JP2007277076A - Method of melting glass, and glass - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a method of melting glass which can repeatedly melt an SnO-P<SB>2</SB>O<SB>5</SB>-based glass or the like easily corroding a platinum-made melting container, over a long period of time, and does not deteriorate the quality of a glass by eluted components even in the case where the constituents of the melting container are eluted into a molten glass in melting, and a glass made by the method. <P>SOLUTION: In the method of melting glass for melting a blended glass raw material in the melting container, the melting container is characterised by being made of zirconium or a zirconium alloy. <P>COPYRIGHT: (C)2008,JPO&INPIT

Description

  The present invention relates to a glass melting method and glass, and in particular, various ceramic packages, sealing of electronic parts such as magnetic heads, sealing of various display devices, partition walls of plasma display panels (PDP), and metal double containers of thermos. The present invention relates to a glass melting method and glass suitable for sealing and various optical glasses.

  Sealing materials used in electronic parts and display devices such as ceramic packages and magnetic heads can be sealed at low temperatures so as not to adversely affect elements such as ICs and crystal units, and the thermal expansion coefficient is sealed. It is required to be consistent with that of the kimono.

Up to now, various kinds of PbO—B ₂ O ₃ glass or composite materials obtained by adding a refractory filler to these glasses have been proposed as sealing materials that satisfy these characteristics (for example, Patent Document 1). reference).

However, recently, from an environmental point of view, it is required to remove lead, which is an environmentally hazardous substance, from glass, and SnO—P ₂ O ₅ glass has been proposed as an alternative material for PbO—B ₂ O ₃ glass. (For example, see Patent Documents 2 and 3).

By the way, PbO—B ₂ O ₃ glass is usually produced by melting a glass raw material in a platinum melting vessel excellent in heat resistance and corrosion resistance. Generally, PbO—B ₂ O ₃ glass has a low melting temperature, so that the amount of erosion of the platinum melting container after melting is small, and problems such as breakage of the melting container do not occur.

On the other hand, SnO—P ₂ O ₅ glass tends to erode the platinum melting container during melting, and cracks may occur in the platinum melting container, so that there is a problem that the platinum melting container cannot be used for a long period of time. is there. Further, platinum is a very expensive metal, and if the platinum melting container is replaced in a short period of time, the melting cost will increase.

Under such circumstances, as described in Patent Documents 4 to 6, an expensive silica (quartz) melting vessel is used for melting SnO—P ₂ O ₅ glass.
JP-A-2-229738 JP 11-292564 A JP 2001-48579 A Japanese Patent No. 2628007 Japanese Patent Publication No. 7-25567 Japanese Patent Laid-Open No. 9-235136

  Since the silica-made melting containers described in Patent Documents 4 to 6 have a small coefficient of thermal expansion, it is difficult to match the coefficient of thermal expansion with the glass remaining in the silica-made melting container after pouring out the molten glass. . If the thermal expansion coefficients of the two are mismatched, the silica melting container is easily cracked due to the difference in thermal expansion coefficient, and the melting container cannot be used for a long period of time.

  It is also conceivable to use a heat-resistant Inconel-based metal melting vessel as the melting vessel. However, since Inconel metal contains Cr in the metal, there is a problem that a large amount of Cr is melted in the glass when it is melted to color the glass, and the melted Cr makes the glass unstable.

Therefore, the technical problem of the present invention is that it is possible to repeatedly melt SnO—P ₂ O ₅ glass or the like that easily corrodes a platinum melting vessel over a long period of time, and the components of the melting vessel are eluted into the molten glass during melting. Even if it is a case, it is providing the melting method of glass and glass which an elution component does not denature glass.

As a result of repeating various experiments in order to solve the above technical problem, the present inventors have used a highly corrosive SnO—P ₂ O ₅ system when a melting vessel made of zirconium or a zirconium alloy is used as the melting vessel. Even when glass or the like is melted, the melting container is not easily eroded, the melting container is not easily damaged, and even if the constituent components of the melting container are eluted in the glass at the time of melting, the elution component does not alter the glass. It is discovered and proposed as the present invention. That is, the glass melting method of the present invention is a glass melting method in which a prepared glass raw material is melted in a melting vessel, wherein the melting vessel is made of zirconium or a zirconium alloy.

Second, the glass melting method of the present invention is characterized by melting in an inert atmosphere or a reducing atmosphere. Here, “inert atmosphere” refers to a vacuum environment (100 Torr or less), a rare gas atmosphere such as N ₂ , Ar, and He, and “reducing atmosphere” refers to an oxygen concentration of 10% by volume or less at normal pressure. In this case, it refers to an atmosphere in which a reducing gas such as hydrogen or hydrocarbon is injected.

  Third, the glass melting method of the present invention is characterized in that the glass contains 20 to 70 mol% of SnO as a glass composition.

Fourth, the glass melting method of the present invention is that the glass contains, as a glass composition, mol%, SnO 20 to 70%, P ₂ O ₅ 10 to 50%, B ₂ O ₃ 0 to 30%. Characterized by

  Fifth, the glass melting method of the present invention is characterized in that zirconium has a purity of 97% by mass or more and contains one or more selected from the group of Hf, Fe and Cr as impurities. It is done.

  Sixth, the method for melting glass of the present invention is characterized in that the zirconium alloy is a zircaloy alloy containing zirconium and one or more selected from the group consisting of Sn, Fe, Cr and Ni. It is done.

  Seventh, the glass melting method of the present invention is characterized in that the zirconium alloy is any one of a zirconium iron alloy, a zirconium copper alloy, and a zirconium aluminum alloy.

  Eighth, the glass of the present invention is characterized by being produced by the glass melting method described above.

Ninth, the glass of the present invention is characterized by containing 100 to 3000 ppm of ZrO ₂ in terms of mass as a glass composition.

Tenth, the glass of the present invention contains, as a glass composition, 20 to 70% SnO, 10 to 50% P ₂ O ₅ and 0 to 30% B ₂ O ₃ in mol%, and ZrO ₂ in terms of mass. It is characterized by containing 100 to 3000 ppm.

  Eleventh, the glass of the present invention is characterized for use in sealing electronic components or display devices.

According to the glass melting method of the present invention, SnO—P ₂ O ₅ glass or the like that easily corrodes the melting container can be melted repeatedly over a long period of time. Is difficult to alter.

Since the glass melting method of the present invention uses zirconium or a zirconium alloy as the melting container, the heat resistance and corrosion resistance of the melting container can be ensured. A melting vessel made of zirconium or a zirconium alloy does not deform at the melting temperature of the glass (for example, 700 to 1000 ° C.), and the melting vessel corrodes even if highly corrosive SnO—P ₂ O ₅ glass or the like is melted. It has the advantage that it is difficult to do.

  In addition, a melting vessel made of zirconium or a zirconium alloy has characteristics that it is difficult to devitrify the glass in addition to difficult to separate the glass even if zirconium or the like is eluted into the glass at the time of melting. Moreover, if zirconium or the like is positively eluted into the glass at the time of melting, the following effects can also be enjoyed.

  Further, since zirconium and zirconium alloys have excellent malleability and workability, various shapes of melting containers can be produced. Zirconium and zirconium alloys are cheaper than platinum, and as a result, the melting cost can be reduced.

  In the glass melting method of the present invention, it is preferable to melt in an inert atmosphere or a reducing atmosphere. If zirconium or a zirconium alloy is left in the atmosphere in the melting temperature range (for example, 700 to 1000 ° C.), the surface of the zirconium or the zirconium alloy is oxidized and its toughness is easily impaired. In particular, when the melting temperature is 900 ° C. or higher, this tendency becomes remarkable. As a result, the melting container is liable to undergo stress failure when subjected to thermal shock or when the melting container is cooled. If melted in an inert atmosphere or a reducing atmosphere, zirconium and zirconium alloys are not easily oxidized, so that the melting vessel is not easily damaged, and the above situation can be effectively avoided.

  The glass melting method of the present invention does not exclude the aspect of melting in the air, but if it is melted in an inert atmosphere or a reducing atmosphere, in addition to the above advantages, the life of the melting container is increased. Since it can be increased, the melting cost can be reduced.

In the case of SnO-containing glass, particularly SnO—P ₂ O ₅ -based glass, melting in an inert atmosphere or a reducing atmosphere can also enjoy the advantage of preventing oxidation of SnO, which is more preferable. Note that in the SnO-P ₂ O ₅ based glass, the SnO in the glass composition is oxidized, the flowability of the glass is impaired upon firing. Here, if the SnO content is less than 20%, the merit of using a melting vessel made of zirconium or a zirconium alloy becomes poor. Conversely, if the SnO content is more than 70%, the glass is devitrified during melting. Glass production efficiency is impaired. Therefore, the content of SnO is mol%, preferably 20 to 70%, more preferably 20 to 65%, and still more preferably 30 to 60%.

  In the method for melting glass according to the present invention, zirconium has a purity of 97% by mass or more, preferably 99% by mass or more, and for example, one or more selected from the group consisting of Hf, Fe and Cr as impurities. Can be contained. It is preferable that Hf, Fe, and Cr are expressed by mass% and Hf is 3% or less and Fe + Cr is 0.2% or less. If the purity of zirconium is less than 97% by mass, the impurity component may be dissolved during melting and the glass may be altered, which is not preferable.

  In the glass melting method of the present invention, the zirconium alloy is Zircaloy (equivalent to ASTM R60802 or ASTM R60804) or zirconium iron to which one or more selected from the group of Sn, Fe, Cr and Ni are added. Alloys, zirconium copper alloys, and zirconium aluminum alloys are preferred. These zirconium alloys are excellent in corrosion resistance, heat resistance, workability and the like, and can be suitably used as a melting vessel.

  Zircaloy has Sn, Fe, Cr, and Ni added in amounts of Sn 1.0 to 2.0%, Fe 0.05 to 0.3%, Cr 0.05 to 0.2%, Ni It is preferable that it is 0.02 to 0.1%. If these components are added, excessive corrosion resistance can be prevented.

  In the glass melting method of the present invention, the thickness of the melting container is preferably 1 to 5 mm, more preferably 2 to 3 mm. If it does in this way, the crack of a melting container can be prevented, without impairing the workability of a melting container.

  In the glass melting method of the present invention, in the case of a vacuum atmosphere, the melting temperature is preferably 800 to 1400 ° C. In the case of an inert atmosphere, the melting temperature is preferably 800 to 1100 ° C. Moreover, if the melting temperature is set to 800 to 1000 ° C., the glass can be appropriately melted. When the melting temperature is high, the valence of Sn is likely to change from divalent to tetravalent, that is, SnO is easily oxidized, and when the melting temperature is low, undissolved components of the glass raw material are likely to remain after melting.

In the glass melting method of the present invention, zirconium is eluted from zirconium or a zirconium alloy so that the ZrO ₂ content in the glass composition is 100 to 3000 ppm (preferably 200 to 2000 ppm, more preferably 300 to 1000 ppm) in terms of mass. Is desirable. In this way, the weather resistance and moisture resistance of the glass can be improved without adversely affecting the glass properties such as devitrification resistance. In particular, in the case of SnO—P ₂ O ₅ -based glass, if zirconium is eluted from zirconium or a zirconium alloy, this eluted component acts as a reducing agent, thereby suppressing the situation where SnO in the glass composition is oxidized. it can. When the content of ZrO ₂ is less than 100 ppm, it becomes difficult to improve the weather resistance and moisture resistance of the glass. When the content of ZrO ₂ is more than 3000 ppm, the softening point of the glass rises and it becomes difficult to seal at a low temperature.

  In addition, the equipment in direct contact with the molten glass, such as a stirring blade and a gas pipe, is usually manufactured using platinum. Therefore, if these facilities are also made using zirconium or a zirconium alloy, the advantages of the melting container described above can be enjoyed.

Since the glass produced by the glass melting method of the present invention has a low melting point property, it is preferably SnO—P ₂ O ₅ glass. Further, SnO-P ₂ O ₅ based glass, a glass composition, in _{mol%, SnO 20~70%, P 2} O 5 10~50%, preferably has ₂ O _{3 0~30%} B.

The reason why the glass composition of the SnO—P ₂ O ₅ glass is limited as described above will be described below.

  SnO is a component that lowers the melting point of glass. If the SnO content is less than 30%, the viscosity of the glass becomes high, the firing temperature becomes too high, and it becomes impossible to seal at a low temperature. When the content of SnO exceeds 70%, vitrification becomes difficult. In particular, if there is a large amount of SnO, the glass tends to be devitrified during firing. Therefore, if devitrification of the glass is not allowed during firing, the SnO content is preferably 60% or less. Further, if the SnO content is 40% or more, the fluidity of the glass can be improved, and the airtight reliability of electronic parts and the like can be secured, which is more preferable.

P ₂ O ₅ is a glass-forming oxide and a component that stabilizes the glass, and its content is 10 to 50%, preferably 15 to 45%, more preferably 20 to 35%. When the content of P ₂ O ₅ is less than 10%, the stability of the glass becomes insufficient. When the content of P ₂ O ₅ is more than 50%, the moisture resistance of the glass deteriorates.

Although B ₂ O ₃ is not an essential component, it is a glass-forming component and can be stabilized by containing it in the glass composition. The content of B ₂ O ₃ is 0 to 30%, preferably 2 to 15%. When the content of B ₂ O ₃ is more than 30%, the viscosity of the glass increases and it becomes difficult to seal at a low temperature.

In addition to the above components, the SnO—P ₂ O ₅ glass according to the present invention has ZnO 0-20%, MgO 0-20%, Al ₂ O ₃ 0-10%, SiO ₂ 0 in addition to the above components. -15%, La ₂ O ₃ 0-10%, R ₂ O (R ₂ O is the total amount of Li ₂ O, Na ₂ O, K ₂ O and / or Cs ₂ O) 0-20% it can. The reason why these components are limited to the above range will be described below.

  Although ZnO is not an essential component, it is a network-modifying oxide, and since it has a large effect of stabilizing the glass, it is desirable to contain 4% or more. However, if the ZnO content exceeds 20%, devitrification tends to occur on the glass surface during firing. In addition, when the sealing process is a long time (for example, 1 hour or more), specifically, in the PDP sealing process or the like, devitrification is likely to occur on the glass surface, so it is necessary to stabilize the glass. . In such a case, the ZnO content may be 5 to 15%.

  MgO is a network-modifying oxide and has the effect of stabilizing the glass. If MgO exceeds 20%, devitrification tends to occur on the glass surface during firing. The content of MgO is preferably 0 to 5%.

Al ₂ O ₃ is an intermediate oxide. Al ₂ O ₃ is not an essential component, but it is desirable to contain Al ₂ O _{3 because} it has the effect of stabilizing the glass and the effect of reducing the thermal expansion coefficient. However, if it exceeds 10%, the softening temperature rises and the fluidity of the glass during firing is inhibited. In addition, when considering the stability, thermal expansion coefficient, fluidity, and the like of glass, the content of Al ₂ O ₃ is more preferably 1 to 5%.

SiO ₂ is a glass forming oxide. Although SiO ₂ is not an essential component, it is desirable to contain it because it has an effect of suppressing devitrification. In addition, when it exceeds 15%, the softening temperature rises and the fluidity at the time of firing becomes extremely poor. In consideration of fluidity as a low melting point material, the content of SiO ₂ is preferably 0 to 10%.

R ₂ O is not an essential component, but by containing at least one of the R ₂ O components in the glass composition in an amount of 0.1% or more, the sealing strength with the object to be sealed can be increased. However, if the content of R ₂ O exceeds 20%, the glass tends to devitrify during firing. Incidentally, if the fluidity of the devitrification resistance and the glass during firing is required, it is preferable that the content of R ₂ O to 10% or less.

Furthermore, the SnO—P ₂ O ₅ glass according to the present invention can contain various components as a glass composition in addition to the above components. For example, for the purpose of stabilizing the glass, WO ₃ , MoO ₃ , Nb ₂ O ₅ , TiO ₂ , CuO, MnO, R′O (R′O is the total amount of MgO, CaO, SrO and / or BaO), etc. In a total amount of 0 to 35%, preferably 0 to 25%. In addition, when the total amount of these components exceeds 35%, the balance of the glass composition is lost, and conversely, the glass becomes unstable, and is easily devitrified when the glass is formed. In addition, In ₂ O ₃ or the like can be contained in order to improve the weather resistance and moisture resistance of the glass.

  The content of the stabilizing component and the reason for limitation will be described below.

The contents of WO ₃ and MoO ₃ are each preferably 0 to 20%, particularly preferably 0 to 10%. If these components exceed 20%, the viscosity of the glass tends to increase, and sealing at low temperatures becomes impossible.

The contents of Nb ₂ O ₅ and TiO ₂ are each preferably 0 to 15%, particularly preferably 0 to 10%. When these components exceed 15%, the devitrification tendency of the glass tends to increase.

  The contents of CuO and MnO are each preferably 0 to 10%, particularly preferably 0 to 5%. If these components exceed 10%, the glass tends to be unstable.

  The total content of R′O is preferably 0 to 15%, particularly preferably 0 to 5%. If R'O exceeds 15%, the glass tends to be unstable.

In ₂ O ₃ can be used for the purpose of obtaining high weather resistance and moisture resistance. The content of In ₂ O ₃ is preferably 0 to 5%. When the content of In ₂ O ₃ is more than 5%, since the In ₂ O ₃ is an expensive raw material, leading to rising raw material cost of the glass.

  In addition, it is preferable not to contain PbO substantially in a glass composition from an environmental viewpoint. Here, “substantially no PbO” refers to a case where the content of PbO in the glass composition is 1000 ppm or less.

The glass of the present invention, as a glass composition, in _{mol%, SnO 20~70%, P 2} O 5 10~50%, B 2 O 3 containing 0-30%. Further, in the glass of the present invention, is preferably contained 100~3000ppm the ZrO ₂ in the glass composition in terms of the weight, more preferably be contained 200～2000Ppm, it is particularly preferred to incorporate 300～1000Ppm. If it does in this way, the weather resistance and moisture resistance of glass can be improved. When the content of ZrO ₂ is less than 100 ppm, it becomes difficult to improve the weather resistance and moisture resistance of the glass. When the content of ZrO ₂ is more than 3000 ppm, it becomes difficult to seal at a low temperature. As described above, ZrO ₂ can be introduced into the glass composition by melting using a zirconium melting vessel or the like.

The glass of the present invention can be suitably produced by the above glass melting method. The SnO—P ₂ O ₅ glass obtained by the glass melting method or the SnO—P ₂ O ₅ glass having the glass composition has a glass transition point of 270 to 380 ° C., and is about 400 to 600 ° C. It is a low melting point glass showing good fluidity in the temperature range. Further, these SnO—P ₂ O ₅ glasses have a thermal expansion coefficient of about 90 to 150 × 10 ⁻⁷ / ° C. in a temperature range of 30 to 250 ° C.

SnO—P ₂ O ₅ -based glass having such characteristics can be used as a sealing material by itself as glass powder when the thermal expansion coefficient matches that of the object to be sealed.

On the other hand, when the thermal expansion coefficient does not match the material to be sealed, for example, alumina (70 × 10 ⁻⁷ / ° C.), high strain point glass (85 × 10 ⁻⁷ / ° C.), soda plate glass (90 × 10 ⁻⁷ / ° C.) ) And the like, a fireproof filler powder may be added to the SnO—P ₂ O ₅ glass powder to form a composite material. It is important that the thermal expansion coefficient of the composite material is designed to be about 5 to 30 × 10 ⁻⁷ / ° C. lower than the material to be sealed. If it does in this way, the stress concerning a sealing layer can be made into a compression (compression) side, and destruction of a sealing layer can be prevented. In this case, what is necessary is just to prepare so that it may become 45-95 volume% of glass powder, and 5-55 volume% of refractory filler powder.

In particular, when sealing a fluorescent display tube (VFD), a field emission display (FED), a PDP, and a cathode ray tube (CRT), the thermal expansion coefficient of the sealing material is about 60 to 100 × 10 ⁻⁷ / ° C. It is preferable to adjust to.

  As refractory filler, various refractory filler powders such as willemite ceramic, β-eucryptite, lead titanate ceramic, cordierite, tin oxide solid solution, zircon ceramic, mullite, quartz glass, and alumina are added. Also good. In addition to adjusting the thermal expansion coefficient, for example, a refractory filler powder can be added to improve mechanical strength. In addition, from an environmental viewpoint, it is preferable that a refractory filler powder does not contain PbO substantially.

  Hereinafter, the present invention will be described in detail based on examples.

  Tables 1 and 2 show examples (Nos. 1 to 9) of the present invention, and Table 3 shows comparative examples (Nos. 10 to 12).

  Various oxides, carbonate raw materials and the like were prepared so that the glass composition in the table was obtained, and glass raw materials were produced. This glass raw material was put into a melting container shown in the table, and melted at the melting temperature in the table for 2 hours in the melting atmosphere in the table.

  Subsequently, the molten glass in the melting container was poured out between a pair of rotating rollers, and a film-like glass sample was prepared while rapidly cooling the molten glass with the rotating rollers. The formed film-like glass was pulverized with a ball mill and then passed through a sieve having an aperture of 105 μm to obtain a glass powder having an average particle size of about 10 μm. Moreover, the molten glass in the melting container was poured out into a carbon mold, and a plate-shaped glass sample was produced.

  The glass transition point was determined by differential thermal analysis (DTA), and the thermal expansion coefficient was determined by a push rod thermal expansion measurement (TMA) apparatus.

  The flow diameter was evaluated by the following flow button test. First, the molded film-like glass was pulverized with a ball mill, and then passed through a sieve having an aperture of 105 μm to obtain a glass powder having an average particle size of about 10 μm. Next, a powder having a mass corresponding to the true specific gravity of the obtained glass powder was weighed and pressed into a button shape having a diameter of 20 mm using a mold to obtain a button-shaped powder compact. Subsequently, this powder compact was placed on the window glass and then fired in the atmosphere shown in the table. As firing conditions, the temperature was raised to 450 ° C., which is a firing temperature, at a rate of 10 ° C./minute, held at 450 ° C. for 10 minutes, and then cooled to room temperature at 10 ° C./minute. Finally, the diameter of the button after firing was measured with a digital caliper. The diameter of the button is desirably 20 mm or more when used as a sealing material.

  The “cracking of the melting container” was evaluated by visually judging whether or not a crack occurred in the melting container by leaving the melting container at room temperature after pouring the molten glass from the melting container. The case where there was no crack was “◯”, and the case where there was a crack was “x”.

“Content of ZrO ₂ in glass” was measured by fluorescent X-ray analysis. In addition, the numerical value in a table | surface is a numerical value of mass conversion.

As is clear from Tables 1 and 2, Example No. In Nos. 1 to 9, there was no cracking of the melting container, the flow diameter in the flow button test was 20 mm or more, and the obtained glass properties were also good. The ZrO ₂ content was also 700 to 1900 ppm.

  On the other hand, as is clear from Table 3, Comparative Example No. Nos. 10 and 12 cause cracks in the melting containers. In No. 11, since the molten glass was strongly colored green and the powdered glass was also devitrified, the flow diameter was 18 mm, and the glass properties were impaired.

  As described above, the glass melting method and glass according to the present invention include various ceramic packages, sealing of electronic parts such as magnetic heads, sealing of various display devices, PDP partition walls, and sealing of metal double containers of thermos bottles. And suitable for various optical glasses.

Claims (11)

In the glass melting method of melting the prepared glass raw material in a melting container,
A method for melting glass, wherein the melting container is made of zirconium or a zirconium alloy.   The method for melting glass according to claim 1, wherein the glass is melted in an inert atmosphere or a reducing atmosphere.   The glass melting method according to claim 1 or 2, wherein the glass contains 20 to 70% of SnO as a glass composition. The glass contains, as a glass composition, in mol%, SnO 20 to 70%, P ₂ O ₅ 10 to 50%, B ₂ O ₃ 0 to 30%. The method for melting glass as described.   The glass according to any one of claims 1 to 4, wherein the purity of zirconium is 97% by mass or more, and contains one or more selected from the group of Hf, Fe and Cr as impurities. Melting method.   The glass according to any one of claims 1 to 4, wherein the zirconium alloy is zirconium and a zircaloy alloy containing one or more selected from the group consisting of Sn, Fe, Cr and Ni. Melting method.   The method for melting glass according to any one of claims 1 to 4, wherein the zirconium alloy is any one of a zirconium iron alloy, a zirconium copper alloy, and a zirconium aluminum alloy.   A glass produced by the glass melting method according to claim 1. The glass according to claim 8, wherein the glass contains 100 to 3000 ppm of ZrO ₂ in terms of mass as a glass composition. As a glass composition, in mol% SnO 20 to 70% and wherein the _{P 2 O 5 10~50%, B} 2 O 3 containing 0-30%, and to 100~3000ppm containing ZrO ₂ in terms of the weight Glass to do.   The glass according to any one of claims 8 to 10, which is used for sealing an electronic component or a display device.