in Comparative Example 10 is composed of a composition in which the content of (SrO+BaO) is outside the range of the present invention. The temperature difference obtained by subtracting the devitrification temperature of the glass from the temperature at which the glass had a viscosity of 100 dPa·sec was −18° C., which was lower than those of the examples according to the present invention.
The glass produced in Comparative Example 11 is composed of a composition in which the contents of (MgO+CaO+SrO+BaO) and ZnO are outside the range of the present invention. The average linear expansion coefficient was 67×10−7/° C., which was smaller than those of the examples according to the present invention. Furthermore, the glass transition point was 612° C., which was lower than those of the examples according to the present invention. Moreover, the temperature difference obtained by subtracting the devitrification temperature of the glass from the temperature at which the glass had a viscosity of 100 dPa·sec was −23° C., which was lower than those of the examples according to the present invention.
The glass produced in Comparative Example 12 is composed of a composition in which the content of ZrO2 is outside the range of the present invention. The average linear expansion coefficient was 67×10−7/° C., which was smaller than those of the examples according to the present invention. Furthermore, the temperature difference obtained by subtracting the devitrification temperature of the glass from the temperature at which the glass had a viscosity of 100 dPa·sec was −203° C., which was lower than those of the examples according to the present invention.
The glass produced in Comparative Example 13 is composed of a composition in which the contents of (SiO2+B2O3+Al2O3) and La2O3 are outside the range of the present invention. The temperature difference obtained by subtracting the devitrification temperature of the glass from the temperature at which the glass had a viscosity of 100 dPa·sec was −78° C., which was lower than those of the examples according to the present invention.
The glass produced in Comparative Example 14 is composed of a composition in which the content of Y2O3 is outside the range of the present invention. The temperature difference obtained by subtracting the devitrification temperature of the glass from the temperature at which the glass had a viscosity of 100 dPa·sec was −55° C., which was lower than those of the examples according to the present invention.
The glass produced in Comparative Example 15 is composed of a composition in which the contents of (MgO+CaO+SrO+BaO), TiO2, and (TiO2+Fe2O3+Nb2O5+Ta2O5) are outside the range of the present invention. The average linear expansion coefficient was 69×10−7PC, which was smaller than those of the examples according to the present invention. Furthermore, the temperature difference obtained by subtracting the devitrification temperature of the glass from the temperature at which the glass had a viscosity of 100 dPa·sec was −65° C., which was lower than those of the examples according to the present invention.
The glass produced in Comparative Example 16 is composed of a composition in which the contents of (SiO2+B2O3+Al2O3), Fe2O3, and (TiO2+Fe2O3+Nb2O5+Ta2O5) are outside the range of the present invention. The temperature difference obtained by subtracting the devitrification temperature of the glass from the temperature at which the glass had a viscosity of 100 dPa·sec was −184° C., which was lower than those of the examples according to the present invention.
The glass produced in Comparative Example 17 is composed of a composition in which the contents of Nb2O5 and (TiO2+Fe2O3+Nb2O5+Ta2O5) are outside the range of the present invention. The temperature difference obtained by subtracting the devitrification temperature of the glass from the temperature at which the glass had a viscosity of 100 dPa·sec was −40° C., which was lower than those of the examples according to the present invention.
The glass produced in Comparative Example 18 is composed of a composition in which the contents of (SiO2+B2O3+Al2O3), Ta2O5, and (TiO2+Fe2O3+Nb2O5+Ta2O5) are outside the range of the present invention. The temperature difference obtained by subtracting the devitrification temperature of the glass from the temperature at which the glass had a viscosity of 100 dPa·sec was −130° C., which was lower than those of the examples according to the present invention.
As described above, in each glass produced in the aforementioned comparative examples, the temperature difference obtained by subtracting the devitrification temperature of the glass from the temperature at which the glass had a viscosity of 100 dPa·sec is small and a minus value. However, in each glass produced in the aforementioned examples, the temperature difference is at least 0° C. Accordingly, it is proved that the glasses produced in the examples have better formability than that of the glasses produced in the comparative examples.
The method of manufacturing a glass spacer is described with reference to
After each glass composition obtained in the aforementioned examples was melted by the method described above, it was formed into pellets while being cooled. These pellets were fed into a manufacturing apparatus 100 and thereby a glass spacer was manufactured. The manufacturing apparatus used herein was the manufacturing apparatus 100 shown in
In the manufacturing apparatus 100 shown in
| Number | Date | Country | Kind |
|---|---|---|---|
| 2006-128188 | May 2006 | JP | national |
| Filing Document | Filing Date | Country | Kind | 371c Date |
|---|---|---|---|---|
| PCT/JP2007/059264 | 4/27/2007 | WO | 00 | 10/28/2008 |
