WO2012049858A1 - 無機繊維質成形体及びその製造方法並びに加熱設備 - Google Patents
無機繊維質成形体及びその製造方法並びに加熱設備 Download PDFInfo
- Publication number
- WO2012049858A1 WO2012049858A1 PCT/JP2011/005763 JP2011005763W WO2012049858A1 WO 2012049858 A1 WO2012049858 A1 WO 2012049858A1 JP 2011005763 W JP2011005763 W JP 2011005763W WO 2012049858 A1 WO2012049858 A1 WO 2012049858A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- fiber
- inorganic
- sio
- weight
- heat treatment
- Prior art date
Links
Images
Classifications
-
- 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
- C04B14/00—Use of inorganic materials as fillers, e.g. pigments, for mortars, concrete or artificial stone; Treatment of inorganic materials specially adapted to enhance their filling properties in mortars, concrete or artificial stone
- C04B14/38—Fibrous materials; Whiskers
- C04B14/46—Rock wool ; Ceramic or silicate fibres
- C04B14/4643—Silicates other than zircon
- C04B14/465—Ca-silicate, e.g. wollastonite
-
- 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
- C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C13/00—Fibre or filament compositions
- C03C13/006—Glass-ceramics fibres
-
- 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
- C04B14/00—Use of inorganic materials as fillers, e.g. pigments, for mortars, concrete or artificial stone; Treatment of inorganic materials specially adapted to enhance their filling properties in mortars, concrete or artificial stone
- C04B14/38—Fibrous materials; Whiskers
- C04B14/40—Asbestos
-
- 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
- C04B28/00—Compositions of mortars, concrete or artificial stone, containing inorganic binders or the reaction product of an inorganic and an organic binder, e.g. polycarboxylate cements
- C04B28/24—Compositions of mortars, concrete or artificial stone, containing inorganic binders or the reaction product of an inorganic and an organic binder, e.g. polycarboxylate cements containing alkyl, ammonium or metal silicates; containing silica sols
-
- 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
- C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/62227—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products obtaining fibres
- C04B35/62231—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products obtaining fibres based on oxide ceramics
- C04B35/6224—Fibres based on silica
-
- 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
- C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/626—Preparing or treating the powders individually or as batches ; preparing or treating macroscopic reinforcing agents for ceramic products, e.g. fibres; mechanical aspects section B
- C04B35/62605—Treating the starting powders individually or as mixtures
- C04B35/62645—Thermal treatment of powders or mixtures thereof other than sintering
-
- 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
- C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/626—Preparing or treating the powders individually or as batches ; preparing or treating macroscopic reinforcing agents for ceramic products, e.g. fibres; mechanical aspects section B
- C04B35/63—Preparing or treating the powders individually or as batches ; preparing or treating macroscopic reinforcing agents for ceramic products, e.g. fibres; mechanical aspects section B using additives specially adapted for forming the products, e.g.. binder binders
- C04B35/6303—Inorganic additives
- C04B35/6316—Binders based on silicon compounds
-
- 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
- C04B35/71—Ceramic products containing macroscopic reinforcing agents
- C04B35/78—Ceramic products containing macroscopic reinforcing agents containing non-metallic materials
- C04B35/80—Fibres, filaments, whiskers, platelets, or the like
- C04B35/82—Asbestos; Glass; Fused silica
-
- 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
- C04B38/00—Porous mortars, concrete, artificial stone or ceramic ware; Preparation thereof
-
- D—TEXTILES; PAPER
- D01—NATURAL OR MAN-MADE THREADS OR FIBRES; SPINNING
- D01F—CHEMICAL FEATURES IN THE MANUFACTURE OF ARTIFICIAL FILAMENTS, THREADS, FIBRES, BRISTLES OR RIBBONS; APPARATUS SPECIALLY ADAPTED FOR THE MANUFACTURE OF CARBON FILAMENTS
- D01F9/00—Artificial filaments or the like of other substances; Manufacture thereof; Apparatus specially adapted for the manufacture of carbon filaments
- D01F9/08—Artificial filaments or the like of other substances; Manufacture thereof; Apparatus specially adapted for the manufacture of carbon filaments of inorganic material
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C2213/00—Glass fibres or filaments
- C03C2213/02—Biodegradable glass fibres
-
- 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
- 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
- C04B2235/3205—Alkaline earth oxides or oxide forming salts thereof, e.g. beryllium oxide
- C04B2235/3206—Magnesium oxides or oxide-forming salts thereof
-
- 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
- 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
- C04B2235/3205—Alkaline earth oxides or oxide forming salts thereof, e.g. beryllium oxide
- C04B2235/3208—Calcium oxide or oxide-forming salts thereof, e.g. lime
-
- 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
- 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
-
- 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
- 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
-
- 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
- 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
- C04B2235/50—Constituents or additives of the starting mixture chosen for their shape or used because of their shape or their physical appearance
- C04B2235/52—Constituents or additives characterised by their shapes
- C04B2235/5208—Fibers
- C04B2235/5216—Inorganic
- C04B2235/522—Oxidic
- C04B2235/5228—Silica and alumina, including aluminosilicates, e.g. mullite
-
- 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
- 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
- C04B2235/50—Constituents or additives of the starting mixture chosen for their shape or used because of their shape or their physical appearance
- C04B2235/52—Constituents or additives characterised by their shapes
- C04B2235/5208—Fibers
- C04B2235/526—Fibers characterised by the length of the fibers
-
- 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
- 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
- C04B2235/50—Constituents or additives of the starting mixture chosen for their shape or used because of their shape or their physical appearance
- C04B2235/52—Constituents or additives characterised by their shapes
- C04B2235/5208—Fibers
- C04B2235/5264—Fibers characterised by the diameter of the fibers
-
- 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
- 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
-
- 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
- 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
- C04B2235/9615—Linear firing shrinkage
-
- 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
- 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
- C04B2235/963—Surface properties, e.g. surface roughness
- C04B2235/9638—Tolerance; Dimensional accuracy
-
- 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
- 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
Definitions
- the present invention relates to an inorganic fiber molded body, a method for producing the same, and a heating facility, and more particularly to suppression of deformation due to heating of an inorganic fiber molded body containing biosoluble inorganic fibers.
- An inorganic fiber molded body containing inorganic fibers and a binder is lightweight, easy to handle, and excellent in heat insulation, and is used, for example, as a heat insulating material in an industrial furnace.
- problems have recently been pointed out that inorganic fibers are inhaled into the human body and enter the lungs.
- biosoluble inorganic fibers contain MgO and CaO, and shrink when heated compared to inorganic fibers that do not have biosolubility such as alumina fibers. It is easy to do, and it is easy to cause thermal creep.
- the present invention has been made in view of the above problems, and is an inorganic fiber in which deformation during heating or at least a part of a high temperature range (hereinafter also referred to as heating during use) is effectively suppressed. It is an object of the present invention to provide a molded body, a manufacturing method thereof, and a heating facility.
- An inorganic fiber molded body according to an embodiment of the present invention for solving the above-mentioned problems is characterized in that it includes biosoluble inorganic fibers partially crystallized and an inorganic binder.
- ADVANTAGE OF THE INVENTION According to this invention, the inorganic fibrous molded object by which the deformation
- the said inorganic fiber molded object WHEREIN The said biosoluble inorganic fiber is good also as including the crystal
- the biosoluble inorganic fiber may have an SiO 2 content of 66 to 82% by mass.
- the biosoluble inorganic fiber may have a CaO content of 10 to 34% by mass.
- MgO content of the said biosoluble inorganic fiber is good also as being 1 mass% or less.
- a method for producing an inorganic fibrous molded body includes a first step of heat-treating amorphous biosoluble inorganic fibers, and the heat treatment. And a second step of forming an inorganic fibrous formed body containing the biosoluble inorganic fiber and an inorganic binder.
- the amorphous biosoluble inorganic fiber may be heat-treated at a temperature equal to or higher than the crystallization temperature to obtain the biosoluble inorganic fiber partially crystallized.
- the biosoluble inorganic fiber subjected to the heat treatment may contain wollastonite, diopside or enstatite crystals.
- the biosoluble inorganic fiber may have an SiO 2 content of 66 to 82% by mass.
- the biosoluble inorganic fiber may have a CaO content of 10 to 34% by mass.
- MgO content of the said biosoluble inorganic fiber is good also as being 1 mass% or less.
- a heating facility for solving the above-described problems is characterized by including any one of the inorganic fibrous molded bodies.
- ADVANTAGE OF THE INVENTION According to this invention, the heating equipment containing the inorganic fiber molded object by which the deformation
- an inorganic fibrous molded body in which deformation due to heating during use is effectively suppressed, a manufacturing method thereof, and a heating facility.
- the method includes a first step of heat-treating amorphous biosoluble inorganic fibers (hereinafter referred to as “heat treatment step”), the biosoluble inorganic fibers subjected to the heat treatment, and inorganic And a second step (hereinafter referred to as “molding step”) of molding an inorganic fibrous molded body containing a binder.
- an amorphous biosoluble inorganic fiber is prepared.
- the biosoluble inorganic fiber is an inorganic fiber and has biosolubility (for example, a property of being decomposed in the living body even when inhaled into the lungs of the living body).
- the biologically soluble inorganic fiber is at least partially amorphous, and it is confirmed by powder X-ray diffraction (XRD) measurement that it is amorphous.
- the biosoluble inorganic fiber is, for example, an inorganic fiber having a physiological saline dissolution rate at 40 ° C. of 1% or more.
- the physiological saline dissolution rate is measured, for example, as follows. That is, first, 1 g of a sample prepared by pulverizing inorganic fibers to 200 mesh or less and 150 mL of physiological saline are placed in an Erlenmeyer flask (volume: 300 mL) and placed in an incubator at 40 ° C. Next, a horizontal vibration of 120 revolutions per minute is continuously applied to the Erlenmeyer flask for 50 hours. Thereafter, the concentration (mg / L) of each element contained in the filtrate obtained by filtration is measured with an ICP emission analyzer.
- the physiological saline dissolution rate (%) is calculated. That is, for example, when the measurement element is silicon (Si), magnesium (Mg), calcium (Ca), and aluminum (Al), the physiological saline dissolution rate C (%) is calculated by the following equation.
- C (%) [filtrate amount (L) ⁇ (a1 + a2 + a3 + a4) ⁇ 100] / [mass of inorganic fiber before dissolution (mg) ⁇ (b1 + b2 + b3 + b4) / 100].
- a1, a2, a3 and a4 are the measured concentrations of silicon, magnesium, calcium and aluminum (mg / L), respectively, and b1, b2, b3 and b4 are respectively in the inorganic fibers before dissolution. It is content (mass%) of silicon, magnesium, calcium, and aluminum.
- the biosoluble inorganic fiber has, for example, an inorganic fiber having a dissolution rate constant of 150 ng / cm 2 ⁇ h or more, preferably 150 to 1500 ng / cm 2 ⁇ h, more preferably 200 to 1500 ng / cm 2 ⁇ h. It is.
- the biosoluble inorganic fiber is, for example, an inorganic fiber having an estimated half-life of 40 days or less, preferably 10 to 40 days, more preferably 10 to 30 days.
- the SiO 2 content of the biosoluble inorganic fiber may be, for example, 50 to 82% by mass.
- the SiO 2 content is preferably 63 to 81% by mass, more preferably 66 to 80% by mass, and even more preferably 71 to 76% by mass. That is, the biosoluble inorganic fiber is, for example, an inorganic fiber having a SiO 2 content of 66 to 82% by mass and a total of CaO content and MgO content of 18 to 34% by mass.
- the total of the CaO content and the MgO content is preferably 19 to 34% by mass, and more preferably 20 to 34% by mass.
- the total range of these CaO content and MgO content can be arbitrarily combined with the above-described range of SiO 2 content.
- SiO 2 content of bio-soluble inorganic fibers is in the range described above, the bio-soluble inorganic fibers, in addition to bio-solubility, and thus also has excellent heat resistance.
- the CaO content of the biosoluble inorganic fiber may be, for example, 10 to 34% by mass. That is, the biosoluble inorganic fiber has an SiO 2 content of 66 to 82% by mass and an CaO content of 10 to 34% by mass (hereinafter referred to as “SiO 2 / CaO fiber”). )).
- the CaO content is preferably 12 to 32% by mass, and more preferably 14 to 30% by mass.
- the MgO content of the biosoluble inorganic fiber may be, for example, 1% by mass or less (that is, 0 to 1% by mass). MgO is usually more than 0% by mass. That is, the biosoluble inorganic fiber has, for example, a SiO 2 / CaO fiber having a SiO 2 content of 66 to 82% by mass, a CaO content of 10 to 34% by mass, and a MgO content of 1% by mass or less. It is good also as being.
- the MgO content is preferably 0.9% by mass or less, and more preferably 0.8% by mass or less.
- the MgO content of the biosoluble inorganic fiber may be more than 1% by mass and 20% by mass or less. That is, biosoluble inorganic fibers, for example, a SiO 2 content of 66 to 82 wt%, MgO content of 1 wt percent, and 20 mass% of inorganic fibers (hereinafter, "SiO 2 / MgO fibers It may also be “.”
- the MgO content is preferably 2 to 19% by mass, and more preferably 3 to 19% by mass.
- the biosoluble inorganic fiber may have, for example, a total content of SiO 2 content, MgO content and CaO content of 97% by mass or more (that is, 97 to 100% by mass).
- the total of the SiO 2 content, the MgO content and the CaO content is preferably 97.5% by mass or more, and more preferably 98% by mass or more.
- the total range of these SiO 2 content, MgO content and CaO content is the range of the SiO 2 content described above, the total range of the CaO content and MgO content described above, the range of the CaO content described above. , And can be arbitrarily combined with the above-described MgO content range.
- the biosoluble inorganic fiber may further contain other components in addition to SiO 2 and an alkaline earth metal oxide (for example, at least one of MgO and CaO). That is, biosoluble inorganic fibers include, for example, alumina (Al 2 O 3 ), titania (TiO 2 ) and zirconia (ZrO 2 ), iron oxide (Fe 2 O 3 ), manganese oxide (MnO), potassium oxide (K One or more selected from the group consisting of 2 O) may be further contained, or may not be contained.
- the bio-soluble inorganic fibers containing Al 2 O 3, Al 2 O 3 content for example, 5 wt% or less, and 3.4 wt% or less, or 3.0 wt% or less. Moreover, it can be 1.1 weight% or more or 2.0 weight% or more. The content is preferably 0 to 3% by mass, more preferably 1 to 3% by mass. If Al 2 O 3 is contained within this range, the strength becomes high.
- the biosoluble inorganic fiber has, for example, a total content of SiO 2 content, MgO content, CaO content and Al 2 O 3 content of 98% by mass or more (that is, 98 to 100% by mass) or 99% by mass. % Or more (that is, 99 to 100% by mass).
- biosoluble inorganic fibers having the following composition can be exemplified. 50 to 82% by weight of SiO 2 , Al 2 O 3 , ZrO 2 and TiO 2 Total of CaO and MgO 18-50% by weight
- biosoluble inorganic fiber of the following compositions can be illustrated.
- SiO 2 50 to 82% by weight
- SiO 2 / MgO fibers SiO 2 66-82% by weight CaO 1-9% by weight (for example, it can be 2-8% by weight) MgO 10-30% by weight (for example, it can be 15-20% by weight) Al 2 O 3 3 wt% or less Other oxides Less than 2 wt%
- SiO 2 / CaO fibers Fibers having the following composition are excellent in biosolubility and fire resistance after heating.
- SiO 2 66-82 wt% (for example, it can be 68-80 wt%, 70-80 wt%, 71-80 wt% or 71.25-76 wt%)
- CaO 10-34% by weight (for example, it can be 18-30% by weight, 20-27% by weight or 21-26% by weight)
- MgO 3 wt% or less eg, 1 wt% or less
- Al 2 O 3 5% by weight or less eg, 3.4% by weight or less or 3% by weight or less, and 1.1% by weight or more or 2.0% by weight or more
- the biologically soluble inorganic fiber includes, as other components, alkali metal oxides (K 2 O, Na 2 O, etc.), Fe 2 O 3 , ZrO 2 , TiO 2 , P 2 O 5 , B 2 O 3 , R 2 O 3 (R is selected from Sc, La, Ce, Pr, Nd, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, Y, or a mixture thereof) The above may or may not be included. Other oxides may be 0.2 wt% or less or 0.1 wt% or less, respectively.
- Alkali metal oxide may or may not be contained, and may be 0.2% by weight or less, 0.15% by weight or less, or 0.1% by weight or less. In the alkali metal oxide, each oxide may be 0.2% by weight or less, or 0.1% by weight or less. Moreover, it is good also considering the sum total of an alkali metal oxide as 0.2 weight% or less. Alkali metal oxide may be contained more than 0.01% by weight, 0.05% by weight or more, or 0.08% by weight or more.
- K 2 O may or may not be contained, and may be 0.2% by weight or less, 0.15% by weight or less, or 0.1% by weight or less. K 2 O may be contained more than 0.01% by weight, 0.05% by weight or more, or 0.08% by weight or more. Na 2 O may or may not be contained, and may be 0.2% by weight or less, 0.15% by weight or less, or 0.1% by weight or less. Na 2 O may be contained more than 0.01% by weight, 0.05% by weight or more, or 0.08% by weight or more. Further, the total content of Na and K may be more than 500 ppm.
- the average fiber diameter of the biosoluble inorganic fiber is not particularly limited as long as the inorganic fiber molded body is suitably produced, and is, for example, 1 to 10 ⁇ m, preferably 2 to 6 ⁇ m.
- the average fiber diameter is less than 1 ⁇ m, the water resistance tends to decrease, so the strength of the produced inorganic fibrous molded body tends to be low.
- the average fiber diameter exceeds 10 ⁇ m, the density of the produced inorganic fibrous molded body is too low, and the strength of the inorganic fibrous molded body tends to be low.
- the average fiber length of the biosoluble inorganic fiber is not particularly limited as long as the inorganic fiber molded body is suitably produced, and is, for example, 1 to 200 mm, preferably 1 to 100 mm. When the average fiber length is within the above range, it becomes easy to produce an inorganic fibrous molded body having an appropriate density.
- the amorphous biosoluble inorganic fiber prepared as described above is subjected to heat treatment to obtain the biosoluble inorganic fiber subjected to the heat treatment.
- the method including the heat treatment step is a method in which an amorphous biosoluble inorganic fiber (hereinafter referred to as “untreated fiber”) is subjected to a heat treatment, and the biosoluble inorganic fiber subjected to the heat treatment. (Hereinafter, referred to as “heat-treated fiber”).
- the manufactured heat-treated fiber is used as a raw material for an inorganic fibrous shaped body as described later.
- the conditions (for example, temperature and time) of the heat treatment are such that when the inorganic fibrous molded body containing the heat treated fibers is heated, the deformation (warp, shrinkage, etc.) of the inorganic fibrous molded body If it determines so that it may reduce compared with that of the inorganic fiber molding to contain, it will not be restricted in particular.
- the heat treatment is performed, for example, under the condition that the amount of warping when the inorganic fiber molded body including the heat-treated fiber is heated is reduced as compared with that of the inorganic fiber molded body including the untreated fiber.
- the heat treatment is performed under the condition that, for example, the heating linear shrinkage rate at 300 to 1300 ° C. of the inorganic fiber molded body containing the heat treated fiber is reduced as compared with that of the inorganic fiber molded body containing the untreated fiber.
- the heating linear shrinkage rate is, for example, the length of the inorganic fiber molded body before and after the heating measured by heating the inorganic fiber molded body at a constant temperature in the range of 300 to 1300 ° C. for 24 hours in an electric furnace.
- the heating linear shrinkage rate (%) ⁇ (XY) / X ⁇ ⁇ 100.
- X indicates the length (mm) of the inorganic fibrous molded body before heating
- Y indicates the length (mm) of the inorganic fibrous molded body after heating.
- heating temperature in the heat treatment of the SiO 2 / MgO fiber is, for example, 600 to 1300 ° C., preferably 800 to 1300 ° C., more preferably 850 to 1000 ° C. is there.
- heating temperature in the heat treatment of the SiO 2 / CaO fiber is, for example, 820 to 1300 ° C., preferably 830 to 1300 ° C., more preferably 840 to 1000 ° C. Yes, most preferably 850-1000 ° C.
- the heat treatment temperature may be a temperature equal to or higher than the crystallization temperature of untreated fibers, for example. That is, in this case, in the heat treatment step, the untreated fiber is subjected to a heat treatment at a temperature equal to or higher than the crystallization temperature to obtain a heat-treated fiber partially crystallized.
- the crystallization temperature of the untreated fiber is measured by, for example, TG-DTA (thermogravimetric-differential heat measurement).
- a heat treatment temperature not lower than the crystallization temperature cannot be generally determined. For example, 600 to 1300 ° C., 600 to 1100 ° C., or 800 to 1000 ° C.
- the heat-treated fiber includes, for example, crystals that are not included in the untreated fiber used for the production thereof.
- the crystals contained in the heat-treated fiber can be analyzed by, for example, powder X-ray diffraction. That is, the heat treatment is performed so that, for example, a heat-treated fiber in which crystals that are not detected in the untreated fiber in powder X-ray diffraction are detected can be obtained by performing heat treatment on the untreated fiber.
- the heat-treated fiber When the heat-treated fiber is the above-described SiO 2 / CaO fiber, the heat-treated fiber partially crystallized includes, for example, wollastonite crystals. In this case, the heat-treated fiber may further contain other crystals. That is, the heat-treated fiber includes, for example, one type or two or more types of crystals selected from the group consisting of wollastonite, cristobalite, and tridymite.
- the heat-treated fiber When the heat-treated fiber is the above-described SiO 2 / MgO fiber, the heat-treated fiber partially crystallized includes, for example, enstatite crystals. In this case, the heat-treated fiber may further contain other crystals. That is, the heat-treated fiber includes, for example, one or more crystals selected from the group consisting of enstatite, diopsite, cristobalite, and tridymite.
- Heat-treated fibers are other biosoluble inorganic fibers (for example, SiO 2 content is 35 to 45% by mass, Al 2 O 3 content is 10 to 20% by mass, MgO content is 4 to 8% by mass, and CaO is contained. Heat-treated partly crystallized when the amount is 20 to 40% by mass, Fe 2 O 3 content is 0 to 3% by mass, and MnO content is 0 to 1% by mass.
- the fiber may contain, for example, one or more crystals selected from the group consisting of wollastonite, annosite, diopsite, acarmanite, and augite.
- heat processing temperature has the effect that the deformation
- the heating time in the heat treatment (hereinafter referred to as “heat treatment time”) is also not particularly limited as long as the above-described effects of the heat treatment can be obtained. That is, the heat treatment time is, for example, 1 minute to 48 hours, preferably 3 minutes to 24 hours.
- the heat treatment time is, for example, 3 minutes to 8 hours, preferably 5 minutes to 3 hours.
- the biosoluble inorganic fiber can change its biosolubility by being subjected to heat treatment. That is, the biologically soluble inorganic fiber is likely to be degraded in its biological solubility when subjected to heat treatment.
- the biosolubility after heating is lower than that before heating. Often to do.
- the inventors of the present invention can obtain heat-treated fibers having better biosolubility than before heat treatment by using the above-mentioned SiO 2 / CaO fibers as bio-soluble inorganic fibers. I found this on my own.
- a SiO 2 content of 66 to 82 mass%, CaO content of the 10 to 34% by weight of SiO 2 / CaO fibers by heat treatment at the crystallization temperature or higher obtained
- the biosolubility of the heat-treated fiber is significantly increased as compared with that before the heat treatment.
- the heat-treated fiber since the heat-treated fiber has a large SiO 2 content, it has excellent heat resistance in addition to excellent biosolubility.
- the chemical reaction between the heat-treated fiber and Al 2 O 3 is a phenomenon that occurs depending on the ratio of the components of SiO 2 / CaO / Al 2 O 3 , and the chemical reaction (melting) also occurs from the solid state diagram of the oxide. You can see what happens.
- This chemical reaction involving melting can be suppressed, for example, by increasing the SiO 2 content of the biosoluble inorganic fiber.
- the chemical reaction between the SiO 2 / CaO fiber and Al 2 O 3 constituting the industrial furnace wall is effectively suppressed.
- SiO 2 / CaO fibers having a SiO 2 content of 66 to 82% by mass, a CaO content of 10 to 34% by mass, and an MgO content of 1% by mass or less are also preferably used.
- the MgO content is small, deformation during heating of the inorganic fibrous formed body including the heat-treated fibers can be effectively reduced.
- the SiO 2 / MgO fiber since the SiO 2 / MgO fiber has a relatively high MgO content, crystals containing Si and Mg as main components (for example, enstatite) preferentially by heating at a temperature higher than the crystallization temperature. Formed.
- the above-mentioned SiO 2 / CaO fiber has a high CaO content and a low MgO content. Therefore, crystals containing Si and Ca as main components by heating at a temperature equal to or higher than the crystallization temperature (for example, waving) Lastite) is preferentially formed.
- the specific gravity of a crystal containing Si and Ca as main components is smaller than that of a crystal containing Si and Mg as main components. Then, the smaller the specific gravity of the crystals contained in the heat-treated fiber, the smaller the deformation amount of the heat-treated fiber (for example, the heat shrinkage).
- the inorganic fiber molded body contains the SiO 2 / CaO fiber having a small MgO content as the heat-treated fiber, deformation (warping, heating line shrinkage, etc.) of the inorganic fiber molded body is effective. Is suppressed.
- the biosolubility after the heat treatment is within a desired range (for example, the physiological saline dissolution rate at 40 ° C. is 1%) If it is above, there is no particular problem.
- an inorganic fibrous molded body containing the heat-treated fiber prepared in the above-described heat treatment step and an inorganic binder is molded. That is, first, a raw material containing heat-treated fibers and an inorganic binder is prepared.
- the inorganic binder is not particularly limited as long as it binds the heat-treated fiber.
- anionic colloidal silica colloidal silica such as cationic colloidal silica, fumed silica, zirconia sol, titania sol, alumina sol, bentonite,
- colloidal silica such as cationic colloidal silica, fumed silica, zirconia sol, titania sol, alumina sol, bentonite
- One or more selected from the group consisting of kaolins can be used.
- the content of the heat-treated fiber is, for example, 70 to 95.5% by mass, and the content of the inorganic binder is, for example, 0.5 to 30% by mass.
- the raw material may further contain other components in addition to the heat-treated fiber and the inorganic binder. That is, the raw material may further contain, for example, an organic binder.
- the organic binder is not particularly limited as long as it binds the heat-treated fiber, and is, for example, one or more selected from the group consisting of starch, acrylic resin, and polyacrylamide.
- the raw material may further contain, for example, a refractory inorganic powder.
- the refractory inorganic powder is, for example, ceramic powder such as silica, alumina, titania, zirconia, silicon nitride, silicon carbide, and / or carbon powder such as carbon black.
- the raw material is prepared by mixing a heat-treated fiber, an inorganic binder, and other components as necessary with a solvent.
- the solvent is not particularly limited as long as the heat-treated fiber and the inorganic binder are mixed and dispersed.
- water for example, distilled water, ion exchange water, tap water, ground water, industrial water
- a polar organic solvent For example, monovalent alcohols such as ethanol and propanol, divalent alcohols such as ethylene glycol, and preferably water.
- the raw material of the inorganic fibrous molded body thus prepared is an amorphous composition. That is, the raw material is a plastic composition, for example, a fluid composition (so-called slurry or the like).
- a fixed inorganic fiber molded body is manufactured from the amorphous raw material thus prepared. That is, for example, by putting the raw material in a mold having a predetermined shape, removing the solvent from the raw material in the mold, and further drying the raw material, an inorganic fibrous molded body having a shape corresponding to the shape of the mold is obtained. obtain.
- the raw material is poured into a mold having a net at the bottom, and then the solvent is removed by sucking the solvent contained in the raw material through the net, and then the raw material Is dried by heating in a dryer.
- the heating temperature for drying is, for example, 60 to 150 ° C., preferably 80 to 120 ° C.
- an inorganic fiber molded body can be obtained by a method in which an amorphous composition having low fluidity as compared with a slurry is prepared as a raw material, the raw material is placed in a mold having a predetermined shape, and dried and fired in the mold. Can be obtained.
- the inorganic fibrous molded body (hereinafter referred to as “the molded body”) according to the present embodiment is preferably manufactured by such a method. That is, this molded object is an inorganic fibrous molded object containing the heat-processing fiber mentioned above and an inorganic binder.
- the molded body is an inorganic fibrous molded body containing, for example, a biosoluble inorganic fiber (heat-treated fiber) partially crystallized and an inorganic binder.
- the SiO 2 content of the heat-treated fiber contained in the molded body is, for example, 66 to 82% by mass. In this case, the formed body has excellent heat resistance due to the relatively large SiO 2 content of the heat-treated fiber.
- the CaO content of the heat-treated fiber contained in the molded body is, for example, 10 to 34% by mass. That is, this heat-treated fiber is, for example, a SiO 2 / CaO fiber having a SiO 2 content of 66 to 82% by mass and a CaO content of 10 to 34% by mass.
- the partially crystallized SiO 2 / CaO fiber includes, for example, wollastonite crystals.
- the SiO 2 / CaO fiber may contain, for example, one or more crystals selected from the group consisting of wollastonite, cristobalite, and tridymite.
- these SiO 2 / CaO fibers have a very excellent biosolubility increased by the heat treatment because the heat treatment is performed prior to the molding of the inorganic fiber molded body. is doing.
- the SiO 2 content of the SiO 2 / CaO fiber is large, as described above, even when the molded body is used by being heated on an industrial furnace wall containing Al 2 O 3 , the SiO 2 The chemical reaction between the 2 / CaO fiber and the Al 2 O 3 is effectively suppressed, and deformation of the molded body is also effectively suppressed.
- the MgO content of the heat-treated fiber contained in the molded body is, for example, 1% by mass or less. That is, this heat-treated fiber is, for example, SiO 2 / CaO fiber having a SiO 2 content of 66 to 82% by mass, a CaO content of 10 to 34% by mass, and a MgO content of 1% by mass or less. is there. In this case, since the MgO content of the heat-treated fiber is small, as described above, deformation (warping, heating line shrinkage, etc.) during heating of the molded body is effectively suppressed.
- the contents of the heat-treated fiber and the inorganic binder in the molded body are not particularly limited, and are appropriately determined depending on the use and required characteristics.
- the content of the heat-treated fiber is 70 to 95.5% by mass. More specifically, for example, in the molded body, the content of the heat-treated fiber is 70 to 95.5% by mass, and the content of the inorganic binder is 0.5 to 30% by mass.
- the density of the molded body is not particularly limited, and is appropriately determined depending on the application and required characteristics.
- the density of the molded body is 0.1 to 1.0 kg / cm 3 , preferably 0.15 to 0.6 kg / cm 3 .
- the shape of the molded body is not particularly limited, and is appropriately determined depending on its use and required characteristics.
- the shape of the molded body may be a plate shape (polygonal plate shape such as a square (board), disc shape, etc.), a cylindrical shape (polygonal shape such as a square shape, a cylindrical shape, etc.), a weight shape ( A polygonal pyramid such as a square pyramid, a cone, etc.
- the present molded body contains heat-treated fibers as biosoluble fibers, so that deformation when used in a heated state is effectively suppressed. That is, for example, preferably, the heating linear shrinkage rate when the molded body is heated at 1100 ° C. for 24 hours is 3.0% or less, more specifically 0.0 to 3.0%. .
- the amount of warping when the molded body is heated at 400 ° C. for 24 hours is 1.3 mm or less, and more specifically, 1.0 mm or less.
- the measurement method is as shown in the examples.
- This molded body is applied to various uses. That is, this molded object is used as a heat insulating material, a sealing material, and a packing material in heating equipment, such as a heat treatment apparatus, an industrial furnace, and an incinerator, for example. Moreover, this molded object is used also as a sound-absorbing material, a filter material, a catalyst support
- the biosolubility of the biosoluble inorganic fiber before and after the heat treatment was evaluated.
- the SiO 2 content is 73 mass%
- the CaO content is 21 to 26 mass%
- the MgO content is 1 mass% or less
- Al 2 O 3 is 1 to 3 mass%.
- Amorphous SiO 2 / CaO fiber (hereinafter referred to as “fiber A”) was prepared.
- the crystallization temperature of fiber A was 895 ° C.
- the heat treatment temperature was 800 ° C., 1000 ° C., or 1100 ° C.
- the heat treatment time was 24 hours.
- the biosolubility of the fiber A before the heat treatment and after the heat treatment at each temperature was evaluated. That is, the dissolution rate constant (ng / cm 2 ⁇ h) and the assumed half-life (days) were evaluated as indicators of biosolubility.
- the dissolution rate constant of the fiber A was measured as follows. That is, first, the fiber A was passed through a 45 ⁇ m sieve, and the fiber A from which the shot was removed was placed on the filter paper. Subsequently, the physiological saline was dripped on the fiber A with the micropump, and the filtrate which passed the fiber A and the filter paper was stored in the tank. The filtrate collected after the lapse of a predetermined time was recovered. And the elution component in the collect
- the estimated half-life was measured with reference to a test (German standard) on whether or not the exemption condition according to NoteQ of EU Directive 97/69 / EC was satisfied. That is, in this test, when a fiber longer than 20 ⁇ m has a load half-life of less than 40 days in a short-term in vivo retention test by injection into the trachea of an animal, the fiber satisfies the exemption condition. . Therefore, when this test was performed using the fiber A before the heat treatment, the load half-life of the fiber A was 19 days. And the assumed half life of the fiber A after the heat treatment is obtained by dividing the dissolution rate constant of the fiber A before the heat treatment by the dissolution rate constant of the fiber A after the heat treatment. Calculated by multiplying by the load half-life.
- the SiO 2 content is 76 mass%
- the CaO content is 2 to 6 mass%
- the MgO content is 16 to 20 mass%
- Al 2 O 3 is 1 to 2 mass.
- % Amorphous SiO 2 / MgO fiber hereinafter referred to as “fiber B”.
- the crystallization temperature of the fiber B was 857 ° C.
- the fiber B was heat-treated.
- the heat treatment temperature was 700 ° C, 800 ° C, 850 ° C, 900 ° C or 1000 ° C.
- the heat treatment time was 24 hours for 700 ° C., 800 ° C. and 1000 ° C., and 50 hours for 850 ° C. and 900 ° C.
- FIG. 1 shows the results of evaluating the biosolubility of fiber A.
- FIG. 2 the result of having evaluated the biosolubility of the fiber B is shown.
- both the fiber A and the fiber B before the heat treatment (“untreated” in the figure) had excellent biosolubility.
- the biological solubility of fiber A was increased by heat treatment.
- the heat treatment by performing the heat treatment at a temperature exceeding the crystallization temperature of the fiber A, the biosolubility of the fiber A significantly increased.
- the fiber A after the heat treatment had extremely excellent biosolubility.
- the biosolubility of fiber B was reduced by heat treatment.
- the heat treatment is performed at a temperature near or higher than the crystallization temperature of the fiber B, the biosolubility of the fiber B is significantly reduced.
- the fiber A was subjected to heat treatment, and the generation of crystals in the fiber A was analyzed.
- the fiber A was heat-treated.
- the heat treatment temperature was 600 ° C, 700 ° C, 800 ° C, 900 ° C, 1000 ° C, 1100 ° C, 1200 ° C, 1300 ° C, or 1400 ° C.
- the heat treatment time was 24 hours.
- the fiber A after the heat treatment was analyzed by powder X-ray diffraction (XRD).
- FIG. 3 the XRD measurement result of the fiber A obtained by heat processing in each heat processing temperature is shown.
- ⁇ indicates the peak of wollastonite (CaSiO 3 ) crystal
- ⁇ indicates the peak of pseudowollastonite crystal
- ⁇ indicates the peak of cristobalite crystal.
- X marks indicate the peaks of tridymite crystals.
- wollastonite crystals were produced by heat treatment at 900 ° C. or higher. Moreover, the crystal
- the fiber B was subjected to a heat treatment, and XRD measurement was performed.
- enstatite crystals were produced by heat treatment at 900 ° C. or higher.
- crystallization of cristobalite was produced
- crystallization was produced
- An inorganic fibrous molded body containing the fiber A was produced, and its heating line shrinkage rate was evaluated. First, a fiber A that was not heat-treated, a fiber A that was heat-treated at 850 ° C. for 10 minutes, and a fiber A that was heat-treated at 900 ° C. for 10 minutes were prepared.
- any fiber A 5 parts by weight of colloidal silica (ST30, manufactured by Nissan Chemical Industries, Ltd.) as an inorganic binder, and starch (Petrosize J, manufactured by Nissho Chemical Co., Ltd.) as an organic binder was mixed with 4.5 parts by weight and aggregating material (Polystron 117, manufactured by Arakawa Chemical Co., Ltd.) with 0.5 parts by weight, and 5000 parts by weight of water to prepare a raw material slurry.
- colloidal silica ST30, manufactured by Nissan Chemical Industries, Ltd.
- starch Petrosize J, manufactured by Nissho Chemical Co., Ltd.
- aggregating material Polystron 117, manufactured by Arakawa Chemical Co., Ltd.
- this raw material slurry was poured into a mold having a net installed at the bottom. And the water contained in the raw material slurry was sucked and removed through the net of the mold. Thereafter, the dehydrated raw material was heated and dried in a dryer.
- a rectangular plate-like inorganic fibrous board having a size of 600 mm ⁇ 900 mm and a thickness of 50 mm was formed.
- the content of fiber A was 91.0% by mass, and the content of colloidal silica was 4.5% by mass.
- heating linear shrinkage rate (%) ⁇ (XY) / X ⁇ ⁇ 100.
- X is the length (mm) of the inorganic fiber board before heating
- Y is the length (mm) of the inorganic fiber board after heating.
- FIG. 4 shows the results of measuring the heating linear shrinkage rate.
- the heating line shrinkage of the inorganic fiber board (“850 ° C. treated fiber A” and “900 ° C. treated fiber A” in the figure) manufactured using the heat-treated fiber A.
- the rate was reduced compared to the inorganic fibrous board (“untreated fiber A” in the figure) manufactured using the fiber A that was not subjected to the heat treatment.
- the heating linear shrinkage of the inorganic fiber board (“900 ° C. treated fiber A” in the figure) containing the fiber A that has been heat-treated at a heat treatment temperature higher than the crystallization temperature is determined by the heating temperature at the time of measurement. It was significantly reduced in the entire range of 700 to 1300 ° C.
- An inorganic fiber molded body containing fiber A or fiber B was produced, and the amount of warpage when the inorganic fiber molded body was heated was evaluated. First, the fiber A and the fiber B were subjected to heat treatment.
- fiber A not subjected to heat treatment fiber A not subjected to heat treatment, fiber A subjected to heat treatment at 800 ° C. for 5 minutes, fiber A subjected to heat treatment at 850 ° C. for 5 minutes, heat treatment at 850 ° C. for 10 minutes , Fiber A subjected to heat treatment at 900 ° C. for 5 minutes, and fiber A subjected to heat treatment at 950 ° C. for 10 minutes were prepared.
- a fiber B that was not heat-treated, a fiber B that was heat-treated at 800 ° C. for 5 minutes, and a fiber B that was heat-treated at 900 ° C. for 10 minutes were prepared.
- an inorganic fibrous board containing fiber A or fiber B was manufactured. That is, 100 parts by weight of any fiber A, 5 parts by weight of colloidal silica (ST30, manufactured by Nissan Chemical Industries, Ltd.) as an inorganic binder, and starch (Petrosize J, manufactured by Nissho Chemical Co., Ltd.) as an organic binder. was mixed with 4.5 parts by weight and aggregating material (Polystron 117, manufactured by Arakawa Chemical Co., Ltd.) with 0.5 parts by weight, and 5000 parts by weight of water to prepare a raw material slurry. And the inorganic fiber board containing the fiber A was manufactured similarly to the above-mentioned Example 3.
- any fiber B 100 parts by weight of any fiber B, 5 parts by weight of colloidal silica (ST30, manufactured by Nissan Chemical Industries, Ltd.) as an inorganic binder, and starch (Petrosize J, manufactured by Nissho Chemical Co., Ltd.) as an organic binder.
- colloidal silica ST30, manufactured by Nissan Chemical Industries, Ltd.
- starch Petrosize J, manufactured by Nissho Chemical Co., Ltd.
- aggregating material Polystron 117, manufactured by Arakawa Chemical Co., Ltd.
- the inorganic fiber board containing the fiber B was manufactured similarly to the above-mentioned Example 3.
- the amount of warpage of the inorganic fiber board was measured.
- the inorganic fibrous board manufactured as described above was cut into a size of 860 mm ⁇ 450 mm and a thickness of 50 mm to obtain a test piece.
- one surface (surface of 860 mm ⁇ 450 mm) arranged so as to face the inside of the electric furnace at the time of heating described later is determined, and the one end from the longitudinal end of the determined surface to the other end
- a straight ruler was handed over to measure the distance (the amount of deformation before the heat treatment) between the straight ruler and the portion of the surface farthest from the straight ruler (the most recessed portion).
- the inorganic fiber board was placed on the inner wall of the electric furnace so that the surface on which the deformation amount before the heat treatment was measured as described above faced the inside of the electric furnace. Furthermore, in this electric furnace, the inorganic fiber board was heated at 300 ° C., 400 ° C., 500 ° C., 600 ° C., 700 ° C., 800 ° C. or 900 ° C. for 24 hours by a panel heater arranged in the electric furnace. . After heating, the amount of deformation of the inorganic fibrous board was measured in the same manner as before heating. And the value which reduced the deformation amount before a heating from the deformation amount after a heating was obtained as curvature amount (mm).
- FIG. 5 shows the results of measuring the warpage (mm) of the inorganic fibrous board containing the fiber A.
- FIG. 6 the result of having measured the curvature amount (mm) of the inorganic fibrous board containing the fiber B is shown.
- the fiber A subjected to the heat treatment at 850 ° C. or higher is compared with the inorganic fiber board (“untreated fiber A” in the figure) containing the fiber A not subjected to the heat treatment.
- the included inorganic fiber board had a small maximum warpage amount between 300 ° C. and 900 ° C., and the change in the warp amount was also reduced.
- the surface facing the furnace becomes high temperature by heating, and the opposite surface becomes lower temperature. Accordingly, the heating up to 800 ° C. causes warping due to the temperature difference in the board, but at 900 ° C., the opposite surface is also heated, so that the warping is returned on many boards. If such a change in the amount of warping is large, it may cause cracks.
- the fiber B subjected to the heat treatment at 800 ° C. or higher is compared with the inorganic fiber board (“untreated fiber B” in the figure) containing the fiber B not subjected to the heat treatment.
- the amount of warpage of the inorganic fiber board contained was effectively reduced.
Abstract
Description
SiO2とAl2O3とZrO2とTiO2との合計 50~82重量%
CaOとMgOとの合計 18~50重量%
SiO2 50~82重量%
CaOとMgOとの合計 10~43重量%
SiO2 66~82重量%
CaO 1~9重量%(例えば、2~8重量%とできる)
MgO 10~30重量%(例えば、15~20重量%とできる)
Al2O3 3重量%以下
他の酸化物 2重量%未満
SiO2 66~82重量%(例えば、68~80重量%、70~80重量%、71~80重量%又は71.25~76重量%とできる)
CaO 10~34重量%(例えば、18~30重量%、20~27重量%又は21~26重量%とできる)
MgO 3重量%以下(例えば、1重量%以下とできる)
Al2O3 5重量%以下(例えば3.4重量%以下又は3重量%以下とできる。また、1.1重量%以上又は2.0重量%以上とできる)
他の酸化物 2重量%未満
Na2Oは含まれても含まれなくてよく、0.2重量%以下、0.15重量%以下又は0.1重量%以下とすることができる。Na2Oは0.01重量%超、0.05重量%以上又は0.08重量%以上含まれていてもよい。
また、NaとKの合計の含有量を500ppm超としてもよい。
この明細書に記載の文献の内容を全てここに援用する。
Claims (9)
- 一部が結晶化した生体溶解性無機繊維と、無機バインダーとを含み、
前記生体溶解性無機繊維が、以下の組成を有するSiO2/MgO繊維又はSiO2/CaO繊維である
ことを特徴とする無機繊維質成形体。
[SiO2/MgO繊維]
SiO2 66~82重量%
CaO 1~9重量%
MgO 10~30重量%
Al2O3 3重量%以下
[SiO2/CaO繊維]
SiO2 66~82重量%
CaO 10~34重量%
MgO 3重量%以下
Al2O3 5重量%以下 - 前記生体溶解性無機繊維は、ワラストナイト、ディオプサイド又はエンスタタイトの結晶を含む
ことを特徴とする請求項1に記載された無機繊維質成形体。 - 前記成形体がボードであり、400℃で24時間加熱したときの反り量が1.3mm以下である
ことを特徴とする請求項1又は2に記載された無機繊維質成形体。 - 以下の組成を有するSiO2/MgO繊維である、非晶質の生体溶解性無機繊維に600~1300℃の加熱処理を施す第一工程と、
前記加熱処理が施された前記生体溶解性無機繊維と、無機バインダーと、を含む無機繊維質成形体を成形する第二工程と、
を含む
ことを特徴とする無機繊維質成形体の製造方法。
[SiO2/MgO繊維]
SiO2 66~82重量%
CaO 1~9重量%
MgO 10~30重量%
Al2O3 3重量%以下 - 以下の組成を有するSiO2/CaO繊維である、非晶質の生体溶解性無機繊維に820~1300℃の加熱処理を施す第一工程と、
前記加熱処理が施された前記生体溶解性無機繊維と、無機バインダーと、を含む無機繊維質成形体を成形する第二工程と、
を含む
ことを特徴とする無機繊維質成形体の製造方法。
[SiO2/CaO繊維]
SiO2 66~82重量%
CaO 10~34重量%
MgO 3重量%以下
Al2O3 5重量%以下 - 前記第一工程において、前記非晶質の生体溶解性無機繊維に結晶化温度以上の温度で加熱処理を施し、一部が結晶化した前記生体溶解性無機繊維を得る
ことを特徴とする請求項4又は5に記載された無機繊維質成形体の製造方法。 - 前記加熱処理が施された前記生体溶解性無機繊維は、ワラストナイト、ディオプサイド又はエンスタタイトの結晶を含む
ことを特徴とする請求項4~6のいずれかに記載された無機繊維質成形体の製造方法。 - 前記成形体がボードであり、400℃で24時間加熱したときの反り量が1.3mm以下である
ことを特徴とする請求項4~7のいずれかに記載された無機繊維質成形体の製造方法。 - 請求項1~3のいずれかに記載された無機繊維質成形体を含む
ことを特徴とする加熱設備。
Priority Applications (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP11832302.1A EP2628717A4 (en) | 2010-10-14 | 2011-10-14 | INORGANIC FIBER FORM BODIES, METHOD FOR THE PRODUCTION THEREOF AND HEATING DEVICE THEREFOR |
KR1020137009307A KR20140020826A (ko) | 2010-10-14 | 2011-10-14 | 무기 섬유질성형체 및 그 제조 방법 및 가열 설비 |
AU2011315024A AU2011315024B2 (en) | 2010-10-14 | 2011-10-14 | Inorganic fiber molded article, method for producing same, and heating equipment |
CN201180049363.9A CN103153913B (zh) | 2010-10-14 | 2011-10-14 | 无机纤维质成型体及其制造方法以及加热设备 |
Applications Claiming Priority (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2010-231303 | 2010-10-14 | ||
JP2010231303 | 2010-10-14 | ||
JP2011-154567 | 2011-07-13 | ||
JP2011154567A JP4975179B2 (ja) | 2010-10-14 | 2011-07-13 | 無機繊維質成形体及びその製造方法並びに加熱設備 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2012049858A1 true WO2012049858A1 (ja) | 2012-04-19 |
Family
ID=45938099
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2011/005763 WO2012049858A1 (ja) | 2010-10-14 | 2011-10-14 | 無機繊維質成形体及びその製造方法並びに加熱設備 |
Country Status (7)
Country | Link |
---|---|
US (1) | US20120100983A1 (ja) |
EP (1) | EP2628717A4 (ja) |
JP (1) | JP4975179B2 (ja) |
KR (1) | KR20140020826A (ja) |
CN (1) | CN103153913B (ja) |
AU (1) | AU2011315024B2 (ja) |
WO (1) | WO2012049858A1 (ja) |
Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2013175545A1 (ja) * | 2012-05-22 | 2013-11-28 | ニチアス株式会社 | 加熱装置 |
JP5863917B1 (ja) * | 2014-09-22 | 2016-02-17 | ニチアス株式会社 | 耐火構造及びその使用方法 |
WO2017090633A1 (ja) * | 2015-11-27 | 2017-06-01 | 曙ブレーキ工業株式会社 | 摩擦材 |
US9944552B2 (en) | 2013-07-22 | 2018-04-17 | Morgan Advanced Materials Plc | Inorganic fibre compositions |
US10894737B2 (en) | 2016-01-15 | 2021-01-19 | Thermal Ceramics Uk Limited | Apparatus and method for forming melt-formed inorganic fibres |
DE102021211745A1 (de) | 2020-10-23 | 2022-04-28 | Thermal Ceramics Uk Limited | Wärmeisolierung |
CN114635229A (zh) * | 2022-02-25 | 2022-06-17 | 江苏恒科新材料有限公司 | 一种隔热聚酯纳米纤维膜的制备方法 |
Families Citing this family (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US8940134B2 (en) * | 2011-04-05 | 2015-01-27 | Nichias Corporation | Paper comprising heat treated bio-soluble inorganic fibers, and method and equipment for making same |
JP5022512B1 (ja) * | 2011-12-01 | 2012-09-12 | ニチアス株式会社 | 不定形組成物 |
JP5856541B2 (ja) * | 2012-06-07 | 2016-02-09 | ニチアス株式会社 | 生理食塩水に可溶なAl−Ca系無機繊維及びその組成物 |
JP2014228035A (ja) * | 2013-05-21 | 2014-12-08 | イソライト工業株式会社 | 耐火断熱材及びその製造方法 |
CN103405167B (zh) * | 2013-08-09 | 2016-01-20 | 赵伟 | 家用食品烘烤装置 |
JP5634637B1 (ja) * | 2014-08-08 | 2014-12-03 | ニチアス株式会社 | 生体溶解性無機繊維 |
JP6496268B2 (ja) * | 2016-03-29 | 2019-04-03 | 日本碍子株式会社 | セラミックス焼成体の製造方法 |
JP6453824B2 (ja) * | 2016-09-07 | 2019-01-16 | ニチアス株式会社 | 無機繊維質成形体 |
JP6940792B2 (ja) * | 2019-12-03 | 2021-09-29 | デンカ株式会社 | 無機繊維成形体、加熱炉、構造体、及び無機繊維成形体の製造方法 |
DE102022203542A1 (de) | 2022-04-07 | 2023-10-12 | E.G.O. Elektro-Gerätebau GmbH | Wärmedämmformkörper und Verfahren zur Herstellung eines solchen Wärmedämmformkörpers |
Citations (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2003003335A (ja) * | 2001-06-21 | 2003-01-08 | Toshiba Monofrax Co Ltd | 無機繊維 |
JP2003089547A (ja) * | 2001-04-09 | 2003-03-28 | Toshiba Monofrax Co Ltd | 生理食塩水に可溶な無機繊維とその製造方法 |
JP2005089913A (ja) * | 2003-09-18 | 2005-04-07 | Saint-Gobain Tm Kk | 無機繊維およびその製造方法 |
JP2005515307A (ja) * | 2002-01-10 | 2005-05-26 | ユニフラックス コーポレイション | 高温耐性ガラス質無機繊維 |
JP2007197870A (ja) * | 2006-01-27 | 2007-08-09 | Nichias Corp | 無機繊維質成形体及びその製造方法 |
JP2007211963A (ja) * | 2006-02-13 | 2007-08-23 | Ibiden Co Ltd | 無機繊維体 |
JP2008518119A (ja) * | 2004-11-01 | 2008-05-29 | ザ・モーガン・クルーシブル・カンパニー・ピーエルシー | アルカリ土類シリケート繊維の改質 |
JP2008162853A (ja) | 2006-12-28 | 2008-07-17 | Nichias Corp | 無機繊維質成形体及び不定形無機繊維質組成物 |
Family Cites Families (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
AR204579A1 (es) * | 1974-05-30 | 1976-02-12 | Babcock & Wilcox Co | Procedimiento para la formacion de un producto eristalino elastico de grano fino y material obtenido |
JP2000220037A (ja) * | 1999-01-28 | 2000-08-08 | Nichias Corp | 生理学的媒体に可溶な非晶質無機繊維 |
JP2002266169A (ja) * | 2000-12-27 | 2002-09-18 | Toshiba Monofrax Co Ltd | 耐熱性無機繊維及び無機繊維製品 |
KR101047623B1 (ko) * | 2001-10-09 | 2011-07-07 | 쓰리엠 이노베이티브 프로퍼티즈 컴파니 | 생체가용성 무기 섬유 및 운모질 결합제를 함유하는 조성물 |
GB0424190D0 (en) * | 2004-11-01 | 2004-12-01 | Morgan Crucible Co | Modification of alkaline earth silicate fibres |
CN101460717B (zh) * | 2006-06-01 | 2013-01-16 | 3M创新有限公司 | 多层安装垫 |
AU2007327075B8 (en) * | 2006-11-28 | 2012-09-06 | Morgan Advanced Materials Plc | Inorganic fibre compositions |
US20080178992A1 (en) * | 2007-01-31 | 2008-07-31 | Geo2 Technologies, Inc. | Porous Substrate and Method of Fabricating the Same |
JP4977253B1 (ja) * | 2011-03-30 | 2012-07-18 | ニチアス株式会社 | 無機繊維質ペーパー及びその製造方法並びに設備 |
JP4937414B1 (ja) * | 2011-03-30 | 2012-05-23 | ニチアス株式会社 | 硬化定形物 |
-
2011
- 2011-07-13 JP JP2011154567A patent/JP4975179B2/ja active Active
- 2011-10-14 WO PCT/JP2011/005763 patent/WO2012049858A1/ja active Application Filing
- 2011-10-14 CN CN201180049363.9A patent/CN103153913B/zh active Active
- 2011-10-14 AU AU2011315024A patent/AU2011315024B2/en not_active Ceased
- 2011-10-14 KR KR1020137009307A patent/KR20140020826A/ko not_active Application Discontinuation
- 2011-10-14 EP EP11832302.1A patent/EP2628717A4/en not_active Withdrawn
- 2011-10-14 US US13/317,301 patent/US20120100983A1/en not_active Abandoned
Patent Citations (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2003089547A (ja) * | 2001-04-09 | 2003-03-28 | Toshiba Monofrax Co Ltd | 生理食塩水に可溶な無機繊維とその製造方法 |
JP2003003335A (ja) * | 2001-06-21 | 2003-01-08 | Toshiba Monofrax Co Ltd | 無機繊維 |
JP2005515307A (ja) * | 2002-01-10 | 2005-05-26 | ユニフラックス コーポレイション | 高温耐性ガラス質無機繊維 |
JP2005089913A (ja) * | 2003-09-18 | 2005-04-07 | Saint-Gobain Tm Kk | 無機繊維およびその製造方法 |
JP2008518119A (ja) * | 2004-11-01 | 2008-05-29 | ザ・モーガン・クルーシブル・カンパニー・ピーエルシー | アルカリ土類シリケート繊維の改質 |
JP2007197870A (ja) * | 2006-01-27 | 2007-08-09 | Nichias Corp | 無機繊維質成形体及びその製造方法 |
JP2007211963A (ja) * | 2006-02-13 | 2007-08-23 | Ibiden Co Ltd | 無機繊維体 |
JP2008162853A (ja) | 2006-12-28 | 2008-07-17 | Nichias Corp | 無機繊維質成形体及び不定形無機繊維質組成物 |
Cited By (19)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
KR102183051B1 (ko) * | 2012-05-22 | 2020-11-25 | 니찌아스 카부시키카이샤 | 가열장치 |
CN104335676A (zh) * | 2012-05-22 | 2015-02-04 | 霓佳斯株式会社 | 加热装置 |
US10143042B2 (en) | 2012-05-22 | 2018-11-27 | Nichias Corporation | Heating device |
KR20190097330A (ko) * | 2012-05-22 | 2019-08-20 | 니찌아스 카부시키카이샤 | 가열장치 |
WO2013175545A1 (ja) * | 2012-05-22 | 2013-11-28 | ニチアス株式会社 | 加熱装置 |
US9944552B2 (en) | 2013-07-22 | 2018-04-17 | Morgan Advanced Materials Plc | Inorganic fibre compositions |
JP5863917B1 (ja) * | 2014-09-22 | 2016-02-17 | ニチアス株式会社 | 耐火構造及びその使用方法 |
WO2016047041A1 (ja) * | 2014-09-22 | 2016-03-31 | ニチアス株式会社 | 耐火構造及びその使用方法 |
US11077641B2 (en) | 2014-09-22 | 2021-08-03 | Nichias Corporation | Fireproof construction and method for using same |
US10584757B2 (en) | 2015-11-27 | 2020-03-10 | Akebono Brake Industry Co., Ltd. | Friction material |
WO2017090633A1 (ja) * | 2015-11-27 | 2017-06-01 | 曙ブレーキ工業株式会社 | 摩擦材 |
US10894737B2 (en) | 2016-01-15 | 2021-01-19 | Thermal Ceramics Uk Limited | Apparatus and method for forming melt-formed inorganic fibres |
DE102021211745A1 (de) | 2020-10-23 | 2022-04-28 | Thermal Ceramics Uk Limited | Wärmeisolierung |
DE102021211747A1 (de) | 2020-10-23 | 2022-04-28 | Thermal Ceramics Uk Limited | Wärmeisolierung |
WO2022084655A1 (en) | 2020-10-23 | 2022-04-28 | Thermal Ceramics Uk Limited | Thermal insulation |
DE102021211746A1 (de) | 2020-10-23 | 2022-04-28 | Thermal Ceramics Uk Limited | Wärmeisolierung |
DE112021005608T5 (de) | 2020-10-23 | 2023-08-24 | Thermal Ceramics Uk Limited | Wärmeisolierung |
DE102021211747B4 (de) | 2020-10-23 | 2024-02-29 | Thermal Ceramics Uk Limited | Wärmeisolierung |
CN114635229A (zh) * | 2022-02-25 | 2022-06-17 | 江苏恒科新材料有限公司 | 一种隔热聚酯纳米纤维膜的制备方法 |
Also Published As
Publication number | Publication date |
---|---|
EP2628717A4 (en) | 2014-04-16 |
JP2012102450A (ja) | 2012-05-31 |
JP4975179B2 (ja) | 2012-07-11 |
AU2011315024B2 (en) | 2015-03-19 |
KR20140020826A (ko) | 2014-02-19 |
AU2011315024A1 (en) | 2013-03-14 |
CN103153913B (zh) | 2016-04-20 |
EP2628717A1 (en) | 2013-08-21 |
US20120100983A1 (en) | 2012-04-26 |
CN103153913A (zh) | 2013-06-12 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP4975179B2 (ja) | 無機繊維質成形体及びその製造方法並びに加熱設備 | |
JP4977253B1 (ja) | 無機繊維質ペーパー及びその製造方法並びに設備 | |
JP5015336B1 (ja) | 無機繊維質ペーパー及びその製造方法 | |
JP5277337B1 (ja) | 加熱装置 | |
EP2692712B1 (en) | Method of hardening a shaped article | |
JP2007197264A (ja) | 無機繊維質成形体 | |
KR20130130842A (ko) | 습윤 블랭킷 | |
US8940134B2 (en) | Paper comprising heat treated bio-soluble inorganic fibers, and method and equipment for making same | |
JP5236100B1 (ja) | 無機繊維質ペーパーからなる緩衝材及びその製造方法並びに設備 | |
JP5148770B1 (ja) | 無機繊維質ペーパーからなる緩衝材及びその製造方法 | |
JP2013243120A (ja) | 加熱装置 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
WWE | Wipo information: entry into national phase |
Ref document number: 201180049363.9 Country of ref document: CN |
|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 11832302 Country of ref document: EP Kind code of ref document: A1 |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2011832302 Country of ref document: EP |
|
ENP | Entry into the national phase |
Ref document number: 2011315024 Country of ref document: AU Date of ref document: 20111014 Kind code of ref document: A |
|
ENP | Entry into the national phase |
Ref document number: 20137009307 Country of ref document: KR Kind code of ref document: A |
|
NENP | Non-entry into the national phase |
Ref country code: DE |