JP2005314185A - Molten glass supplying unit - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a molten glass supplying unit for supplying a molten glass to a molding unit. <P>SOLUTION: In this unit, all or a part of the supplying route in the shape of a pipe or a trough for supplying a molten glass to a molding unit comprises an aluminum titanate or an aluminum magnesium titanate sintered material which is provided by firing at 1,000-1,700 °C, a feed mixture containing 100 pts. mass, as an equivalent of oxide, a mixture (X component) of an aluminum-containing compound and a titanium-containing compound containing the metal component in the same ratio of metal component as an aluminum titanate or an aluminum magnesium titanate shown by the formula: Al<SB>2</SB>TiO<SB>5</SB>or Mg<SB>x</SB>Al<SB>2(1-x)</SB>Ti<SB>(1+x)</SB>O<SB>5</SB>(wherein 0<x<1), and, if necessary, an Mg-containing compound, and 1-10 pts. mass, as an equivalent of oxide, an oxide having a spinel structure, containing alkali feldspar and Mg, and shown by the formula: (Na<SB>y</SB>K<SB>1-y</SB>)AlSi<SB>3</SB>O<SB>8</SB>(wherein 0≤y≤1), or MgO or a Mg-containing compound (Y component) which can be converted into MgO by sintering. <P>COPYRIGHT: (C)2006,JPO&NCIPI

Description

  The present invention relates to a molten glass supply device used when supplying molten glass for forming optical glass products or glass containers to a molding apparatus.

  When molding optical glass products, glass containers such as bottles and tableware, etc., a certain amount of molten glass lump (hereinafter referred to as gob) is supplied to the forming device by a gob supply device. An example of such a gob supply apparatus will be described with reference to FIG. In this gob supply device, a gob supply path is formed by connecting a pipe-shaped gob guide 5, a trough-shaped trough 6 and a turning trough 7. After dropping onto the trough 6, it falls along the trough surface of the trough 6, and is further supplied to the forming device 8 by the action of the turning trough 7.

Conventionally, various materials are known as materials for the gob supply device. For example, Patent Document 1 discloses a gob feeding device cast from heat-resistant stainless steel or aluminum. Patent Document 2 also covers the inside of metal troughs and turning troughs with Teflon (registered trademark, the same applies hereinafter) resin to reduce the resistance when the gob passes and prevent the temperature of the gob from decreasing. Yes. Further, Patent Document 3 discloses that when an optical element is formed from a special glass such as lanthanum glass or phosphate glass, which is invalidated when the temperature of the glass is lowered, in order to keep the molten glass at a high temperature, It has been shown to supply the forming apparatus with a supply pipe formed of platinum or a platinum alloy that can withstand high temperatures.
JP 2003-104732 A JP 2001-233623 A JP 2002-274857 A

  When the gob supply device for supplying the gob to the forming device is formed of heat resistant steel such as stainless steel as described above, although the heat resistance strength is excellent, the gob supply device becomes heavy because the specific gravity is large. The contact resistance when the gob slides or slides on the trough of the trough is large, so that not only the trough wears and the trough life is shortened but also the supply control of the gob is strictly required. Thus, it is necessary to coat the surface of the trough with a Teflon resin with a low contact resistance. However, there was a problem that it was not applicable.

  In addition, as in Patent Document 3, forming the molten glass supply device with expensive platinum or a platinum alloy is limited to small products such as optical glass products even when used because the manufacturing cost increases. The

  An object of the present invention is to provide a molten glass supply device formed of a material that is lightweight, has high heat resistance strength, and is excellent in corrosion resistance and thermal shock resistance against high-temperature molten glass or glass gob.

  The present inventor has intensively studied in order to solve the above problems, and as a material of the molten glass supply device, by using a specific aluminum titanate sintered body or aluminum magnesium titanate sintered body, the above object can be obtained. Found that can be achieved.

  That is, the present inventor has found that a specific aluminum titanate sintered body or aluminum magnesium titanate sintered body is excellent in heat resistance and corrosion resistance to high-temperature molten glass or glass gob and has a small thermal expansion coefficient. Since it has excellent thermal shock resistance and high mechanical strength, it has been found that it is extremely excellent as a material for a molten glass supply device that comes into contact with high-temperature molten glass, and has reached the present invention.

That is, this invention provides the following molten glass supply apparatus.
(1) A bowl-shaped or pipe-shaped molten glass supply apparatus for supplying molten glass to a molding apparatus, wherein a part or all of the bowl-shaped or pipe-shaped supply path is
Composition ratio: Al ₂ TiO ₅ or Mg _x Al _{2 (1-x)} Ti _{(1 + x)} O ₅ (wherein 0 <x <1) and the metal component ratio in aluminum titanate or aluminum magnesium titanate And 100 parts by mass of a mixture containing an Al-containing compound, a Ti-containing compound, and an Mg-containing compound as required (X component), in an equivalent amount of oxide, and a composition formula: (Na _y K _{1) -y} ) AlSi ₃ O ₈ (wherein 0 ≦ y ≦ 1), an alkali feldspar, an oxide having a spinel structure containing Mg, or an Mg-containing compound that is converted to MgO by firing with MgO (referred to as Y component) Formed from an aluminum titanate or aluminum magnesium titanate sintered body obtained by firing a raw material mixture containing 1 to 10 parts by mass in terms of oxide in an amount of 1000 to 1700 ° C. Molten glass supply device according to claim.
(2) The X component is a mixture containing an Al-containing compound and a Ti-containing compound, which is contained in the same metal component ratio as each metal component ratio in aluminum titanate represented by Al ₂ TiO ₅ , and the Y component is (Na _y K _1-y ) AlSi ₃ O ₈ (wherein 0 ≦ y ≦ 1), an feldspar represented by Mg, a spinel-type oxide containing Mg and / or MgO or a Mg-containing compound that is converted to MgO by firing The molten glass supply device according to (1), which is a mixture of
(3) Metal component ratio similar to the metal component ratio in aluminum magnesium titanate represented by X component being Mg _x Al _{2 (1-x)} Ti _{(1 + x)} O ₅ (where 0 <x <1) And a mixture containing an Al-containing compound, a Ti-containing compound and an Mg-containing compound, and the Y component is represented by the composition formula: (Na _y K _1-y ) AlSi ₃ O ₈ (where 0 ≦ y ≦ 1) The molten glass supply apparatus according to the above (1), which is an alkali feldspar represented.
(4) The molten glass supply device according to any one of the above (1) to (3), wherein the molten glass supply device is a glass gob supply device for forming an optical glass product or a glass container.

  In the molten glass supply apparatus according to the present invention, the supply path in contact with the molten glass is excellent in heat resistance and corrosion resistance to high-temperature molten glass, has a small thermal expansion coefficient, and is excellent in thermal shock resistance, and in conventional stainless steel. It is made of a ceramic material that is lighter in weight and has a desired mechanical strength. As a result, molten glass can be smoothly and stably supplied to various glass product forming apparatuses, and high-temperature molten glass that can only be handled by platinum or a platinum alloy can be supplied. In addition, because of its excellent thermal shock resistance, even if it is used repeatedly as a molten glass supply device, it does not break due to thermal shock, and even when it comes into contact with high-temperature molten glass, it does not decompose or react. Therefore, the lifetime of the device can be kept long.

  The present invention relates to a molten glass supply device that supplies molten glass for forming various glass products such as optical glass products such as lenses and optical elements, glass containers such as bottles and tableware, and lighting tubes, to a molding apparatus. . Here, the molten glass supplied to the molding apparatus is generally supplied as a gob cut into a certain amount of molten glass lump, but depending on the type of product to be molded, the molten glass is not in the form of a gob. In other words, it can be supplied in a non-gob state. The molten glass in the present invention includes any of these gob-like and non-gob-like forms.

  The molten glass supply apparatus in the present invention has a bowl-shaped or pipe-shaped supply path for supplying these gob-shaped or non-gob-shaped molten glass to the molding apparatus. In the molten glass supply apparatus according to the present invention, a part or all of the bowl-shaped or pipe-shaped supply path is formed from a ceramic material described in detail below.

In the present invention, as described above, a part or all of the bowl-like or pipe-like supply path of the molten glass supply apparatus has a composition formula: Al ₂ TiO ₅ or Mg _x Al _{2 (1-x)} Ti _{(1 + x)} O ₅ (wherein, Al-containing compound, Ti-containing compound, if necessary, containing at a metal component ratio similar to the metal component ratio in aluminum titanate or aluminum magnesium titanate represented by 0 <x <1) 100 parts by mass of the mixture containing the Mg-containing compound (component X) in terms of oxide and the composition formula: (Na _y K _1-y ) AlSi ₃ O ₈ (where 0 ≦ y ≦ 1) 1000 to 1000 parts of a raw material mixture containing 1 to 10 parts by mass of an alkali feldspar, an oxide having a spinel structure containing Mg, or MgO or an Mg-containing compound (referred to as Y component) that is converted into MgO by firing. Baked at 1700 ° C It is formed from the formed aluminum titanate or aluminum magnesium titanate sintered body.

The Al-containing compound, the Ti-containing compound, and the Mg-containing compound included as necessary, which form the X component in the above, are calcined to form a composition formula: Al ₂ TiO ₅ or Mg _x Al _{2 (1-x)} Ti _{(1 + x)} O ₅ (wherein 0 <x <1) can be used without particular limitation as long as it is a component that forms aluminum titanate or aluminum magnesium titanate. The Mg-containing compound, Al-containing compound, and Ti-containing compound may not be separate compounds, but may be a compound containing two or more metal components. These compounds are appropriately selected from those usually used as raw materials for various ceramics such as alumina ceramics, titania ceramics, magnesia ceramics, aluminum titanate ceramics, magnesium titanate ceramics, spinel ceramics, aluminum magnesium titanate ceramics, etc. Can be used. Specific examples of such a compound include two or more kinds of oxides such as Al ₂ O ₃ , TiO ₂ , and MgO, MgAl ₂ O ₄ , Al ₂ TiO ₅ , and spinel structures containing Mg and Ti. Examples thereof include composite oxides containing metal components, compounds containing one or more metal components selected from the group consisting of Al, Ti and Mg (carbonates, nitrates, sulfates, etc.).

The mixing ratio of the Al-containing compound, Ti-containing compound, and Mg-containing compound is such that the ratio of the metal components contained in these compounds is the above-described composition formula: Al ₂ TiO ₅ or Mg _x Al _{2 (1-x )} Metals of Mg, Al and Ti in aluminum magnesium titanate represented by Ti _{(1 + x)} O ₅ (where 0 <x <1, preferably 0.2 ≦ x ≦ 0.8) The ratio may be the same as the component ratio, preferably the substantially same ratio. By mixing and using each of the above compounds at such a ratio, it is possible to obtain aluminum titanate or aluminum magnesium titanate having a metal component ratio similar to the metal component ratio in the mixture used as a raw material.

The Y component to be mixed with the above X component is composed of an alkali feldspar, an oxide having a spinel structure containing Mg, or MgO or a Mg-containing compound that is converted to MgO by firing. As the alkali feldspar that is one of the Y components, those represented by the composition formula: (Na _y K _1-y ) AlSi ₃ O ₈ are used. In the formula, y satisfies 0 ≦ y ≦ 1, preferably 0.1 ≦ y ≦ 1, and particularly preferably 0.15 ≦ y ≦ 0.85. Alkaline feldspar having a y value in this range has a low melting point, and is particularly effective for promoting the sintering of aluminum titanate or aluminum magnesium titanate.

As an oxide having a spinel structure containing Mg, which is another Y component, for example, MgAl ₂ O ₄ , MgTi ₂ O _4, or the like can be used. The oxide having such a spinel structure may be a natural mineral, a substance containing MgO and Al ₂ O ₃ , a substance containing MgO and TiO ₂ , or a spinel oxide obtained by firing the substance. May be. Two or more kinds of oxides having different types of spinel structures may be mixed and used. Any MgO precursor can be used as long as it forms MgO by firing, and examples thereof include MgCO ₃ , Mg (NO ₃ ) ₂ , MgSO _{4, and} mixtures thereof.

  The mixing ratio of the X component and the Y component is important, and the Y component is 1 to 10 parts by mass with respect to 100 parts by mass of the X component. Note that each of the X component and the Y component is a ratio as an oxide, and when a raw material other than the oxide is used, the value is converted to an oxide. When the Y component relative to 100 parts by mass of the X component is smaller than 1 part by mass, the effect of adding the Y component is small in improving the characteristics of the sintered body. On the contrary, when the amount exceeds 10 parts by mass, the solid solubility limit of Si or Mg element in aluminum titanate or aluminum magnesium titanate crystal is greatly exceeded. It is unsuitable because it results in an increase in the coefficient of thermal expansion. Especially, 3-7 mass parts is suitable for Y component with respect to 100 mass parts of X components.

In the present invention, the X component is a mixture containing an Al-containing compound and a Ti-containing compound, which is contained in a metal component ratio similar to the metal component ratio in aluminum titanate represented by the composition formula: Al ₂ TiO ₅ , and The Y component is an alkali feldspar represented by the composition formula: (Na _y K _1-y ) AlSi ₃ O ₈ (where 0 ≦ y ≦ 1), Mg-containing spinel-type oxide, and / or A mixture of MgO or its precursor is preferable because an aluminum titanate sintered body having excellent characteristics can be obtained. In this case, the mixture of the alkali feldspar, which is the Y component, and the spinel-type oxide containing Mg and / or MgO or a precursor thereof preferably has a ratio of the former / the latter of 2 to 6/8. -4, particularly 3.5 to 4.5 / 6.5 to 5.5 is preferred.

Further, in the present invention, the X component is a metal component ratio in magnesium aluminum titanate represented by Mg _x Al _{2 (1-x)} Ti _{(1 + x)} O ₅ (where 0 <x <1). It is a mixture containing an Al-containing compound, a Ti-containing compound and an Mg-containing compound, which are contained in the same metal component ratio, and the Y component has a composition formula: (Na _y K _1-y ) AlSi ₃ O ₈ (wherein The alkali feldspar represented by 0 ≦ y ≦ 1) is preferable because an aluminum magnesium titanate sintered body having particularly excellent characteristics can be obtained.

In the present invention, in addition to the above-mentioned X component and Y component, other sintering aids can be used as necessary, and the properties of the resulting sintered body can be improved. Other sintering aids such _{as, SiO 2, ZrO 2, FeO} 3, CaO, and the like Y ₂ O _3.

  The raw material mixture containing the X component and the Y component is sufficiently mixed and pulverized. The mixing and pulverization of the raw material mixture is not particularly limited and is performed according to a known method. For example, a ball mill, a medium stirring mill, or the like may be used. The degree of pulverization of the raw material mixture is not particularly limited, but the average particle size is preferably 30 μm or less, particularly preferably 8 to 15 μm. This is preferably as small as possible as long as secondary particles are not formed.

  Preferably, a molding aid can be blended in the raw material mixture. As molding aids, known ones such as binders, mold release agents, antifoaming agents, and peptizers can be used. As the binder, polyvinyl alcohol, microwax emulsion, methylcellulose, carboxymethylcellulose and the like are preferable. As the releasing agent, stearic acid emulsion and the like are preferable, as the antifoaming agent, n-octyl alcohol, octylphenoxyethanol and the like are preferable, and as the peptizer, diethylamine, triethylamine and the like are preferable.

  The amount of the molding aid used is not particularly limited, but in the case of the present invention, both are solids with respect to a total amount of 100 parts by mass of the X component and Y component (converted as oxides) used as raw materials. The following ranges are preferable in terms of conversion. That is, the binder is preferably about 0.2 to 0.6 parts by weight, the release agent is preferably about 0.2 to 0.7 parts by weight, and the antifoaming agent is preferably 0.5 to 1.5 parts by weight. It is preferable to use about 0.5 to 1.5 parts by weight of peptizer and peptizer.

  The raw material mixture to which the molding aid is added is mixed and kneaded and molded into a molded body having a predetermined shape by a known molding method such as casting molding or CIP molding. The shaped body is preferably dried and then fired at 1250-1700 ° C, preferably 1300-1450 ° C. There is no particular limitation on the firing atmosphere, and an oxygen-containing atmosphere such as air that is usually employed is preferable. The firing time may be fired until the sintering proceeds sufficiently, and usually about 1 to 20 hours is employed.

There is no restriction | limiting in particular also about the temperature increase rate and temperature decrease rate in the case of the said baking, What is necessary is just to set suitably the conditions which a crack etc. do not enter in the obtained sintered compact. For example, it is preferable to gradually raise the temperature without rapidly raising the temperature in order to sufficiently remove moisture, binders and other molding aids contained in the raw material mixture. Further, prior to heating to the sintering temperature as described above, if necessary, preferably in a temperature range of about 500 to 1000 ° C., it is preferable to perform baking by gentle heating of about 10 to 30 hours. In this case, it is possible to relieve the stress in the sintered body that causes cracking when aluminum titanate or aluminum magnesium titanate is formed, and to suppress the generation of cracks in the sintered body to achieve a dense and uniform structure. Can be obtained.

  The sintered body obtained in this way has an aluminum titanate or magnesium aluminum titanate formed from the X component as a basic component, a Y component, an Si component contained in alkali feldspar, and a spinel structure containing Mg. Mg components derived from oxides of Mg, MgO, or Mg-containing compounds that are converted to MgO by firing are dissolved in the crystal lattice of aluminum titanate or aluminum magnesium titanate. As described above, such a sintered body has a high mechanical strength and a low thermal expansion coefficient, and has a stable crystal structure, so that the sintered body has excellent thermal decomposition resistance.

The ceramic material composed of the sintered body of aluminum titanate or aluminum magnesium titanate is lightweight, excellent in heat resistance and corrosion resistance, and has a small thermal expansion coefficient, and is also excellent in thermal shock resistance. It is particularly suitable as a material for the glass supply device. That is, the specific gravity of the ceramic material is about 3.3, which is about ½ of conventionally used stainless steel (specific gravity: 7.6). In addition, since the ceramic material has a melting temperature of about 1700 ° C. or higher, it can be sufficiently used as a material for a molten glass supply apparatus. In addition, the thermal expansion coefficient at room temperature is as small as about 2.0 × 10 ⁻⁶ K ⁻¹ or less, and since this thermal expansion coefficient hardly changes in the temperature range from room temperature to the molding temperature of glass, a large thermal shock strength is obtained. can get. Furthermore, since it does not decompose or react at all even when it comes into contact with high-temperature glass as a chemical property, it can be used as a raw material for a molten glass supply device.

  Embodiments of the present invention will be described below with reference to the drawings. However, the following drawings are illustrated for facilitating understanding of the molten glass supply apparatus of the present invention, and the present invention is not limited thereto, and includes these changes and improvements. FIG. 1 is a schematic view of a gob supply device for supplying molten glass to a forming device in the form of a gob, and FIG.

  As shown in FIG. 1, the gob supply device of this example (hereinafter referred to as “this device”) includes a gob guide 5, a trough 6, and a turning trough 7, and these go from the gob feeder 1 to the molding device 8. By continuously arranging in this order, a gob supply path is obtained. In this apparatus, the gob 4 can be obtained by cutting a molten glass base extruded from the orifice 2 of the gob feeder 1 into a certain amount of molten glass lump with a cutter 3 installed at the lower part of the orifice 2. The cut gob 4 can be supplied to the molding device 8 through the supply path of the gob supply device. The configuration of such a gob supply device is substantially the same as that of a conventional gob supply device and will not be described in detail, but will be outlined below in order to understand the gob supply device.

  In this apparatus, the gob guide 5 is a cylindrical body having an inner diameter larger than the maximum diameter of the cross-section of the gob 4, and is installed below the cutter 3 so that the opening at the upper end is directly below the orifice 2. It has a role of receiving the falling gob 4 from the opening and transferring it to the trough 6 reliably. The length (height) of the gob guide 5 is not limited as long as it is determined so that this role can be achieved.

  Further, as shown in FIG. 2, the trough 6 has a saddle shape in which the bottom of the cross section has a curved saddle surface with a radius of curvature r, and the gob falling from the lower end of the gob guide 5 is After being received, it is gently bent in the longitudinal direction so that the direction can be changed toward the molding apparatus while being dropped. The radius of curvature r can be appropriately determined according to the size of the gob to be supplied. The turning trough 7 continuously installed at the lower end of the trough 6 has a saddle shape like the trough 6, but the direction of the saddle surface and the direction of bending in the longitudinal direction are opposite to the trough 6. Yes. That is, the direction of the saddle face is opposite to the trough 6, and the gob falling diagonally downward from the trough 6 is received by this reverse face, and subsequently dropped along the saddle face of the turning trough 7. In the meantime, the falling direction of the gob is adjusted downward, and the gob is put into the molding device 8.

In this apparatus, the form of the gob supply apparatus can be changed depending on the type of product to be molded. For example, although not shown, the gob 4 obtained by cutting with the cutter 3 without providing the gob guide 5 may be directly received by the trough 6. Further, when it is desired to sequentially distribute the gob 4 to a plurality of molding positions of the molding device 8 or to a plurality of molding devices, for example, a scoop between the trough 6 and the turning trough 7 (see Japanese Patent Laid-Open No. 2001-233632). After the gob sent from the trough 6 is received by the scoop, the gob can be distributed by rotating the scoop according to the molding position or the position of the molding apparatus. Needless to say, the scoop in this case is also included in the gob feeder. Furthermore, other members can be combined with the gob guide 5, the trough 6, and the turning trough 7 made of the ceramic material as necessary. Examples of other members include heat-resistant steel materials for the purpose of attachment convenience and reinforcement.
In this apparatus, one gob feeder is provided for one gob feeder 1, but a plurality (for example, 2 to 4) of orifices 2 are provided in the gob feeder 1, and the gob is supplied to these orifices 2, respectively. By providing the apparatus, the gob can be simultaneously supplied to a plurality of molding apparatuses.

  In this apparatus, the gob guide 5, the trough 6 and the turning trough 7 constituting the gob supply apparatus are all formed, that is, the entire gob supply path of the gob supply apparatus is formed of the ceramic material. In order to utilize the characteristics of the ceramic material, the entire gob supply path is usually made of the above-mentioned ceramic material instead of the conventional material as in this example. However, a part of the gob supply device, for example, the gob guide 5 in this device. Can be formed of a material other than the above ceramic material. Therefore, the present invention forms part or all of the gob guide 5, the trough 6 and the turning trough 7, etc. constituting the gob supply device, that is, part or all of the gob supply path of the gob supply device is made of the above ceramic material. To do.

  FIG. 3 is a schematic view of an apparatus for supplying molten glass to a molding apparatus in a non-gob form, according to another embodiment of the present invention. As shown in FIG. 3, the molten glass is supplied from the glass melting tank 9 to the molding apparatus 11 in a non-gob form by a supply pipe 10. As described above, such a molten glass supply apparatus is conventionally known. When the molten glass is supplied to the molding apparatus 11 through the supply pipe 10, the molten glass is directly supplied to the molding apparatus 11 as in this example, and a molten glass feeder (not shown) is provided between the supply pipe 10 and the molding apparatus 11. And the like may be supplied from the molten glass feeder to the forming apparatus 11, and the present invention includes such a form.

The present invention is characterized in that the above-described ceramic material is used as the material of the supply pipe 10. In this case, the inner surface of the supply pipe 10 can be covered with a material other than the ceramic material. For example, in order to eliminate or reduce the influence of alkali components such as Na ₂ O and K ₂ O contained in the molten glass, it is one preferable method to coat the inner surface of the supply pipe 10 with, for example, platinum or a platinum alloy. One. Even if the material of the supply pipe 10 is thus changed to the ceramic material of the present invention, the function of the supply pipe 10 is the same. Examples of the cross-sectional shape of the supply pipe 10 include a circular shape, an elliptical shape, a substantially quadrangular shape, and a polygonal shape. However, a circular shape or a substantially quadrangular shape is generally used because of ease of manufacturing and ease of use. . In FIG. 3, the supply pipe 10 is lowered toward the molding apparatus 11, but the molten glass can be supplied by arranging the supply pipe 10 almost horizontally. In this way, when the supply pipe 10 is arranged almost horizontally, the lower half portion through which the molten glass flows is formed into a bowl shape with the above-mentioned ceramic material, and the upper portion thereof is covered with a cover made of the same material or different material from the lower half portion. It may be covered.

  EXAMPLES Hereinafter, the present invention will be specifically described with reference to examples, but the present invention is not construed as being limited thereto.

Example 1
For 100 parts by mass of a mixture composed of 56.1% by mass (50 mol%) of easily sinterable α-type alumina and 43.9% by mass (50 mol%) of anatase type titanium oxide, (Na _0.6 K _0.4 ) 4 parts by mass of alkali feldspar represented by AlSi ₃ O ₈ , 0.25 parts by mass of polyvinyl alcohol as a binder, 1 part by mass of diethylamine as a peptizer, 0.5 mass of polypropylene glycol as an antifoaming agent Part was added and mixed with a ball mill for 3 hours, and then dried with a 120 ° C. dryer for 12 hours or more to obtain a raw material powder.

  The obtained raw material powder was pulverized to an average particle size of 10 μm or less, and a trough-like trough (trough 6 in FIG. 1) was formed by a casting method. Baked in. As a result, a trough having a thickness of 10 mm and a radius of curvature at the bottom of the inner surface (r in FIG. 2) of about 50 mm was obtained.

  The trough was replaced with a stainless steel trough of the gob supply device, and the gob supply was performed for 90 days. As a result, the trough can be easily replaced due to its light weight, and the gob can be supplied more smoothly than the stainless steel trough without being damaged by thermal shock. Also, there was almost no wear by gob on the trough surface.

Example 2
With respect to 100 parts by mass of a mixture composed of 56.1% by mass (50 mol%) of easily sinterable α-type alumina and 43.9% by mass (50 mol%) of anatase type titanium oxide, (Na _0.6 K _0.4 ) 4 parts by mass of an alkali feldspar represented by AlSi ₃ O ₈ , 6 parts by mass of a spinel compound represented by the chemical formula: MgAl ₂ O ₄ , 0.25 parts by mass of polyvinyl alcohol as a binder, and 1 of diethylamine as a peptizer 0.5 parts by mass of polypropylene glycol as a part by mass and an antifoaming agent were added, mixed for 3 hours by a ball mill, and then dried at 120 ° C. by a dryer for 12 hours or more to obtain a raw material powder.

  Using the obtained raw material powder, troughs having the same dimensions were obtained by pulverizing, molding, drying and firing in the same manner as in Example 1.

Example 3 (comparative example)
In Example 1, raw material powder was obtained by carrying out in exactly the same manner except that alkali feldspar was not used. Using the obtained raw material powder, troughs having the same dimensions were obtained by pulverizing, molding, drying and firing in the same manner as in Example 1.

Example 4
26.7 mass% (20 mol%) of easily sinterable α-type alumina, 62.8 mass% (60 mol%) of anatase type titanium oxide, and periclase type magnesium oxide existing as a natural mineral 4 parts by mass of alkali feldspar represented by (Na _0.6 K _0.4 ) AlSi ₃ O ₈ and 0.25 mass of polyvinyl alcohol as a binder with respect to 100 parts by mass of a mixture consisting of 10.5% by mass (20 mol%). 1 part by weight of diethylamine as a peptizer and 0.5 parts by weight of polypropylene glycol as an antifoaming agent were mixed for 3 hours by a ball mill and then dried by a 120 ° C. dryer for 12 hours or more to obtain a raw material powder. .

Using the obtained raw material powder, troughs having the same dimensions were obtained by pulverizing, molding, drying and firing in the same manner as in Example 1.

[Characteristic test]
About the troughs obtained in the above Examples 1 to 4, the thermal expansion coefficient (× 10 ⁻⁶ K ⁻¹ ) from room temperature to 800 ° C., the thermal shock resistance (° C.) by the submerged dropping method, the softening temperature (° C.), and Three-point bending strength (MPa) was measured and the results are shown in Table 1. The thermal expansion coefficient was measured by a method according to JISR1618, the thermal shock resistance was measured by JISR1648, the softening temperature was measured by JISR2209, and the three-point bending strength was measured by a method based on JISR1601. The results are shown in Table 1.

[Pyrolysis resistance test]
A test piece having a length of 10 mm, a width of 10 mm, and a length of 10 mm was cut out from the troughs of Examples 1 to 4 and held in a high-temperature atmosphere at 1100 ° C., and the time-dependent change in residual ratio β (%) of aluminum titanate or aluminum magnesium titanate. A thermal decomposition resistance test was conducted by examining the above.

  The residual ratio of aluminum titanate or aluminum magnesium titanate was determined from the spectrum of X-ray diffraction measurement (XRD) by the following method.

First, when aluminum titanate is thermally decomposed, Al ₂ O ₃ (corundum) and TiO ₂ (rutile) are produced, and when aluminum magnesium titanate is thermally decomposed, MgAl ₂ O ₄ (spinel) and TiO _{2 are produced.} (Rutile) is produced. Therefore, the integrated intensity (I _{TiO2 (110)} ) of the diffraction peak of rutile (110) plane and the integrated intensity I ₍₀₂₃₎ of the diffraction peak of (023) plane of aluminum titanate or aluminum magnesium titanate is used to titanate. The strength ratio R of aluminum or aluminum magnesium titanate to rutile was determined from the following formula.

R = I ₍₀₂₃₎ / (I ₍₀₂₃₎ + _{ITiO2 (110)} )
Further, the strength ratio R ₀ of aluminum titanate or aluminum magnesium titanate to rutile was determined in the same manner for the sintered body before heat treatment at 1100 ° C. Next, using R and R ₀ determined by the above method, the residual ratio β (%) of aluminum titanate or aluminum magnesium titanate was determined from the following formula.

β = (R / R ₀ ) × 100
Table 1 shows the residual ratio β of each crystal after 100 hours for the troughs of Examples 1 to 4.

上記特性を有する実施例１、２及び４のセラミック素材から形成したトラフは、溶融ガラス供給装置として使用でき、優れた性能を発揮する。

The troughs formed from the ceramic materials of Examples 1, 2, and 4 having the above characteristics can be used as a molten glass supply device and exhibit excellent performance.

It is a schematic diagram of a gob supply apparatus. It is arrow sectional drawing of the AA part of FIG. It is a schematic diagram of a molten glass supply apparatus.

Explanation of symbols

1: Gob feeder 2: Orifice 3: Cutter 4: Gob 5: Gob guide 6: Trough 7: Turning trough 8: Molding device 9: Glass melting device 10: Molten glass supply pipe 11: Molding device

Claims (4)

A molten glass supply apparatus having a bowl-shaped or pipe-shaped supply path for supplying molten glass to a molding apparatus, wherein a part or all of the bowl-shaped or pipe-shaped supply path is
Composition ratio: Al ₂ TiO ₅ or Mg _x Al _{2 (1-x)} Ti _{(1 + x)} O ₅ (wherein 0 <x <1) and the metal component ratio in aluminum titanate or aluminum magnesium titanate And 100 parts by mass of a mixture containing an Al-containing compound, a Ti-containing compound, and an Mg-containing compound as required (X component), in an equivalent amount of oxide, and a composition formula: (Na _y K _{1) -y} ) AlSi ₃ O ₈ (wherein 0 ≦ y ≦ 1) an alkali feldspar, an oxide having a spinel structure containing Mg, or Mg-containing compound (Y component) that is converted to MgO by firing. It is formed from an aluminum titanate or aluminum magnesium titanate sintered body obtained by firing a raw material mixture containing 1 to 10 parts by mass as an oxide conversion amount at 1000 to 1700 ° C. Molten glass supply device for. The X component is a mixture containing an Al-containing compound and a Ti-containing compound containing the same metal component ratio as each metal component ratio in aluminum titanate represented by Al ₂ TiO ₅ , and the Y component is (Na _y K _{1 -y} ) an alkali feldspar represented by AlSi ₃ O ₈ (where 0 ≦ y ≦ 1) and an oxide having a spinel structure containing Mg and / or MgO or an Mg-containing compound that is converted to MgO by firing. The molten glass supply apparatus according to claim 1, which is a mixture. X component contains Mg _x Al _{2 (1-x)} Ti _{(1 + x)} O ₅ (wherein 0 <x <1) and a metal component ratio similar to the metal component ratio in aluminum magnesium titanate represented by Alkali is a mixture containing an Al-containing compound, a Ti-containing compound and an Mg-containing compound, and the Y component is represented by the composition formula: (Na _y K _1-y ) AlSi ₃ O ₈ (where 0 ≦ y ≦ 1) The molten glass supply apparatus according to claim 1, which is feldspar.   The molten glass supply apparatus according to any one of claims 1 to 3, wherein the molten glass supply apparatus is a glass gob supply apparatus for forming an optical glass product or a glass container.

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