WO2011086809A1 - 融液保持容器 - Google Patents
融液保持容器 Download PDFInfo
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- WO2011086809A1 WO2011086809A1 PCT/JP2010/072676 JP2010072676W WO2011086809A1 WO 2011086809 A1 WO2011086809 A1 WO 2011086809A1 JP 2010072676 W JP2010072676 W JP 2010072676W WO 2011086809 A1 WO2011086809 A1 WO 2011086809A1
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B65—CONVEYING; PACKING; STORING; HANDLING THIN OR FILAMENTARY MATERIAL
- B65D—CONTAINERS FOR STORAGE OR TRANSPORT OF ARTICLES OR MATERIALS, e.g. BAGS, BARRELS, BOTTLES, BOXES, CANS, CARTONS, CRATES, DRUMS, JARS, TANKS, HOPPERS, FORWARDING CONTAINERS; ACCESSORIES, CLOSURES, OR FITTINGS THEREFOR; PACKAGING ELEMENTS; PACKAGES
- B65D1/00—Containers having bodies formed in one piece, e.g. by casting metallic material, by moulding plastics, by blowing vitreous material, by throwing ceramic material, by moulding pulped fibrous material, by deep-drawing operations performed on sheet material
- B65D1/40—Details of walls
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F27—FURNACES; KILNS; OVENS; RETORTS
- F27B—FURNACES, KILNS, OVENS, OR RETORTS IN GENERAL; OPEN SINTERING OR LIKE APPARATUS
- F27B14/00—Crucible or pot furnaces
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- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/01—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics
- C04B35/16—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on silicates other than clay
- C04B35/18—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on silicates other than clay rich in aluminium oxide
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- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/515—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics
- C04B35/56—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on carbides or oxycarbides
- C04B35/565—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on carbides or oxycarbides based on silicon carbide
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F27—FURNACES; KILNS; OVENS; RETORTS
- F27B—FURNACES, KILNS, OVENS, OR RETORTS IN GENERAL; OPEN SINTERING OR LIKE APPARATUS
- F27B14/00—Crucible or pot furnaces
- F27B14/08—Details peculiar to crucible or pot furnaces
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F27—FURNACES; KILNS; OVENS; RETORTS
- F27D—DETAILS OR ACCESSORIES OF FURNACES, KILNS, OVENS, OR RETORTS, IN SO FAR AS THEY ARE OF KINDS OCCURRING IN MORE THAN ONE KIND OF FURNACE
- F27D1/00—Casings; Linings; Walls; Roofs
- F27D1/0003—Linings or walls
- F27D1/0006—Linings or walls formed from bricks or layers with a particular composition or specific characteristics
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- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
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- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3217—Aluminum oxide or oxide forming salts thereof, e.g. bauxite, alpha-alumina
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- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/34—Non-metal oxides, non-metal mixed oxides, or salts thereof that form the non-metal oxides upon heating, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3418—Silicon oxide, silicic acids, or oxide forming salts thereof, e.g. silica sol, fused silica, silica fume, cristobalite, quartz or flint
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- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/38—Non-oxide ceramic constituents or additives
- C04B2235/3817—Carbides
- C04B2235/3826—Silicon carbides
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- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
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- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
- C04B2235/74—Physical characteristics
- C04B2235/77—Density
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- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
- C04B2235/96—Properties of ceramic products, e.g. mechanical properties such as strength, toughness, wear resistance
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- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
- C04B2235/96—Properties of ceramic products, e.g. mechanical properties such as strength, toughness, wear resistance
- C04B2235/9607—Thermal properties, e.g. thermal expansion coefficient
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- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
- C04B2235/96—Properties of ceramic products, e.g. mechanical properties such as strength, toughness, wear resistance
- C04B2235/9669—Resistance against chemicals, e.g. against molten glass or molten salts
- C04B2235/9676—Resistance against chemicals, e.g. against molten glass or molten salts against molten metals such as steel or aluminium
Definitions
- the present invention relates to a melt holding container.
- melt holding container As a container for holding a melt such as a molten metal or a molten salt (hereinafter also referred to as “melt holding container”), a heat-resistant metal container or an iron container such as a ladle is used.
- An iron container such as a ladle usually has a ceramic lining inside the container.
- the lining material an indefinite refractory material such as castable is generally used.
- Patent Document 1 discloses an induction furnace having a multilayer lining structure in which a low-breathing shaped material is arranged on an outer layer portion of a lining material.
- the induction furnace is provided with a low-breathable shaped material on the outer layer part of the lining material. It has a two-layer structure with a dry-type amorphous refractory on the inner layer.
- Patent Document 2 there is an impermeability to the inner surface of the iron can body so that the iron can body is not corroded by the corrosive gas generated during the production of hydrochloric acid, zinc chloride or titanium oxide contained in the raw material of activated carbon.
- a rotary kiln is disclosed in which a film is lined and a brick layer is formed on the inside to form a two-layer lining structure.
- Patent Document 3 discloses a hot water leak detection device for an induction melting furnace.
- the inner surface in contact with the molten metal is formed with a molten metal holding lining obtained by sintering a powder refractory material, and castable cement on the outer periphery.
- a two-layer structure provided with a coil holding lining formed in a cylindrical shape.
- Patent Document 4 describes corrosion resistance and spalling resistance (cracking and cracking of refractories) in vessels such as blast furnaces, flash furnaces, converters, and holding furnaces for non-ferrous metals (copper, zinc, lead, etc.) excluding aluminum.
- a high durability non-ferrous metal refractory with improved phenomenon) is disclosed.
- the refractory mainly contains Al 2 O 3 and further contains ZrO 2 , Cr 2 O 3 and SiO 2 .
- melt holding container examples include a melt of zinc chloride by-produced by a zinc reduction reaction of silicon tetrachloride or a melt holding container for holding a mixed melt of zinc chloride and zinc.
- a melt holding container for holding a melt of zinc chloride produced as a by-product or a mixed melt of zinc chloride and zinc is not suitable for melting.
- the container must be capable of preventing contamination of the liquid with impurities.
- the functions required in the melt holding container are the following three points.
- the present invention has been made in view of the above-described circumstances.
- a container for holding a metal melt and / or a metal salt melt the amount of heat released from the melt is small, and the melt penetrates and cracks and cracks are generated.
- An object of the present invention is to provide a melt holding container that can suppress generation and suitably hold the melt, and can prevent contamination of the melt with impurities.
- the present inventors have found that the melt holding container having a specific multilayer structure has a small amount of heat released from the melt, causing the melt to penetrate, crack, and crack. As a result, the present inventors have found that not only can the melt be suitably retained, but also the contamination of the melt can be prevented, and the present invention has been completed.
- the present invention relates to the following [1] to [5], for example.
- a container for holding a metal melt and / or a metal salt melt A first layer formed from a refractory having an apparent porosity of 12% or less and a second layer formed from a refractory having a thermal conductivity at 800 ° C. of 4 W / m ⁇ k or less in order from the inside of the container. And a third layer formed of a refractory having a higher thermal conductivity than the second layer.
- the amount of elution into the melt of the material forming the first layer when the melt at 500 ° C. is allowed to stand for 30 days is 0.2% by mass or less
- the refractory constituting the first layer has a thermal conductivity at 800 ° C. of 15 W / m ⁇ k or more
- the refractory constituting the second layer has an apparent porosity of 20% or less
- the refractory constituting the third layer has an apparent porosity of 12% or less
- the melt holding container of the present invention has a small amount of heat released from the melt, can minimize the penetration, cracking and cracking of the melt, and can not only hold the melt suitably, but also contaminate the melt. Can be prevented.
- FIG. 1 is an example of a schematic cross-sectional view of a melt holding container of the present invention.
- the melt holding container of the present invention is a container for holding a metal melt and / or a metal salt melt, and is a first layer formed from a refractory having an apparent porosity of 12% or less, 800 ° C.
- the second layer is formed of a refractory having a thermal conductivity of 4 W / m ⁇ k or less
- the third layer is formed of a refractory having a higher thermal conductivity than the second layer.
- the melt holding container having such a configuration has a small amount of heat released from the melt, can suppress the penetration, cracking and cracking of the melt, and can not only suitably hold the melt but also contaminate the melt with impurities. Can be prevented.
- the first layer in contact with the retained melt is formed from a dense refractory.
- the apparent porosity of the refractory constituting the first layer is 12% or less, and more preferably 5 to 10%. When the apparent porosity of the refractory constituting the first layer is within the above range, the penetration of the melt tends to be suppressed.
- the thermal conductivity at 800 ° C. of the refractory constituting the first layer is preferably 15 W / m ⁇ k or more, and more preferably 15 to 20 W / m ⁇ k.
- the thermal shock resistance of the melt holding container tends to be improved.
- the apparent porosity and thermal conductivity are values obtained by the measurement methods shown in the examples described later.
- the amount of the material forming the first layer eluted into the melt is preferably 0.2% by mass or less, and 0.05 to More preferably, it is 0.2 mass%.
- the elution amount of the material forming the first layer into the melt is within the above range, impurity contamination of the melt can be prevented.
- Examples of the refractory forming the first layer include silicon carbide castable refractories.
- Constituent components of the silicon carbide castable refractory mainly include SiC: 75 to 90% by mass (preferably 80 to 85% by mass), Al 2 O 3 : 5 to 15% by mass (preferably 5 to 10% by mass).
- SiO 2 1 to 10% by mass (preferably 3 to 8% by mass).
- positioned on the outer side of a 1st layer is formed from the heat insulation refractory material whose heat insulation performance is larger than the said 1st layer.
- the heat radiation amount of the melt can be suppressed.
- the heat conductivity at 800 ° C. of the refractory constituting the second layer is 4 W / m ⁇ k or less, preferably 1 to 4 W / m ⁇ k.
- the apparent porosity of the refractory constituting the second layer is preferably 20% or less, more preferably 10 to 20%.
- the apparent porosity of the refractory constituting the second layer is within the above range, the penetration of the melt tends to be suppressed.
- a heat insulation castable refractory As a refractory which forms the 2nd layer, a heat insulation castable refractory is mentioned, for example.
- the components of the heat insulating castable refractory mainly include SiC: 0 to 40% by mass (preferably 20 to 40% by mass), Al 2 O 3 : 30 to 70% by mass (preferably 30 to 60% by mass), SiO 2 2 : 20 to 40% (preferably 20 to 30% by mass).
- the third layer disposed outside the second layer is formed of a refractory having a higher thermal conductivity than the second layer.
- a refractory having a higher thermal conductivity than the second layer it is possible to prevent the melting line (temperature range lower than the melting point of the melt) in the refractory layer from moving outside the container. it can. That is, by using a high thermal conductivity refractory having a higher thermal conductivity than the second layer as the third layer, the solidification of the melt is achieved in the second layer, so that leakage of the melt can be prevented. Therefore, even when a metal layer is formed outside the third layer, it is possible to prevent the metal layer and the melt from coming into direct contact, and as a result, contamination of the melt can be prevented.
- Refractories with high thermal conductivity can reduce the internal temperature gradient, so that refractory cracking due to thermal history can be suppressed.
- the heat conductivity at 800 ° C. of the refractory constituting the third layer is preferably 15 W / m ⁇ k or more, more preferably 15 to 20 W / m ⁇ k.
- the thermal conductivity of the refractory constituting the third layer is within the above range, the temperature difference between the inside and outside of the third layer can be minimized, and the inner surface temperature can be designed to be equal to or lower than the melting point of the holding melt. It becomes easy.
- the apparent porosity of the refractory constituting the third layer is preferably 12% or less, more preferably 5 to 10%.
- the apparent porosity of the refractory constituting the third layer is within the above range, the penetration of the melt tends to be suppressed.
- Examples of the refractory forming the third layer include silicon carbide castable refractories.
- Constituent components of the silicon carbide castable refractory mainly include SiC: 75 to 90% by mass (preferably 80 to 85% by mass), Al 2 O 3 : 5 to 15% by mass (preferably 5 to 10% by mass).
- SiO 2 1 to 10% by mass (preferably 3 to 8% by mass).
- the third layer is not particularly limited as long as it satisfies the above characteristics, but is preferably formed from the same refractory as the first layer.
- the melt holding container of the present invention may further have a metal layer outside the third layer.
- a metal layer By having the metal layer, the strength of the melt holding container can be improved.
- the metal species that form such a metal layer include iron and stainless steel.
- metal melt examples include metal melts such as zinc, aluminum, and magnesium.
- metal salt melt examples include metal salt melts such as zinc chloride, aluminum chloride, and magnesium chloride.
- melt holding container such as a vertical cylindrical container, a horizontal cylindrical container, a box container, and a reverse bell-shaped container, and the shape is not particularly limited.
- a melt holding container having a cylindrical container shape can be obtained, for example, by lining the first to third layers inside a cylindrical metal container and sufficiently curing the container.
- the temperature of the interface between the second layer and the third layer when the melt at 500 ° C. is held for 30 days is lower than the melting point of the melt.
- the temperature at the interface between the second layer and the third layer is controlled to be lower than the melting point of the melt.
- the melt is solidified at the interface between the second layer and the third layer, and the permeation further proceeds. Disappear.
- the melt does not reach the outermost metal shell of the container and cause damage such as erosion.
- Control of the temperature of the interface between the second layer and the third layer can be achieved by selecting the refractory material for the first layer and the third layer and by optimizing the thickness of the first layer and the third layer. Achieved.
- the temperature at the interface between the second layer and the third layer can be made lower than the melting point of the melt.
- the temperature of the interface between the second layer and the third layer can be efficiently lowered below the melting point of the melt.
- the temperature of the interface between the second layer and the third layer is controlled while keeping the refractory thickness to the minimum necessary. It is preferable to design the melt holding container so that it can be lower than the melting point.
- the thickness of each layer is preferably 200 mm or less.
- the outer surface temperature of the melt holding container when the melt at 500 ° C. is held for 30 days is preferably 200 ° C. or less. If the outer surface temperature of the melt holding container when the melt at 500 ° C. is held for 30 days is within the above range, the life of the metal container is extended without reaching the outer wall and the heat energy is increased. Loss can be kept low.
- each layer it is preferable to design the thickness of each layer so that the outer surface temperature of the melt holding container when the melt at 500 ° C. is held for 30 days is within the above range.
- the melt holding container of the present invention condenses and liquefies by-product zinc chloride gas, or by-product zinc chloride gas and unreacted zinc gas, for example, in a method for producing high purity silicon by zinc reduction of silicon tetrachloride.
- Condensed liquefaction equipment, melt of zinc chloride by-product, or melt storage (reception) tank that retains and stores a mixed melt of zinc chloride and zinc by-product, is attached to a reduction reactor, and the raw material zinc gas is It can be used in a zinc evaporator to be supplied, an electrolytic cell for recovering zinc and chlorine by electrolyzing zinc chloride produced as a by-product.
- the present inventor according to Japanese Patent Application No. 2009-168812 already filed, in a method for producing high-purity silicon by zinc reduction of silicon tetrachloride, a condensing liquefaction apparatus for recovering by-produced zinc chloride and unreacted zinc. Although it discloses, it does not mention in particular about the constituent material of this condensing liquefying apparatus.
- Thermal conductivity of the refractory was measured in accordance with the refractory brick test method of the JIS R2616 heat flow method with the test piece heated to 400 ° C. and 800 ° C.
- the apparent porosity of the refractory was measured according to JIS R2205 by holding the test piece at 1000 ° C. in a reducing atmosphere.
- Example 1 Manufacture of melt holding container As members constituting the melt holding container, refractory A having the composition and physical properties shown in Table 1 (manufactured by Nippon Special Furnace Co., Ltd., Flexite KERSIK-PB) and fire resistance Material B (manufactured by Nippon Special Furnace Co., Ltd., Flexite TM-65C3) and a vertical cylindrical iron container (outer diameter 75 cm, length 75 cm, thickness 6 mm) were used.
- Table 1 manufactured by Nippon Special Furnace Co., Ltd., Flexite KERSIK-PB
- fire resistance Material B manufactured by Nippon Special Furnace Co., Ltd., Flexite TM-65C3
- a vertical cylindrical iron container outer diameter 75 cm, length 75 cm, thickness 6 mm
- the refractory A was lined with a thickness of 50 mm inside the vertical cylindrical iron container to form a layer (third layer) made of the refractory A.
- the refractory B was lined with a thickness of 150 mm on the refractory A layer (third layer) to form a refractory B layer (second layer).
- the refractory A was lined with a thickness of 50 mm on the refractory B layer (second layer) to form the refractory A layer (first layer).
- Each refractory A and B was sufficiently cured, and a melt holding container having the first to third layers and the metal (iron) layer was manufactured in this order from the inside of the container.
- the amount of elution of the layer made of refractory A (first layer) into the melt was measured and found to be 0.1% by mass.
- the refractory A was lined with a thickness of 200 mm inside the vertical cylindrical iron container to form a layer (first layer) made of the refractory A. Then, the refractory A was sufficiently cured, and a melt holding container (inner diameter: 35 cm) having the first layer and the metal (iron) layer was manufactured from the inside of the container.
- Comparative Example 2 In Comparative Example 1, the thickness of the layer (first layer) made of the refractory A necessary for setting the outer surface temperature of the melt holding container to about 150 ° C. was calculated by heat transfer calculation. As a result, it has been found that in order to set the outer surface temperature of the melt holding container to 145 ° C., the thickness of the layer made of the refractory A (first layer) must be 1,500 mm.
- the thickness of the refractory A layer (first layer) is 1,500 mm, it is not possible to design an effective container, and it is difficult to accept a single layer of refractory A. It was.
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Abstract
Description
ii)融液の浸透量の少ない保持機能
iii)保持容器からの不純物汚染防止機能
塩化亜鉛等の金属塩化物の融液を保持する容器においては、一般的に金属や酸化物に対するフラックス効果(融液と容器との接触面に存在する酸化物等を溶出する現象)が大きく、融液と接触する容器材料からの不純物溶出による汚染を受けやすいという問題がある。したがって、融液保持容器において、上記i)及びii)の要件は当然配慮しなければならないが、特に塩化亜鉛等の金属塩化物の融液を保持する容器においては、上記iii)の要件を満たすことが求められる。
該容器の内側から順に、見かけ気孔率が12%以下である耐火物から形成される第1層、800℃における熱伝導度が4W/m・k以下である耐火物から形成される第2層、および第2層より熱伝導度が大きい耐火物から形成される第3層を有することを特徴とする融液保持容器。
前記第1層を構成する耐火物が、800℃における熱伝導度が15W/m・k以上であり、
前記第2層を構成する耐火物が、見かけ気孔率が20%以下であり、
前記第3層を構成する耐火物が、見かけ気孔率が12%以下であり、800℃における熱伝導度が15W/m・k以上であることを特徴とする[1]に記載の融液保持容器。
本発明の融液保持容器は、金属の融液および/または金属塩の融液を保持する容器であって、見かけ気孔率が12%以下である耐火物から形成される第1層、800℃における熱伝導度が4W/m・k以下である耐火物から形成される第2層、および第2層より熱伝導度が大きい耐火物から形成される第3層を有することを特徴としている。
保持する融液と接触する第1層は、緻密な耐火物から形成される。第1層を緻密な耐火物から形成することにより、融液の浸透を抑制することができる。第1層を構成する耐火物の見かけ気孔率は、12%以下であり、5~10%であることがより好ましい。第1層を構成する耐火物の見かけ気孔率が前記範囲内であると、融液の浸透を抑制できる傾向がある。
第1層の外側に配設される第2層は、前記第1層より断熱性能が大きい断熱耐火物から形成される。第2層を第1層より断熱性能が大きい断熱耐火物から形成することにより、融液の放熱量を抑制することができる。このような第2層を構成する耐火物の800℃における熱伝導度は、4W/m・k以下であり、1~4W/m・kであることが好ましい。第2層を構成する耐火物の熱伝導度が前記範囲内であると、融液の放熱量を抑制することができる。
第2層の外側に配設される第3層は、第2層より熱伝導度が大きい耐火物から形成される。第3層を第2層より熱伝導度が大きい耐火物から形成することにより、耐火物層中の溶融線(融液の融点よりも低い温度域)を容器外側に移動させないようにすることができる。すなわち、第3層として、第2層より熱伝導度が大きい高熱伝導性の耐火物を使うことで、第2層内で融液の凝固が達成されるため融液の漏れを防止できる。したがって、第3層外側に金属層が形成される場合でも、該金属層と融液とが直接接触することを防止でき、結果として融液の汚染防止ができる。
本発明の融液保持容器は、例えば、四塩化珪素の亜鉛還元による高純度シリコンの製造法において、副生する塩化亜鉛ガス、または副生する塩化亜鉛ガスと未反応亜鉛ガスとを凝縮液化する凝縮液化装置、副生する塩化亜鉛の融液、または副生する塩化亜鉛と亜鉛との混合融液を滞留・貯留する融液貯留(受け)槽、還元反応炉に付設して原料亜鉛ガスを供給する亜鉛蒸発器、副生する塩化亜鉛を電解して亜鉛と塩素とを回収するための電解槽などに用いることができる。
耐火物の熱伝導度は、試験片を400℃および800℃に加熱保持し、JIS R2616熱流法の耐火物レンガの試験法に準拠して測定した。
耐火物の見かけ気孔率は、試験片を還元雰囲気に於いて1000℃に加熱保持し、JIS R2205に準拠して測定した。
耐火物の曲げ強度は、試験片を110℃および1000℃に加熱保持し、JIS R2213に準拠して測定した。
耐火物の圧縮強度は、試験片を110℃および1000℃に加熱保持し、JIS R2553のキャスタブル耐火物の試験法に準拠して測定した。
(1)融液保持容器の製造
融液保持容器を構成する部材として、表1に示す組成及び物理的性質を有する耐火物A(日本特殊炉材株式会社製、フレキサイトKERSIK-PB)および耐火物B(日本特殊炉材株式会社製、フレキサイトTM-65C3)、ならびに縦型円筒鉄製容器(外径75cm、長さ75cm、厚さ6mm)を用いた。
上記(1)で製造した融液保持容器に塩化亜鉛の融液80kgを導入し、融液中に保護管付電熱ヒーターを挿入して、融液温度を500℃に制御し、30日間この状態を保持した。この時の定常状態後の融液保持容器の外側表面温度は167℃であった。
(1)融液保持容器の製造
融液保持容器を構成する部材として、表1に示す組成及び物理的性質を有する耐火物A、ならびに縦型円筒鉄製容器(外径75cm、長さ75cm、厚さ6mm)を用いた。
上記(1)で製造した融液保持容器に塩化亜鉛の融液80kgを導入し、融液中に保護管付電熱ヒーターを挿入して、融液温度を500℃に制御し、30日間この状態を保持した。この時の定常状態後の融液保持容器の外側表面温度は359℃であり、設計目標である200℃を超えていた。
比較例1において、融液保持容器の外側表面温度を150℃程度とするために必要な耐火物Aからなる層(第1層)の厚みを伝熱計算により算出した。その結果、融液保持容器の外側表面温度を145℃とするためには、耐火物Aからなる層(第1層)の厚みを1,500mmとしなければならないことがわかった。
2:第1層
3:第2層
4:第3層
5:金属層
6:融液
Claims (5)
- 金属の融液および/または金属塩の融液を保持する容器であって、
該容器の内側から順に、見かけ気孔率が12%以下である耐火物から形成される第1層、800℃における熱伝導度が4W/m・k以下である耐火物から形成される第2層、および第2層より熱伝導度が大きい耐火物から形成される第3層を有することを特徴とする融液保持容器。 - 500℃の融液を30日間静置浸漬した場合の、前記第1層を形成する材料の前記融液への溶出量が0.2質量%以下であり、
前記第1層を構成する耐火物が、800℃における熱伝導度が15W/m・k以上であり、
前記第2層を構成する耐火物が、見かけ気孔率が20%以下であり、
前記第3層を構成する耐火物が、見かけ気孔率が12%以下であり、800℃における熱伝導度が15W/m・k以上であることを特徴とする請求項1に記載の融液保持容器。 - 500℃の融液を30日間保持した際の、前記第2層と前記第3層との界面の温度が、前記融液の融点よりも低いことを特徴とする請求項1または2に記載の融液保持容器。
- 前記第3層の外側に、さらに金属層を有することを特徴とする請求項1~3のいずれか一項に記載の融液保持容器。
- 前記金属の融液が亜鉛の融液であり、前記金属塩の融液が塩化亜鉛の融液であることを特徴とする請求項1~4のいずれか一項に記載の融液保持容器。
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US13/521,745 US20130092589A1 (en) | 2010-01-15 | 2010-12-16 | Melt container |
CN2010800612686A CN102741640A (zh) | 2010-01-15 | 2010-12-16 | 融液保持容器 |
JP2011549887A JPWO2011086809A1 (ja) | 2010-01-15 | 2010-12-16 | 融液保持容器 |
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Citations (3)
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JPH0585853A (ja) * | 1991-01-17 | 1993-04-06 | Vesuvius Fr Sa | モノリシツク耐火材料及びその製造方法並びに該材料より形成された耐火材製品 |
JPH09157718A (ja) * | 1995-11-29 | 1997-06-17 | Nisshin Steel Co Ltd | 高炉鋳床樋の耐火物構造 |
JP2000103665A (ja) * | 1998-09-30 | 2000-04-11 | Shinagawa Refract Co Ltd | 不焼成炭素含有耐火物および溶融金属用容器 |
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US4072243A (en) * | 1975-04-21 | 1978-02-07 | Intertec Associates, Inc. | Metal coated brittle containers, conduits and other objects for laboratory and industry |
EP0399786A3 (en) * | 1989-05-25 | 1992-05-27 | Alcan International Limited | Refractory linings capable of resisting sodium and sodium salts |
CN1107820A (zh) * | 1994-12-01 | 1995-09-06 | 牟跃荣 | 超高功率电炉偏心底出钢口新型填充料 |
US7449432B2 (en) * | 2006-03-07 | 2008-11-11 | Ashland Licensing And Intellectual Property, Llc (Alip) | Gear oil composition containing nanomaterial |
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- 2010-12-16 JP JP2011549887A patent/JPWO2011086809A1/ja not_active Withdrawn
- 2010-12-16 US US13/521,745 patent/US20130092589A1/en not_active Abandoned
- 2010-12-16 CN CN2010800612686A patent/CN102741640A/zh active Pending
- 2010-12-30 TW TW099146915A patent/TW201135170A/zh unknown
Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
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JPH0585853A (ja) * | 1991-01-17 | 1993-04-06 | Vesuvius Fr Sa | モノリシツク耐火材料及びその製造方法並びに該材料より形成された耐火材製品 |
JPH09157718A (ja) * | 1995-11-29 | 1997-06-17 | Nisshin Steel Co Ltd | 高炉鋳床樋の耐火物構造 |
JP2000103665A (ja) * | 1998-09-30 | 2000-04-11 | Shinagawa Refract Co Ltd | 不焼成炭素含有耐火物および溶融金属用容器 |
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CN102741640A (zh) | 2012-10-17 |
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