WO2013121801A1 - マクロ多孔性チタン化合物モノリスとその製造方法 - Google Patents
マクロ多孔性チタン化合物モノリスとその製造方法 Download PDFInfo
- Publication number
- WO2013121801A1 WO2013121801A1 PCT/JP2013/000886 JP2013000886W WO2013121801A1 WO 2013121801 A1 WO2013121801 A1 WO 2013121801A1 JP 2013000886 W JP2013000886 W JP 2013000886W WO 2013121801 A1 WO2013121801 A1 WO 2013121801A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- monolith
- titanium
- oxygen
- macroporous
- deficient
- Prior art date
Links
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01G—COMPOUNDS CONTAINING METALS NOT COVERED BY SUBCLASSES C01D OR C01F
- C01G23/00—Compounds of titanium
- C01G23/04—Oxides; Hydroxides
- C01G23/043—Titanium sub-oxides
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B82—NANOTECHNOLOGY
- B82Y—SPECIFIC USES OR APPLICATIONS OF NANOSTRUCTURES; MEASUREMENT OR ANALYSIS OF NANOSTRUCTURES; MANUFACTURE OR TREATMENT OF NANOSTRUCTURES
- B82Y30/00—Nanotechnology for materials or surface science, e.g. nanocomposites
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01B—NON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
- C01B21/00—Nitrogen; Compounds thereof
- C01B21/06—Binary compounds of nitrogen with metals, with silicon, or with boron, or with carbon, i.e. nitrides; Compounds of nitrogen with more than one metal, silicon or boron
- C01B21/076—Binary compounds of nitrogen with metals, with silicon, or with boron, or with carbon, i.e. nitrides; Compounds of nitrogen with more than one metal, silicon or boron with titanium or zirconium or hafnium
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01B—NON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
- C01B21/00—Nitrogen; Compounds thereof
- C01B21/06—Binary compounds of nitrogen with metals, with silicon, or with boron, or with carbon, i.e. nitrides; Compounds of nitrogen with more than one metal, silicon or boron
- C01B21/076—Binary compounds of nitrogen with metals, with silicon, or with boron, or with carbon, i.e. nitrides; Compounds of nitrogen with more than one metal, silicon or boron with titanium or zirconium or hafnium
- C01B21/0761—Preparation by direct nitridation of titanium, zirconium or hafnium
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01B—NON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
- C01B21/00—Nitrogen; Compounds thereof
- C01B21/082—Compounds containing nitrogen and non-metals and optionally metals
- C01B21/0821—Oxynitrides of metals, boron or silicon
-
- 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
- C04B35/46—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 titanium oxides or titanates
-
- 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
- C04B35/515—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
- C04B35/58—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 borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides
- C04B35/58007—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 borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on refractory metal nitrides
- C04B35/58014—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 borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on refractory metal nitrides based on titanium nitrides, e.g. TiAlON
-
- 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
- C04B38/0022—Porous mortars, concrete, artificial stone or ceramic ware; Preparation thereof obtained by a chemical conversion or reaction other than those relating to the setting or hardening of cement-like material or to the formation of a sol or a gel, e.g. by carbonising or pyrolysing preformed cellular materials based on polymers, organo-metallic or organo-silicon precursors
- C04B38/0032—Porous mortars, concrete, artificial stone or ceramic ware; Preparation thereof obtained by a chemical conversion or reaction other than those relating to the setting or hardening of cement-like material or to the formation of a sol or a gel, e.g. by carbonising or pyrolysing preformed cellular materials based on polymers, organo-metallic or organo-silicon precursors one of the precursor materials being a monolithic element having approximately the same dimensions as the final article, e.g. a paper sheet which after carbonisation will react with silicon to form a porous silicon carbide porous body
-
- 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
- C04B41/00—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone
- C04B41/0072—Heat treatment
-
- 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
- C04B41/00—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone
- C04B41/009—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone characterised by the material treated
-
- 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
- C04B41/00—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone
- C04B41/80—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone of only ceramics
-
- C—CHEMISTRY; METALLURGY
- C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
- C25B—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES FOR THE PRODUCTION OF COMPOUNDS OR NON-METALS; APPARATUS THEREFOR
- C25B11/00—Electrodes; Manufacture thereof not otherwise provided for
- C25B11/04—Electrodes; Manufacture thereof not otherwise provided for characterised by the material
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2002/00—Crystal-structural characteristics
- C01P2002/70—Crystal-structural characteristics defined by measured X-ray, neutron or electron diffraction data
- C01P2002/72—Crystal-structural characteristics defined by measured X-ray, neutron or electron diffraction data by d-values or two theta-values, e.g. as X-ray diagram
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2004/00—Particle morphology
- C01P2004/01—Particle morphology depicted by an image
- C01P2004/03—Particle morphology depicted by an image obtained by SEM
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2004/00—Particle morphology
- C01P2004/60—Particles characterised by their size
- C01P2004/61—Micrometer sized, i.e. from 1-100 micrometer
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2004/00—Particle morphology
- C01P2004/60—Particles characterised by their size
- C01P2004/62—Submicrometer sized, i.e. from 0.1-1 micrometer
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2004/00—Particle morphology
- C01P2004/60—Particles characterised by their size
- C01P2004/64—Nanometer sized, i.e. from 1-100 nanometer
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2006/00—Physical properties of inorganic compounds
- C01P2006/40—Electric properties
-
- 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
- C04B2111/00—Mortars, concrete or artificial stone or mixtures to prepare them, characterised by specific function, property or use
- C04B2111/00474—Uses not provided for elsewhere in C04B2111/00
- C04B2111/0081—Uses not provided for elsewhere in C04B2111/00 as catalysts or catalyst carriers
-
- 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
- C04B2111/00—Mortars, concrete or artificial stone or mixtures to prepare them, characterised by specific function, property or use
- C04B2111/00474—Uses not provided for elsewhere in C04B2111/00
- C04B2111/0081—Uses not provided for elsewhere in C04B2111/00 as catalysts or catalyst carriers
- C04B2111/00818—Enzyme carriers
-
- 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
- C04B2235/3231—Refractory metal oxides, their mixed metal oxides, or oxide-forming salts thereof
- C04B2235/3232—Titanium oxides or titanates, e.g. rutile or anatase
-
- 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
- C04B2235/38—Non-oxide ceramic constituents or additives
- C04B2235/3852—Nitrides, e.g. oxynitrides, carbonitrides, oxycarbonitrides, lithium nitride, magnesium nitride
- C04B2235/3886—Refractory metal nitrides, e.g. vanadium nitride, tungsten nitride
-
- 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
- C04B2235/40—Metallic constituents or additives not added as binding phase
- C04B2235/404—Refractory metals
-
- 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
- C04B2235/42—Non metallic elements added as constituents or additives, e.g. sulfur, phosphor, selenium or tellurium
- C04B2235/422—Carbon
-
- 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
- C04B2235/48—Organic compounds becoming part of a ceramic after heat treatment, e.g. carbonising phenol resins
-
- 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
- C04B2235/60—Aspects relating to the preparation, properties or mechanical treatment of green bodies or pre-forms
- C04B2235/616—Liquid infiltration of green bodies or pre-forms
-
- 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
- C04B2235/65—Aspects relating to heat treatments of ceramic bodies such as green ceramics or pre-sintered ceramics, e.g. burning, sintering or melting processes
- C04B2235/658—Atmosphere during thermal treatment
- C04B2235/6587—Influencing the atmosphere by vaporising a solid material, e.g. by using a burying of sacrificial powder
-
- 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
- C04B2235/65—Aspects relating to heat treatments of ceramic bodies such as green ceramics or pre-sintered ceramics, e.g. burning, sintering or melting processes
- C04B2235/66—Specific sintering techniques, e.g. centrifugal sintering
- C04B2235/661—Multi-step sintering
- C04B2235/662—Annealing after sintering
- C04B2235/664—Reductive annealing
-
- 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
- C04B2235/79—Non-stoichiometric products, e.g. perovskites (ABO3) with an A/B-ratio other than 1
-
- 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
- C04B2235/80—Phases present in the sintered or melt-cast ceramic products other than the main phase
- C04B2235/81—Materials characterised by the absence of phases other than the main phase, i.e. single phase materials
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M4/00—Electrodes
- H01M4/02—Electrodes composed of, or comprising, active material
- H01M4/36—Selection of substances as active materials, active masses, active liquids
- H01M4/48—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
- Y02E60/10—Energy storage using batteries
Definitions
- the present invention relates to a titanium compound monolith having macroporosity and a method for producing the same. More specifically, the present invention relates to a macroporous titanium compound monolith having a co-continuous structure of a skeleton composed of oxygen-deficient titanium oxide, titanium oxynitride or titanium nitride and macropores, and a method for producing the same.
- a porous monolith having pores made of an inorganic material such as silica is known. Such monoliths are widely used in chromatographic separation columns, enzyme carriers, catalyst carriers and the like.
- a sol-gel method which is a liquid phase reaction is generally used.
- the sol-gel method is based on a sol-gel reaction, that is, hydrolysis of the compound and subsequent polycondensation using an inorganic low-molecular compound having a hydrolyzable functional group dispersed in a dispersion medium as a starting material.
- a method for obtaining an oxide aggregate or polymer will be described.
- the inorganic low molecular weight compound as a starting material is, for example, a metal alkoxide, a metal chloride, and a metal salt having a hydrolyzable functional group.
- Patent Document 1 International Publication No. 03/002458 describes a mesopore having a narrow pore distribution by adjusting the conditions of the sol-gel reaction so that the sol-gel transition and the phase separation occur simultaneously.
- a method for producing a porous monolith having controlled macropores is disclosed.
- Patent Document 2 International Publication No. 2007/021037 discloses a method for producing a porous monolith having a skeleton composed of titanium dioxide (TiO 2 ) and controlled mesopores and macropores. .
- the method disclosed in Patent Document 2 is very hydrolyzable in the state of an inorganic low molecular weight compound (eg, alkoxide) based on the method disclosed in Patent Document 1, and the conventional sol-gel method controls pores.
- an inorganic low molecular weight compound eg, alkoxide
- Non-Patent Document 1 is a document disclosing the method, a porous material obtained by mixing an organic solvent containing a high-molecular substance serving as a macropore mold and titanium dioxide powder, and molding and baking the resulting mixture.
- This porous monolith has electronic conductivity based on oxygen-deficient titanium oxide.
- the porous monolith produced by this method is basically an aggregate of powder as judged from the production method, and has only macropores formed by burning out the polymer substance dispersed in the mixture. Yes, with no controlled macropores.
- oxygen deficient titanium oxide powders are bound to each other, but it is considered that a single crystal phase composed of oxygen deficient titanium oxide has not been realized.
- the present invention relates to a macroporous titanium compound monolith composed of oxygen-deficient titanium oxide, titanium oxynitride or titanium nitride, which is a titanium compound other than titanium dioxide, and having controlled macropores and electronic conductivity, and production thereof
- the purpose is to provide a method.
- the macroporous titanium compound monolith of the present invention has a co-continuous structure of a skeleton composed of single-phase oxygen-deficient titanium oxide and macropores, and has electronic conductivity based on the oxygen-deficient titanium oxide.
- the method for producing a macroporous titanium compound monolith of the present invention accommodates a macroporous titanium dioxide monolith having a co-continuous structure of a skeleton composed of titanium dioxide and macropores and a metal having titanium reducing ability in a container. Then, the inside of the container is set to a vacuum atmosphere or an inert gas atmosphere, and by heating the monolith and the metal, the metal is used as an oxygen getter, and vapor phase reduction is performed to remove oxygen atoms from titanium dioxide constituting the monolith. And obtaining a macroporous oxygen-deficient titanium oxide monolith having a skeleton composed of oxygen-deficient titanium oxide and the macropores and having electronic conductivity based on the oxygen-deficient titanium oxide It is.
- the macroporous titanium compound monolith of the present invention viewed from another aspect has a co-continuous structure of a skeleton composed of titanium oxynitride and macropores, and has electronic conductivity based on the titanium oxynitride.
- a method for producing a macroporous titanium compound monolith includes a macroporous titanium compound monolith having a co-continuous structure of a skeleton composed of titanium dioxide or oxygen-deficient titanium oxide and macropores.
- the metal nitride is contained in a container, the inside of the container is set to a vacuum atmosphere or an inert gas atmosphere, the monolith and the metal nitride are heated, and the metal nitride is used as an oxygen getter and a nitrogen supply source.
- the titanium oxynitride has a co-continuous structure of a skeleton composed of titanium oxynitride and a macropore by performing vapor phase reduction in which oxygen atoms are taken from the titanium compound constituting the monolith and nitrogen atoms are supplied. Is a method for obtaining a macroporous titanium oxynitride monolith having electronic conductivity based on the above.
- the macroporous titanium compound monolith of the present invention viewed from another aspect has a co-continuous structure of a skeleton composed of titanium nitride and macropores, and has electronic conductivity based on the titanium nitride.
- a method for producing a macroporous titanium compound monolith according to the present invention includes a macroporous structure having a co-continuous structure of a skeleton composed of titanium dioxide, oxygen-deficient titanium oxide, or titanium oxynitride and a macropore.
- a macroporous titanium compound monolith composed of oxygen-deficient titanium oxide, titanium oxynitride or titanium nitride, which is a titanium compound other than titanium dioxide, and having controlled macropores and electronic conductivity, and its monolith A manufacturing method is provided. Moreover, according to the present invention, a macroporous titanium compound monolith having a skeleton composed of single-phase oxygen-deficient titanium oxide can be obtained.
- FIG. 1 is a diagram showing an observation image of the macroporous titanium dioxide monolith produced in the example by a scanning electron microscope (SEM).
- FIG. 2 is a diagram showing the results of pore distribution measurement by the mercury intrusion method for the macroporous titanium dioxide monolith and the macroporous oxygen-deficient titanium oxide monolith produced in the examples.
- FIG. 3 is a diagram showing diffraction peaks obtained by X-ray diffraction (XRD) measurement for the macroporous titanium dioxide (anatase type) monolith and the macroporous oxygen-deficient titanium oxide monolith prepared in the examples.
- FIG. 4 is an SEM observation image of the macroporous oxygen-deficient titanium oxide monolith produced in the example.
- FIG. XRD X-ray diffraction
- FIG. 5 is a diagram showing the results of evaluating the temperature dependence of the electrical resistivity for the macroporous oxygen-deficient titanium oxide (Ti 4 O 7 ) monolith produced in the example.
- FIG. 6 is a diagram showing the results of evaluating the temperature dependence of the electrical resistivity for the macroporous oxygen-deficient titanium oxide monolith produced in the example.
- FIG. 7A is a diagram showing diffraction peaks by XRD measurement for the macroporous titanium dioxide (rutile) monolith and the macroporous oxygen-deficient titanium oxide monolith produced in the examples.
- FIG. 7B is an enlarged view of the range of 20 degrees to 30 degrees with the diffraction angle 2 ⁇ at the diffraction peak of R1 shown in FIG. 7A.
- FIG. 8 is an SEM observation image of the macroporous titanium oxynitride monolith produced in the example.
- FIG. 9 is a diagram showing diffraction peaks by XRD measurement for the macroporous titanium oxynitride monolith and the macroporous titanium nitride monolith produced in the examples.
- FIG. 10 is an SEM observation image of the macroporous titanium nitride monolith produced in the example.
- FIG. 11 is a view showing an SEM observation image of the macroporous titanium dioxide monolith and the macroporous oxygen-deficient titanium oxide monolith in which carbon particles are arranged, prepared in the example.
- FIG. 12 is a graph showing the results of pore distribution measurement by the nitrogen adsorption / desorption method for the macroporous titanium dioxide monolith and the macroporous oxygen-deficient titanium oxide monolith produced in the examples.
- FIG. 13 is a diagram showing the results of pore distribution measurement by the nitrogen adsorption / desorption method for the macroporous titanium dioxide monolith and the macroporous oxygen-deficient titanium oxide monolith produced in the examples.
- FIG. 14 is a diagram showing the results of thermogravimetric analysis (TG) evaluation of the macroporous oxygen-deficient titanium oxide monolith in which carbon particles are arranged, prepared in the example.
- TG thermogravimetric analysis
- FIG. 15 is a diagram showing an evaluation result of Raman spectroscopic analysis for a macroporous oxygen-deficient titanium oxide monolith in which carbon particles are arranged, which is produced in the example.
- FIG. 16 is a diagram showing evaluation results of cyclic voltammogram (CV) for the macroporous oxygen-deficient titanium oxide monolith produced in the example.
- FIG. 17 is a diagram showing the CV evaluation results for the macroporous oxygen-deficient titanium oxide monolith produced in the example.
- FIG. 18 is a view showing an SEM observation image of the macroporous oxygen-deficient titanium oxide monolith in which platinum particles are arranged, prepared in the example.
- FIG. 19 is a diagram showing the results of linear sweep voltammetry (LSV) evaluation for the macroporous oxygen-deficient titanium oxide monolith in which platinum particles are arranged, which was produced in the example.
- FIG. 20 is a diagram showing the evaluation results of LSV in the presence of methanol for the macroporous oxygen-deficient titanium oxide monolith in which platinum particles are arranged, prepared in Example.
- LSV linear sweep voltammetry
- a first aspect of the present disclosure is a macroporous titanium having a co-continuous structure of a skeleton composed of a single-phase oxygen-deficient titanium oxide and a macropore, and having electron conductivity based on the oxygen-deficient titanium oxide A compound monolith is provided.
- the second aspect provides a macroporous titanium compound monolith having an electrical resistivity of 10 3 ⁇ ⁇ cm or less.
- the third aspect provides a macroporous titanium compound monolith in which carbon particles and / or metal particles are arranged in the skeleton and / or on the surface of the skeleton in addition to the first or second aspect.
- the fourth aspect provides a macroporous titanium compound monolith as an electrode in addition to any one of the first to third aspects.
- a macroporous titanium dioxide monolith having a co-continuous structure of a skeleton composed of titanium dioxide and macropores and a metal having titanium reducing ability are accommodated in a container, and the inside of the container is evacuated to a vacuum atmosphere.
- the metal is used as an oxygen getter, and vapor phase reduction is performed to remove oxygen atoms from the titanium dioxide constituting the monolith.
- Production of a macroporous titanium compound monolith having a co-continuous structure of the skeleton and the macropores, and obtaining a macroporous oxygen-deficient titanium oxide monolith having electronic conductivity based on the oxygen-deficient titanium oxide Provide a method.
- 6th aspect provides the manufacturing method of a macroporous titanium compound monolith which accommodates the foil-shaped said metal in the said container in addition to a 5th aspect.
- the seventh aspect provides a method for producing a macroporous titanium compound monolith, in addition to the fifth or sixth aspect, wherein the metal is at least one selected from zirconium (Zr) and hafnium (Hf).
- the eighth aspect provides a method for producing a macroporous titanium compound monolith, in addition to any one of the fifth to seventh aspects, wherein the heating temperature is 900 to 1300 ° C.
- a ninth aspect provides a method for producing a macroporous titanium compound monolith, in addition to any one of the fifth to eighth aspects, wherein the titanium dioxide constituting the skeleton of the macroporous titanium dioxide monolith is anatase type To do.
- the tenth aspect provides a macroporous titanium compound monolith having a co-continuous structure of a skeleton composed of titanium oxynitride and a macropore, and having electronic conductivity based on the titanium oxynitride.
- a macroporous titanium compound monolith having a co-continuous structure of a skeleton composed of titanium dioxide or oxygen-deficient titanium oxide and a macropore, and a metal nitride are contained in a container, In a vacuum atmosphere or an inert gas atmosphere, and the monolith and the metal nitride are heated, and the metal nitride is used as an oxygen getter and a nitrogen supply source to remove oxygen atoms from the titanium compound constituting the monolith and to form nitrogen.
- a method for producing a macroporous titanium compound monolith is obtained.
- the twelfth aspect provides a method for producing a macroporous titanium compound monolith in which the powdered metal nitride is accommodated in the container in addition to the eleventh aspect.
- the thirteenth aspect provides a method for producing a macroporous titanium compound monolith, in addition to the eleventh or twelfth aspect, wherein the metal nitride is at least one selected from titanium nitride, zirconium nitride, and hafnium nitride.
- the fourteenth aspect provides a method for producing a macroporous titanium compound monolith, in addition to any one of the eleventh to thirteenth aspects, wherein the heating temperature is 950 to 1200 ° C.
- a macroporous titanium dioxide monolith having a co-continuous structure of a skeleton composed of titanium dioxide and the macropores, the metal nitride, Is provided in the container.
- a method for producing a macroporous titanium compound monolith is provided.
- the sixteenth aspect provides a macroporous titanium compound monolith having a co-continuous structure of a skeleton composed of titanium nitride and macropores and having electronic conductivity based on the titanium nitride.
- a macroporous titanium compound monolith having a co-continuous structure of a skeleton composed of titanium dioxide, oxygen-deficient titanium oxide, or titanium oxynitride and a macropore is subjected to thermal decomposition temperature of ammonia in an atmosphere containing ammonia.
- gas phase reduction is performed by depriving oxygen atoms from the titanium compound constituting the monolith and supplying nitrogen atoms, thereby having a co-continuous structure of the skeleton composed of titanium nitride and the macropores.
- a method for producing a macroporous titanium compound monolith that obtains a macroporous titanium nitride monolith having electronic conductivity based on the titanium nitride.
- 18th aspect provides the manufacturing method of the macroporous titanium compound monolith whose temperature of the said heat processing is 1000 degreeC or more in addition to 17th aspect.
- a macroporous titanium dioxide monolith having a co-continuous structure of a skeleton composed of titanium dioxide and the macropores is heated at a thermal decomposition temperature of ammonia in an atmosphere containing ammonia.
- a method for producing a macroporous titanium compound monolith that is heat-treated as described above is provided.
- macroporous titanium compound monolith refers to a titanium compound monolith having controlled macropores.
- Controlled macropores are macropores that exhibit a co-continuous structure with the monolith skeleton, have high uniformity in diameter, and do not have isolated pores (isolated pores as macropores, the same shall apply hereinafter). Means a hole.
- micropore means a pore having a diameter of 50 nm or more in accordance with the proposal by IUPAC.
- mesopore refers to a pore having a diameter of 2 nm or more and less than 50 nm.
- a pore having a diameter of less than 2 nm is a “micropore”.
- the diameter and average diameter of the pores can be determined by general pore distribution measurement, for example, pore distribution measurement by mercury porosimetry or nitrogen adsorption / desorption method.
- a precursor macroporous titanium dioxide monolith hereinafter referred to as “monolith dioxide”
- a metal having titanium reducing ability are used. use.
- the precursor monolithic monolith has a co-continuous structure of a skeleton composed of titanium dioxide and macropores. As described above, this co-continuous structure has high uniformity of the diameter of macropores and does not have isolated holes.
- the titanium compound constituting the skeleton of the precursor monolith is changed from titanium dioxide to oxygen-deficient titanium oxide. At this time, the structure as a macroporous monolith is maintained. Thereby, an oxygen-deficient monolith in which the co-continuous structure of the skeleton and macropores in the precursor monolith is maintained is obtained.
- the uniformity of the macropore diameter is high and there are no isolated pores.
- Such control of macropores cannot be achieved with a conventional molded body obtained by agglomerating (binding) oxygen-deficient titanium oxide powder, for example, Ebonex. Only spaces with random size and shape that are present between the agglomerated powders are observed.
- the titanium dioxide constituting the skeleton of the precursor monolith is preferably anatase type.
- an oxygen-deficient monolith single-phase oxygen-deficient monolith having a skeleton composed of oxygen-deficient titanium oxide having a single crystal phase (hereinafter also referred to as “single phase”) can be obtained.
- a monophase oxygen-deficient monolith cannot be obtained from a monolith having a skeleton composed of rutile titanium dioxide.
- the formation of a single phase oxygen deficient monolith is also an advantage of the present invention.
- Evonex is merely an aggregate in which plural types of titanium powders having different oxygen deficiency states (different oxidation states) are mixed.
- the precursor monolith dioxide may or may not have mesopores.
- the method of forming the precursor monolith that is, the macroporous titanium dioxide monolith having a co-continuous structure of a skeleton composed of titanium dioxide and macropores.
- a monolith dioxide can be formed according to the methods disclosed in Patent Documents 1 and 2.
- the monolith dioxide is a method disclosed in, for example, George Hasegawa et al., “Facile Preparation of Hierarchically Porous TiO 2 Monoliths”, Journal of American Ceramic Society, vol. 93 [10], pp. 3110-3115 (2010). In this case, the formation of monolithic dioxide having a skeleton composed of anatase-type titanium dioxide is more reliable.
- anatase-type titanium dioxide is obtained by a sol-gel reaction with phase separation using a chelating agent, a strong acid salt and a phase separation controlling agent, and removal of the chelating agent after the sol-gel reaction and aging in water.
- a monolithic dioxide having a co-continuous structure of a skeleton composed of and macropores is formed.
- the skeleton-macropore co-continuous structure is formed by the sol-gel reaction with phase separation in the methods disclosed in Patent Documents 1 and 2, and in these methods, the macropore control precision is the same. And it is possible to form monolithic dioxide with a high degree of freedom, for example a more uniform macropore diameter.
- an oxygen-deficient monolith with high precision and freedom of macropore control, for example, higher uniformity of macropore diameter, can be obtained.
- an oxygen deficient monolith for example, precise control of fluid permeability is possible.
- the precursor monolith dioxide may be selected according to the skeleton of the oxygen-deficient monolith to be obtained and the structure of the macropores (for example, the average diameter of the macropores and the porosity of the monolith).
- the metal having titanium reducing ability is not limited as long as it has a higher affinity for oxygen than titanium, but is at least one selected from, for example, zirconium (Zr) and hafnium (Hf). As is clear from the fact that “the affinity for oxygen is greater than that of titanium”, titanium itself is not included in the metal having the ability to reduce titanium.
- a monolith dioxide and a metal having titanium reducing ability are contained in a container, the inside of the container is set to a vacuum atmosphere or an inert gas atmosphere, and the monolith dioxide and metal are heated. Then, using the metal as an oxygen getter, gas phase reduction is performed to take oxygen atoms from titanium dioxide constituting the skeleton of the monolith dioxide.
- the container is preferably a sealed container that can be sealed after containing the monolith dioxide and the metal.
- the vacuum atmosphere and the inert gas atmosphere mean an atmosphere in which the partial pressure of oxygen is very small (for example, 10 ⁇ 1 Pa or less, preferably 4 ⁇ 10 ⁇ 2 Pa or less). This is because as the partial pressure of oxygen in the container increases, the gas phase reduction is inhibited.
- the vacuum atmosphere is, for example, an atmosphere with a pressure of 10 ⁇ 3 to 10 ⁇ 1 Pa, and an atmosphere with a pressure of 2 ⁇ 10 ⁇ 2 to 4 ⁇ 10 ⁇ 2 Pa is preferable.
- the inert gas is, for example, nitrogen or argon.
- the pressure of the inert gas atmosphere is not particularly limited as long as the partial pressure of oxygen is very small.
- the vacuum atmosphere or inert gas atmosphere in the container has already been realized when the heating of the monolith dioxide and the metal is started. In other words, it is preferable to heat the monolith and the metal after making the inside of the container containing the monolith dioxide and the metal into a vacuum atmosphere or an inert gas atmosphere. Further, it is preferable that a vacuum atmosphere or an inert gas atmosphere in the container is maintained during the gas phase reduction. As a result, reoxidation of the monolith dioxide once reduced is suppressed, and the gas phase reduction can be carried out more stably and reliably.
- the atmosphere in the container may be adjusted by applying known equipment and techniques so that the vacuum atmosphere or inert gas atmosphere before heating is maintained as it is.
- the composition of the obtained oxygen-deficient titanium oxide is easier to control when the container is sealed and heated after the achievement. This is because if the atmosphere in the container is continuously adjusted during heating, oxygen released from titanium dioxide is discharged out of the system without reacting with the metal, and the amount of the metal to be accommodated in the container This is because it becomes difficult to control the composition of oxygen-deficient titanium oxide.
- the material constituting the container is preferably a material that does not deteriorate or corrode itself by gas phase reduction and does not inhibit gas phase reduction.
- a material used for the container glass, quartz, stainless steel, and monel alloy are preferable.
- the metal is foil-shaped, that is, the foil-shaped metal is preferably contained in a container.
- oxidation of the metal by oxygen released from titanium dioxide becomes efficient (free from titanium dioxide by the metal). This makes it possible to capture the oxygen efficiently) and to perform the gas phase reduction more stably and reliably.
- the average thickness of the metal foil is, for example, 0.01 ⁇ m to 100 ⁇ m, and preferably 0.1 ⁇ m to 100 ⁇ m.
- the method for heating the monolith dioxide contained in the container and the metal is not particularly limited. For example, what is necessary is just to accommodate the whole container which accommodated the monolith dioxide and the said metal in the furnace adjusted to heating temperature. It is also possible to heat the furnace with a vacuum.
- the heating temperature of the monolith dioxide and the metal is not limited as long as the gas phase reduction of the monolith dioxide proceeds.
- the specific heating temperature varies depending on the type of metal and the pressure in the container at the time of vapor phase reduction, but when the metal is zirconium, for example, it is 900 ° C. or higher and 1300 ° C. or lower, and preferably 1000 ° C. or higher and 1200 ° C. or lower.
- the heating temperature is too low, the gas phase reduction does not proceed stably. If the heating temperature is too high, a uniform macroporous co-continuous structure disappears. In addition, a single-phase low-order oxidized monolith cannot be obtained.
- the metal becomes an oxygen getter, and deprives oxygen atoms from titanium dioxide constituting the monolith dioxide.
- the reduction reaction can be stably and surely advanced not only to the outer surface of the monolith but also to the inside of the macropore, and the co-continuous structure of the precursor monolith dioxide is maintained (controlled). An oxygen-deficient monolith that retains the macropore structure is obtained.
- the obtained oxygen-deficient monolith has electron conductivity based on a skeleton showing a co-continuous structure, that is, an oxygen-deficient titanium oxide constituting the continuous skeleton.
- the degree of electron conductivity depends on the physical properties of the oxygen-deficient titanium oxide itself constituting the skeleton.
- the color of white monolith dioxide changed to black in oxygen deficient monolith.
- the term “having electronic conductivity” in the present specification means to exhibit an electrical resistivity ⁇ of 10 3 ⁇ ⁇ cm or less, which means at least a semiconductor. Although it is not necessary to show such an electrical resistivity ⁇ in all temperature ranges, it is preferable to show an electrical resistivity ⁇ of 10 3 ⁇ ⁇ cm or less at room temperature, for example. Depending on the composition and temperature range of the material constituting the skeleton of the produced monolith, the monolith has a lower electrical resistivity ⁇ , for example, 10 2 ⁇ ⁇ cm or less, 10 ⁇ ⁇ cm or less, 1 ⁇ ⁇ cm or less, 10 ⁇ 1 ⁇ -Indicates cm or less.
- Oxygen deficient titanium oxide refers to titanium oxide in a state where titanium is reduced as compared with titanium dioxide (the molar equivalent of oxygen is smaller than that of titanium dioxide).
- the oxygen-deficient titanium oxide is, for example, titanium oxide represented by the formula Ti n O 2n-1 (n is 2, 3, 4 or 6).
- the oxygen-deficient titanium oxide does not necessarily have a composition that satisfies the above formula, but the amount of the metal relative to the monolith dioxide contained in the container is within an appropriate range, and sufficient gas phase reduction time is ensured.
- An oxygen-deficient monolith having a skeleton composed of oxygen-deficient titanium oxide satisfying the above formula can be obtained.
- the appropriate range is, for example, from 5% by weight to 10% by weight of the metal in the stoichiometric ratio necessary to make all of the titanium dioxide contained in the monolith dioxide into oxygen-deficient titanium oxide satisfying the above formula. It is a range in which the weight percentage is excessive.
- the time required for the gas phase reduction required to obtain the oxygen-deficient titanium oxide satisfying the above formula depends on the size, shape, porosity and macropore diameter of the monolith dioxide, the form of the metal contained in the container, and the heating temperature. But it may be necessary for more than a day.
- the composition of oxygen-deficient titanium oxide can be evaluated by crystal structure analysis using X-ray diffraction (XRD) on the skeleton.
- the reaction formula of the gas phase reduction for obtaining Ti 2 O 3 (n is 2 in the above formula) using zirconium as the metal is 4TiO 2 + Zr ⁇ 2Ti 2 O 3 + ZrO 2 .
- the reaction formula of gas phase reduction for obtaining Ti 3 O 5 (n is 3), Ti 4 O 7 (n is 4) and Ti 6 O 11 (n is 6) using zirconium as a metal is as follows: 6TiO 2 + Zr ⁇ 2Ti 3 O 5 + ZrO 2 , 8TiO 2 + Zr ⁇ 2Ti 4 O 7 + ZrO 2 , 12TiO 2 + Zr ⁇ 2Ti 6 O 11 + ZrO 2 .
- An appropriate range of the weight of the metal contained in the container can be determined from these reaction equations.
- a monolith dioxide having a skeleton composed of anatase-type titanium dioxide is selected as a precursor, and the amount of the metal relative to the monolith dioxide contained in a container is set to the appropriate amount.
- an oxygen-deficient monolith having a skeleton composed of single-phase oxygen-deficient titanium oxide can be formed. This is because, as disclosed in Non-Patent Document 1, a method for forming a porous monolith in which particulate oxygen-deficient titanium oxide is bound, a method for forming Ebonex, or a titanium monolithic porous monolith with oxygen atoms.
- Particles having reactivity are mixed in advance, and the reaction between the particles and oxygen atoms of titanium dioxide is advanced using heat or the like, so that the skeleton is composed of titanium lacking oxygen.
- heat during heating also contributes to the formation of a skeleton composed of single-phase oxygen-deficient titanium oxide.
- the skeleton of the obtained oxygen-deficient monolith is composed of single-phase oxygen-deficient titanium oxide is determined by crystal structure analysis using X-ray diffraction (XRD) on the skeleton or physical property analysis of the skeleton (for example, , Conductivity analysis and magnetic analysis). For example, when a peak other than a diffraction peak based on a certain crystal phase is not observed in the XRD diffraction pattern, it can be said that the skeleton of the monolith is a single phase of the crystal phase.
- XRD X-ray diffraction
- the macropore structure for example, diameter and shape
- Mesopores that were present in the monolith dioxide may be lost.
- oxygen-deficient monolith obtained by the method for producing an oxygen-deficient monolith of the present invention can be used for various applications depending on the structure of the skeleton and macropores of the precursor monolith dioxide. Focusing on electron conductivity and high fluid permeability, catalytic properties and handling strength derived from the co-continuous structure of the skeleton and macropores, oxygen-deficient monoliths, for example, have battery functional electrodes and functional thin films on the surface. It can be used for an electrode such as an electrode for a gas sensor or a reactive electrode provided. By using it as an electrode, various electrochemical reactions, for example, oxidation, reduction, synthesis and the like of organic and inorganic compounds can proceed.
- oxygen-deficient titanium oxide is a wide-gap semiconductor that absorbs visible light and ultraviolet light.
- Oxygen-deficient monoliths are photocatalyst materials having water-decomposition or organic substance-decomposition characteristics, solar cells or dye-sensitized cell electrodes.
- the oxygen deficient monolith may be doped with a doping species to give further characteristics. For example, when ferroelectricity is imparted by cation doping, use of the oxygen deficient monolith in an electronic device can be considered. It can also be used as a catalyst support.
- the method for producing an oxygen-deficient monolith of the present invention can include optional steps other than those described as long as an oxygen-deficient monolith is obtained.
- the optional step is, for example, a step in which particles (typically metal particles and / or carbon particles) are arranged in the skeleton of the macroporous monolith and / or on the surface of the skeleton (that is, the wall surface of the macropore). .
- An oxygen-deficient monolith in which particles are arranged in the framework and / or on the surface of the framework is expected to exhibit characteristics derived from the arranged particles.
- metal particles are arranged, depending on the type, for example, an oxygen-deficient monolith showing catalytic properties derived from the metal particles can be obtained.
- Oxygen deficient monoliths that exhibit catalytic properties can be used, for example, in reactive electrodes.
- an oxygen-deficient monolith showing a high pore volume and specific surface area based on the carbon particles can be obtained. Even when mesopores in the skeleton are lost due to heat during gas phase reduction, the oxygen-deficient monolith in which the carbon particles are arranged is expected to exhibit a high pore volume and specific surface area.
- the metal is, for example, at least one selected from platinum, gold, palladium, rhodium, ruthenium, silver, copper, nickel, iron and aluminum, and at least one selected from platinum, gold, palladium, rhodium and ruthenium. It may be at least one selected from platinum and palladium.
- the method for arranging particles in the skeleton of the oxygen-deficient monolith and / or on the surface of the skeleton is not limited as long as the production method of the present invention for obtaining an oxygen-deficient monolith by vapor-phase reduction of the monolith dioxide can be carried out.
- Examples of methods are: (1) An oxygen-deficient monolith in which particles are arranged in the skeleton and / or on the surface of the skeleton is obtained by performing the above gas phase reduction on the monolith dioxide having particles arranged in the skeleton and / or on the surface of the skeleton.
- An oxygen-deficient monolith in which particles are arranged in the skeleton and / or on the surface of the skeleton is obtained through the above-mentioned gas phase reduction on the monolith dioxide in which the particle precursor is arranged in the skeleton and / or on the surface of the skeleton.
- the method (1) even when the carbon particles are arranged in the monolith dioxide, the extraction of oxygen from the carbon dioxide monolith skeleton (oxidation of the carbon particles) by the carbon particles is suppressed by the progress of the gas phase reduction. For this reason, a single-phase oxygen-deficient monolith can be obtained.
- the arrangement of the particles in the monolith dioxide is, for example, (a) a method in which a solution containing particles and a monolith dioxide are brought into contact and then dried, and (b) a solution containing a precursor of particles and dioxide.
- the contact between the solution and the monolith is, for example, the impregnation of the monolith into the solution.
- the chemical reduction of (c) can be carried out, for example, by bringing a solution containing a precursor reducing agent into contact with a monolith.
- the reducing agent is, for example, formaldehyde, formic acid, hydrazine.
- the precursor of the particle is, for example, a metal salt for the metal particle, and is, for example, a resin for the carbon particle. Examples of the resin include polyacrylic acid, polyvinyl alcohol, polyvinyl pyrrolidone, and polyacrylonitrile.
- the precursor is preferably dissolved in the solution.
- the precursor of the particles preferably has solubility in a solution in contact with the monolith dioxide.
- the arrangement of the particles in the skeleton (in the mesopores) of the monolith dioxide is more reliable.
- the metal particles can be arranged in the skeleton (mesopores) of the monolith dioxide.
- the arrangement of the particle precursors on the monolith dioxide can be carried out in the same manner as the method (1).
- the formation of the particles from the precursor can be performed simultaneously with the gas phase reduction or after the gas phase reduction as long as the formation of the oxygen-deficient monolith from the monolith dioxide by the gas phase reduction is not inhibited.
- the formation of the particles from the precursor may be carried out in the same manner as in the method (1).
- the arrangement of particles in the obtained oxygen-deficient monolith is, for example, (a) a method in which a solution containing particles and an oxygen-deficient monolith are contacted and then dried, and (b) a precursor of particles.
- metal particles a method of forming particles from a precursor by contacting a solution containing the particle precursor with a monolith dioxide and then chemically reducing the precursor, or (d) the particles are metal particles
- a method of forming metal particles by an electrochemical technique such as electrolytic plating can be performed.
- (A), (b), and (c) are the same as the method of (1).
- the arrangement of the particles in the skeleton of the monolith becomes more reliable.
- the size of the arranged particles is not particularly limited, but is, for example, 2 nm to 1 ⁇ m, preferably 2 nm to 100 nm, and particularly preferably 10 nm or less in the use of a catalyst.
- the oxygen-deficient monolith of the present invention has a co-continuous structure of a skeleton composed of a single-phase (single crystal phase) oxygen-deficient titanium oxide and a macropore, and electron conduction based on the oxygen-deficient titanium oxide. Have sex. As described above, this co-continuous structure has high uniformity of the diameter of macropores and does not have isolated holes.
- the oxygen-deficient titanium oxide is, for example, titanium oxide represented by the formula Ti n O 2n-1 (n is 2, 3, 4 or 6). The degree of electron conductivity depends on the physical properties of the oxygen-deficient titanium oxide itself constituting the skeleton of the monolith.
- the electrical resistivity is, for example, 10 3 ⁇ ⁇ cm or less, and is preferably 10 3 ⁇ ⁇ cm or less at room temperature.
- the oxygen-deficient titanium oxide constituting the skeleton of the monolith for example, 10 2 ⁇ ⁇ cm or less, 10 ⁇ ⁇ cm or less, 1 ⁇ ⁇ cm or less, and further 10 ⁇ 1 ⁇ ⁇ cm or less.
- the oxygen-deficient monolith of the present invention may or may not have mesopores.
- particles such as carbon particles and / or metal particles may be arranged in the skeleton of the monolith (in the mesopores) and / or on the surface of the skeleton (wall surface of the macropores).
- the metal particles and carbon particles are as described above in the description of the method for producing the oxygen-deficient monolith.
- the oxygen-deficient monolith of the present invention can be formed, for example, by the method for producing an oxygen-deficient monolith of the present invention.
- the oxygen-deficient monolith of the present invention can be used for various applications depending on the structure of its skeleton and macropores. Specific examples of applications are as described above in the description of the method for producing an oxygen-deficient monolith of the present invention.
- oxynitride monolith a precursor monodioxide or oxygen deficient monolith and a metal nitride are used.
- the precursor monolith has a co-continuous structure of a skeleton composed of titanium dioxide or oxygen-deficient titanium oxide and macropores. As described above, this co-continuous structure has high uniformity of the diameter of macropores and does not have isolated holes.
- the titanium compound constituting the skeleton of the precursor monolith is changed from titanium dioxide or oxygen-deficient titanium oxide to titanium oxynitride. At this time, the structure as a macroporous monolith is maintained. Thereby, the oxynitride monolith in which the co-continuous structure of the skeleton and the macropores in the precursor monolith is maintained is obtained.
- the uniformity of the macropore diameter is high and there are no isolated pores.
- Such control of macropores cannot be achieved with a compact in which titanium oxynitride powder is agglomerated (bound). Only spaces with random size and shape that are present between the agglomerated powders are observed.
- the oxygen-deficient titanium oxide is as described above in the description of the method for producing the oxygen-deficient monolith of the present invention.
- the crystal system of titanium dioxide constituting the skeleton of the monolith is not limited, and may be an anatase type or a rutile type.
- the precursor monolith may or may not have mesopores.
- the method for forming the precursor monolith dioxide is not particularly limited, and is as described above in the description of the method for producing the oxygen-deficient monolith of the present invention.
- the monolith dioxide can be formed according to the methods disclosed in Patent Documents 1 and 2, or the method disclosed in George Hasegawa et al. These methods can form monolithic dioxide with a high degree of precision and freedom of control of macropores, such as greater uniformity of macropore diameter. That is, by using the monolith dioxide formed by these methods, an oxynitride monolith having high precision and freedom of macropore control, for example, higher uniformity of macropore diameter, can be obtained. With such an oxynitride monolith, for example, precise control of fluid permeability is possible.
- the formation method of the oxygen-deficient monolith that is the precursor is not particularly limited, and can be formed, for example, according to the method for producing an oxygen-deficient monolith of the present invention.
- This method can form an oxygen-deficient monolith with high precision and flexibility in controlling macropores, for example, higher uniformity of macropore diameter. That is, by using an oxygen-deficient monolith formed by the method, an oxynitride monolith having high precision and freedom in controlling macropores, for example, higher uniformity of macropore diameter, can be obtained.
- an oxynitride monolith of the present invention for example, using a monolith dioxide as a precursor monolith, more specifically, a monolith dioxide having a co-continuous structure of a skeleton composed of titanium dioxide and macropores, Alternatively, the metal nitride may be accommodated in a container to perform gas phase reduction.
- the precursor monolith dioxide and oxygen-deficient monolith may be selected according to the skeleton of the oxynitride monolith to be obtained and the structure of the macropores (for example, the average diameter of the macropores and the porosity of the monolith).
- the precursor monolith and the metal nitride are accommodated in a container, the inside of the container is set to a vacuum atmosphere or an inert gas atmosphere, and the monolith and the metal nitride are heated. Then, using the metal nitride as an oxygen getter and a nitrogen supply source, vapor phase reduction is performed in which oxygen atoms are taken from titanium dioxide or oxygen-deficient titanium oxide constituting the skeleton of the precursor monolith and nitrogen atoms are supplied.
- the metal nitride is not limited as long as it can take oxygen atoms from titanium dioxide or oxygen-deficient titanium oxide during vapor phase reduction and supply nitrogen atoms to these titanium compounds.
- the metal nitride is at least one selected from, for example, titanium nitride (TiN), zirconium nitride (ZrN), and hafnium nitride (HfN). Since these nitrides are nitrides of elements belonging to the same group 4 elements as titanium and titanium, the reducing power against titanium dioxide and oxygen-deficient titanium oxide is appropriate, and it is possible to form titanium oxynitride by vapor phase reduction. preferable.
- the metal nitride may be a metal nitride having the same degree of stability (equilibrium oxygen partial pressure) as these nitrides.
- the container is preferably a sealed container that can be sealed after the precursor monolith and the metal oxide are accommodated.
- the vacuum atmosphere and the inert gas atmosphere are as described above in the description of the method for producing an oxygen-deficient monolith of the present invention.
- the pressure of the inert gas atmosphere is not particularly limited as long as the partial pressure of oxygen is very small (for example, 10 ⁇ 1 Pa or less, preferably 4 ⁇ 10 ⁇ 2 Pa or less).
- the vacuum atmosphere or the inert gas atmosphere in the container has already been realized when heating of the precursor monolith and the metal nitride is started.
- a vacuum atmosphere or an inert gas atmosphere in the container is maintained during the gas phase reduction.
- the material constituting the container is as described above in the description of the method for producing the oxygen-deficient monolith of the present invention.
- the metal nitride is in powder form, that is, the powdered metal nitride is contained in a container.
- oxygen released from titanium dioxide or oxygen-deficient titanium oxide by the metal nitride is preferably contained.
- the trapping becomes efficient, and the transfer of nitrogen species from the metal nitride to the gas phase by heating becomes efficient, so that gas phase reduction including nitrogenation can be carried out more stably and reliably.
- the average particle size of the powder is, for example, 0.01 ⁇ m to 100 ⁇ m, and preferably 10 ⁇ m to 100 ⁇ m.
- the amount of the metal nitride relative to the precursor monolith contained in the container varies depending on the type of metal nitride and the heating temperature, but is 2 to 100 parts by weight, for example, with respect to 100 parts by weight of the precursor monolith, and 50 ⁇ 100 parts by weight are preferred.
- the duration of the gas phase reduction depends on the size, shape, porosity and macropore diameter of the precursor monolith, the form of the metal nitride contained in the container, and the heating temperature, but it may be required for more than a day.
- the heating method of the precursor monolith accommodated in the container and the metal nitride is not particularly limited. For example, what is necessary is just to accommodate the whole container which accommodated the precursor monolith and the said metal nitride in the furnace adjusted to heating temperature. It is also possible to heat the furnace with a vacuum.
- the heating temperature of the precursor monolith and the metal nitride is not limited as long as it is a temperature at which gas phase reduction including nitrogenation of the precursor monolith proceeds.
- the specific heating temperature varies depending on the type of metal nitride and the pressure in the container during vapor phase reduction, but when the metal nitride is at least one selected from titanium nitride, zirconium nitride, and hafnium nitride, for example, 950 It is 1000 degreeC or more and 1200 degrees C or less.
- the heating temperature is too low, the gas phase reduction does not proceed stably. If the heating temperature is too high, a single-phase oxynitriding monolith cannot be obtained.
- the metal nitride serves as an oxygen getter and a nitrogen supply source, deprives oxygen atoms from titanium dioxide or oxygen-deficient titanium oxide constituting the precursor monolith, Supply nitrogen atoms.
- the reduction reaction can proceed stably and reliably not only to the outer surface of the monolith but also to the inside of the macropore, and the co-continuous structure of the precursor monolith is maintained (controlled macropores).
- An oxynitride monolith (having the structure) is obtained.
- the obtained oxynitride monolith has electron conductivity based on a skeleton showing a co-continuous structure, that is, titanium oxynitride constituting the continuous skeleton.
- the degree of electron conductivity depends on the physical properties of titanium oxynitride itself constituting the skeleton.
- monolith dioxide is used as a precursor, the color of white monolith dioxide changes to black in oxynitride monolith due to the acquisition of electron conductivity.
- the amount of the metal nitride with respect to the precursor monolith accommodated in the container is within the above-described appropriate range, and the time for the gas phase reduction is sufficiently long, whereby a single-phase acid is obtained.
- An oxynitride monolith having a skeleton composed of titanium nitride can be formed. Note that it is considered that heat during heating also contributes to the formation of a skeleton composed of single-phase titanium oxynitride.
- Whether the skeleton of the obtained oxynitride monolith is composed of single-phase titanium oxynitride depends on the crystal structure analysis using X-ray diffraction (XRD) on the skeleton or the physical property analysis of the skeleton (for example, magnetic properties). Analysis).
- XRD X-ray diffraction
- the macropore structure for example, diameter and shape
- the precursor monolith is heated by the heat during gas phase reduction.
- Mesopores that existed in may be lost.
- Titanium oxynitride is a wide gap semiconductor that absorbs visible light and ultraviolet light, like oxygen-deficient titanium oxide, and can be provided with ferroelectricity by cation doping.
- the method for producing an oxynitride monolith of the present invention can include optional steps other than those described as long as an oxynitride monolith is obtained.
- the optional step is, for example, a step of placing particles (typically metal particles and / or carbon particles) in the macroporous monolith skeleton and / or on the surface of the skeleton.
- particles typically metal particles and / or carbon particles
- the precursor monolith and the resulting monolith differ between the method for producing the oxygen-deficient monolith and the method for producing the oxynitride monolith, the precursors in the above-described method examples (1), (2) and (3) Monoliths are interpreted as “monolithic dioxide or oxygen deficient monoliths”, and the resulting monolith is interpreted as “the resulting oxynitriding monolith”.
- the oxynitride monolith of the present invention has a co-continuous structure of a skeleton composed of titanium oxynitride and a macropore, and has electronic conductivity based on titanium oxynitride. As described above, this co-continuous structure has high uniformity of the diameter of macropores and does not have isolated holes. The degree of electron conductivity depends on the physical properties of titanium oxynitride itself constituting the skeleton of the monolith.
- the skeleton of the oxynitride monolith of the present invention may be composed of a single-phase (single crystal phase) titanium oxynitride.
- the oxynitride monolith of the present invention may or may not have mesopores.
- particles such as carbon particles and / or metal particles may be arranged in the skeleton of the monolith (in the mesopores) and / or on the surface of the skeleton (wall surface of the macropores).
- the metal particles and carbon particles are as described above in the description of the method for producing the oxygen-deficient monolith.
- the oxynitride monolith of the present invention can be formed, for example, by the production method of the oxynitride monolith of the present invention.
- the oxynitride monolith of the present invention can be used for various applications depending on the structure of its skeleton and macropores.
- the example of a specific use is the same as that of the oxygen deficient monolith of this invention.
- nitride monolith a precursor monolith dioxide, oxygen deficient monolith or oxynitride monolith, and ammonia are used.
- Monolithic dioxide a kind of precursor, has a co-continuous structure of a skeleton composed of titanium dioxide and macropores.
- An oxygen-deficient monolith that is another kind of precursor has a co-continuous structure of a skeleton composed of oxygen-deficient titanium oxide and macropores.
- Oxynitride monolith which is still another kind of precursor has a co-continuous structure of a skeleton composed of titanium oxynitride and macropores. As described above, these co-continuous structures have high uniformity in the diameter of macropores and do not have isolated holes.
- the oxygen-deficient titanium oxide is as described above in the description of the method for producing the oxygen-deficient monolith of the present invention.
- the titanium compound constituting the skeleton of the precursor monolith is changed from titanium dioxide, oxygen-deficient titanium oxide or titanium oxynitride to titanium nitride.
- the structure as a macroporous monolith is maintained.
- the nitride monolith in which the co-continuous structure of the skeleton and the macropores in the precursor monolith is maintained can be obtained. That is, in the obtained co-continuous structure of the mononitride nitride, the uniformity of the macropore diameter is high and there are no isolated pores.
- Such a control of macropores cannot be achieved with a compact in which titanium nitride powder is agglomerated (bound). Only spaces with random size and shape that are present between the agglomerated powders are observed.
- the crystal system of titanium dioxide constituting the skeleton of the monolith is not limited, and may be an anatase type or a rutile type.
- the precursor monolith may or may not have mesopores.
- the method for forming the precursor monolith dioxide is not particularly limited, and is as described above in the description of the method for producing the oxygen-deficient monolith of the present invention.
- the monolith dioxide can be formed according to the methods disclosed in Patent Documents 1 and 2, or the method disclosed in George Hasegawa et al. These methods can form monolithic dioxide with a high degree of precision and freedom of control of macropores, such as greater uniformity of macropore diameter. That is, by using the monolith dioxide formed by these methods, a nitrided monolith with high precision and freedom of macropore control, for example, higher uniformity of macropore diameter, can be obtained. Such a nitriding monolith allows, for example, precise control of fluid permeability.
- the formation method of the oxygen-deficient monolith that is the precursor is not particularly limited, and can be formed, for example, according to the method for producing an oxygen-deficient monolith of the present invention.
- the method for forming the precursor oxynitride monolith is not particularly limited, and can be formed, for example, according to the method for producing an oxynitride monolith of the present invention.
- These methods can form oxygen deficient monoliths or oxynitride monoliths with high precision and flexibility in macropore control, for example, greater macropore diameter uniformity. That is, by using the oxygen-deficient monolith or oxynitride monolith formed by this method, a nitriding monolith with high precision and freedom in controlling macropores, for example, higher uniformity in macropore diameter, can be obtained.
- a monolith dioxide as a precursor monolith for example, a monolith dioxide as a precursor monolith, more specifically, a monolith having a co-continuous structure of a skeleton composed of titanium dioxide and macropores, and ammonia are included. You may heat-process in the atmosphere above the thermal decomposition temperature of ammonia.
- the precursor monolith dioxide, oxygen deficient monolith, and oxynitride monolith may be selected according to the skeleton of the monolithic nitride to be obtained and the structure of the macropores (for example, the average diameter of the macropores and the porosity of the monolith).
- the precursor monolith is heat-treated at a temperature equal to or higher than the thermal decomposition temperature of ammonia in an atmosphere containing ammonia.
- oxygen atoms are removed from titanium dioxide, oxygen-deficient titanium oxide or titanium oxynitride constituting the skeleton of the precursor monolith, and nitrogen is removed. Perform gas phase reduction to supply atoms.
- the atmosphere for heat-treating the precursor monolith may be an atmosphere containing ammonia, for example, an ammonia atmosphere.
- the partial pressure of oxygen in the atmosphere is preferably very small (for example, 10 ⁇ 1 Pa or less, preferably 4 ⁇ 10 ⁇ 2 Pa or less).
- the pressure of the atmosphere is not particularly limited.
- the ammonia atmosphere can be realized, for example, by storing the precursor monolith in a container and introducing ammonia into the container and sealing it, or by continuously introducing ammonia into the container. Known equipment and techniques can be applied to the introduction of ammonia into the container and the adjustment of the atmosphere in the container.
- the material constituting the container is as described above in the description of the method for producing the oxygen-deficient monolith of the present invention.
- the heat treatment temperature is equal to or higher than the thermal decomposition temperature (400 to 500 ° C.) of ammonia, for example, 600 ° C. or higher.
- ammonia is caused to function not only as an oxygen getter but also as a supply source of nitrogen atoms by utilizing generation of reactive hydrogen and reactive nitrogen by thermal decomposition of ammonia.
- the heat treatment temperature is preferably 1000 ° C. or higher.
- the method of the heat treatment is not particularly limited, and for example, a vessel in which the precursor monolith is accommodated and ammonia is sealed or ammonia is continuously flowed may be accommodated in a furnace adjusted to the heat treatment temperature.
- the heat treatment time (gas phase reduction time) varies depending on the size and shape of the precursor monolith, the porosity, the diameter of the macropores, and the heat treatment temperature, but may require several hours to one day or more.
- ammonia thermally decomposed by heat of heat treatment becomes an oxygen getter and a nitrogen supply source, and oxygen atoms from titanium dioxide, oxygen deficient titanium oxide or titanium oxynitride constituting the precursor monolith. And supplying nitrogen atoms to these titanium compounds.
- the reduction reaction can proceed stably and reliably not only to the outer surface of the monolith but also to the inside of the macropore, and the co-continuous structure of the precursor monolith is maintained (controlled macropores).
- a monolithic nitride (having the structure) is obtained.
- Titanium nitride is a material that has a very high melting point and hardness and is difficult to be molded and finely processed.
- a skeleton composed of such a material that is difficult to be formed and finely processed is used.
- the macroporous monolith can be produced relatively easily.
- the obtained monolithic nitride has electron conductivity based on a skeleton showing a co-continuous structure, that is, titanium nitride constituting the continuous skeleton.
- the degree of electron conductivity depends on the physical properties of titanium nitride itself constituting the skeleton.
- monolith dioxide is used as a precursor, the color of monolith dioxide that has been white changes to brown in the nitride monolith due to the acquisition of electron conductivity.
- the macropore structure for example, diameter and shape
- the macropore structure for example, diameter and shape
- the mesopores that had been lost may be lost.
- mesopores that were not present in the precursor monolith may appear in the nitride monolith, such as when Ti 2 O 3 reacts with ammonia.
- the nitrided monolith obtained by the method for producing a nitrided monolith of the present invention can be used for various applications depending on the structure of the precursor monolith and the structure of the macropores. Specific examples of applications are the same as those described above in the description of the method for producing an oxygen-deficient monolith of the present invention.
- Titanium nitride is expected to be used as a capacitor, a catalyst (cis-alkene formation by adding hydrogen to alkyne), and a catalyst carrier (methanol oxidation), and is also a superconductor having a transition temperature of about 5K.
- the method for producing a monolithic nitride according to the present invention can include optional steps other than those described as long as a monolithic nitride can be obtained.
- the optional step is, for example, a step of placing particles (typically metal particles and / or carbon particles) in the macroporous monolith skeleton and / or on the surface of the skeleton.
- particles typically metal particles and / or carbon particles
- the precursor monolith and the obtained monolith are different between the method for producing an oxygen-deficient monolith and the method for producing a nitrided monolith
- the precursor monolith in Examples (1), (2) and (3) described above Is interpreted as “a monolith dioxide, an oxygen deficient monolith or an oxynitride monolith” and the resulting monolith is interpreted as “the resulting nitridation monolith”.
- the monolithic nitride of the present invention has a co-continuous structure of a skeleton composed of titanium nitride and macropores, and has electronic conductivity based on titanium nitride. As described above, this co-continuous structure has high uniformity of the diameter of macropores and does not have isolated holes. The degree of electron conductivity depends on the physical properties of titanium nitride itself constituting the skeleton of the monolith.
- the skeleton of the monolithic nitride of the present invention may be composed of single-phase (single crystal layer) titanium nitride.
- the nitrided monolith of the present invention may or may not have mesopores.
- particles such as carbon particles and / or metal particles may be arranged in the skeleton of the monolith (in the mesopores) and / or on the surface of the skeleton (wall surface of the macropores).
- the metal particles and carbon particles are as described above in the description of the method for producing the oxygen-deficient monolith.
- the nitrided monolith of the present invention can be formed, for example, by the method for producing a nitrided monolith of the present invention.
- the nitrided monolith of the present invention can be used for various applications depending on the structure of its skeleton and macropores.
- the example of a specific use is the same as that of the oxygen deficient monolith of this invention.
- the precursor monolith dioxide was made according to the method disclosed in George Hasegawa et al. Specifically, it was produced by the following procedure.
- the temperature of the container was raised to 60 ° C., the solvent was replaced with ethanol, and the mixture was allowed to stand for 8 hours or more, and then the solvent was successively replaced with five mixed solutions of ethanol and water having different mixing ratios.
- the interval between solvent substitutions was 8 hours or more.
- the solvent was replaced with water and allowed to stand at 60 ° C. for 24 hours, and then dried at 40 ° C. for 48 hours to obtain a dry gel.
- the obtained dried gel was baked at 600 ° C. to remove residual organic substances, and Monolith A having a skeleton composed of titanium dioxide was obtained.
- the observation image of the obtained monolith dioxide A by scanning electron microscope (SEM) is shown in FIG. 1, the pore distribution measurement result by mercury intrusion method is shown in FIG. 2, the XRD diffraction peak of the material constituting the skeleton is shown in FIG. Each is shown. What is shown as “TiO 2 ” in FIGS. 2 and 3 is the result for the monolith A dioxide.
- the broken line is the theoretical diffraction peak of each titanium oxide, and the solid line is the diffraction peak actually measured for each of the monolithic dioxide A and each oxygen-deficient monolith prepared in Example 1.
- the monolith A was a macroporous monolith having a co-continuous structure of a skeleton composed of anatase-type titanium dioxide and macropores. Moreover, from the result shown in FIG. 2, it was confirmed that the uniformity of the diameter of the macropore in the monolith dioxide A is high.
- the pore distribution of monoliths including Monolith A and the subsequent monoliths is 0.05 to 50 ⁇ m using a pore distribution measuring device (Quantachrome® Instruments, Pore® Master® 60-GT) unless otherwise specified. Range was measured.
- the XRD diffraction peak for materials constituting the skeleton of the monolith produced from then on, such as the monolith A is 10 to 60 degrees with a wide angle X-ray diffractometer (D8 Advance, manufactured by Bruker) at a diffraction angle 2 ⁇ . Range was measured. At that time, after the skeleton of the monolith was pulverized into powder, the obtained powder was filled in a cell for a powder sample, and X-ray diffraction measurement was performed by a reflection method.
- Example 1 Production of oxygen-deficient monolith
- An oxygen-deficient monolith was produced from the dioxide monolith A produced as described above. Specifically, it was produced by the following procedure.
- Monolith dioxide A and zirconium foil (average thickness 100 ⁇ m) were accommodated in a quartz tube, and the quartz tube was sealed.
- the amount of the zirconium foil accommodated in the quartz tube was 5 to 10% by weight in excess of the stoichiometric amount by which titanium dioxide constituting the monolithic skeleton was reduced to oxygen-deficient titanium oxide.
- Four types of samples with different amounts of zirconium foil were prepared for the purpose of forming four types of oxygen-deficient titanium oxide (Ti 2 O 3 , Ti 3 O 5 , Ti 4 O 7 and Ti 6 O 11 ) skeletons. did.
- the inside of the quartz tube was evacuated at a pressure of 4 ⁇ 10 ⁇ 2 Pa, and thereafter, the quartz tube was sealed to prevent gas from entering and exiting the quartz tube.
- the whole container is put into an electric furnace, and the temperature of the furnace is increased at a heating rate of 100 ° C. per hour, from 1050 ° C. (during the production of Ti 4 O 7 and Ti 6 O 11 monolith) to 1150 ° C. (Ti 2 O 3 And at the time of preparation of the Ti 3 O 5 monolith)
- the heat treatment was performed at ° C for 24 hours.
- FIG. 4 The SEM observation images of the four types of monoliths thus prepared are shown in FIG. 4, the pore distribution measurement results by mercury intrusion method are shown in FIG. 2, and the XRD diffraction peaks of the materials constituting the skeleton are shown in FIG. Show. What is indicated as “Ti 2 O 3 ” or the like in FIGS. 2 and 3 is the result for each oxygen-deficient monolith produced in Example 1.
- the obtained four types of monoliths are each composed of four types of oxygen-deficient titanium oxides (Ti 2 O 3 , Ti 3 O 5 , Ti 4 O 7 and Ti 6 O 11 ). It had a skeleton. In addition, since the diffraction peak is sharp and is detected at almost the same position as the theoretical diffraction angle 2 ⁇ , and diffraction peaks based on other crystal phases were not observed, single-phase oxygen-deficient titanium oxide From this, it was confirmed that the skeleton was composed. From the results shown in FIGS. 2 and 4, each of the four types of monoliths obtained is a macroporous monolith having a co-continuous structure of a skeleton and macropores, including a high uniformity of macropore diameter. It was confirmed that the structure of monolith A as a body was maintained.
- the monolith has a metallic behavior that the electrical resistivity at room temperature is as low as 1.5 ⁇ 10 ⁇ 2 ⁇ ⁇ cm, and the electrical resistivity decreases as the temperature falls from room temperature.
- a metal-semiconductor transition occurred at about 150K. From this, it was confirmed that the produced Ti 4 O 7 monolith has a skeleton composed of single-phase Ti 4 O 7 .
- the graph shown on the right shoulder in FIG. 5 is an enlarged view of the graph shown large.
- the electrical resistivity ⁇ of the monolith was measured by a four-terminal method using a physical property measurement system manufactured by Quantum Design after a part of the obtained monolith was cut out and the cut piece was formed into a rectangular parallelepiped of several millimeters square. .
- FIGS. 6A and 6B The temperature dependence of the electrical resistivity ⁇ for the other three types of monoliths measured in the same manner is shown in FIGS. 6A and 6B together with the temperature dependence of the electrical resistivity ⁇ in the Ti 4 O 7 monolith. .
- the electrical resistivity ⁇ near normal temperature (300K) is 5.6 ⁇ 10 1 ⁇ ⁇ cm for the Ti 2 O 3 monolith and 1 for the Ti 3 O 5 monolith. It was 9 ⁇ 10 0 ⁇ ⁇ cm, and Ti 6 O 11 monolith was 2.3 ⁇ 10 ⁇ 2 ⁇ ⁇ cm.
- the metal-semiconductor transition temperatures of the four types of monoliths produced were evaluated with a superconducting quantum interferometer SQUID (measured by MPMS). This may cause a metal-semiconductor transition at around 130K for Ti 6 O 11 monolith, around 150K for Ti 4 O 7 monolith, around 450K for Ti 3 O 5 monolith, and around 400-600K for Ti 2 O 3 monolith. confirmed. These transition temperatures are almost the same as those conventionally reported for single-phase oxygen-deficient titanium oxides, and each oxygen-deficient monolith is composed of single-phase oxygen-deficient titanium oxides. It was confirmed to have a skeleton.
- Example 2 A monolith dioxide B was obtained according to the method for producing a precursor monolith described above except that the baking temperature of the dried gel was 800 ° C.
- the baking temperature of the dried gel was 800 ° C.
- FIG. 7A shows an XRD diffraction peak of the material constituting the skeleton of the monolith B.
- TiO 2 what is shown as “TiO 2 ” is the result for monolith B2.
- the lower broken line of the two broken lines is the theoretical diffraction peak of rutile TiO 2
- the solid line is actually the monolith B2 and the oxygen-deficient monolith obtained by gas phase reduction of the monolith. It is a measured diffraction peak.
- the monolith B2 is a macroporous monolith having a co-continuous structure of a skeleton composed of rutile-type titanium dioxide and macropores. It was confirmed that the uniformity of the diameter was high.
- an oxygen-deficient monolith was produced from the monooxide B produced as described above.
- zirconium foil Four types of samples R1 to R4 having the same amount as in Example 1 were prepared, and gas phase reduction was performed using a quartz tube.
- R1, R2, R3, and R4 are samples aimed at forming Ti 6 O 11 , Ti 4 O 7 , Ti 3 O 5, and Ti 2 O 3 skeletons, respectively.
- these monoliths were macroporous monoliths having a co-continuous structure of skeleton and macropores. It was confirmed that the structure of the monolith dioxide B as a precursor was maintained, including high uniformity of the diameter of the macropores.
- FIG. 7A the diffraction peaks by XRD of the materials constituting the skeleton of the four types of monoliths thus produced are shown in FIG. 7A. What is indicated as “R1” in FIG. 7A is the result for each oxygen-deficient monolith prepared in Example 2.
- R2 was a sample for the purpose of forming a Ti 4 O 7 skeleton, but formation of Ti 4 O 7 was slight and the diffraction peak of Ti 3 O 5 was dominant.
- R1 was a sample for the purpose of forming a Ti 6 O 11 skeleton, and was composed of four types of oxygen-deficient titanium oxides as shown in FIG. 7B in which the range of 20 to 30 degrees was enlarged with a diffraction angle 2 ⁇ . Had a skeleton.
- Example 3 Production of monolithic oxynitride
- An oxynitride monolith was produced from the monolith dioxide A produced as described above. Specifically, it was produced by the following procedure.
- Monolith A and zirconium nitride powder (average particle size 100 ⁇ m) were placed in a quartz tube, and the quartz tube was sealed.
- the amount of zirconium nitride powder sealed in the quartz tube was 50 parts by weight with respect to 100 parts by weight of titanium dioxide.
- the inside of the quartz tube was evacuated at a pressure of 4 ⁇ 10 ⁇ 2 Pa, and thereafter, the quartz tube was sealed to prevent gas from entering and exiting the quartz tube.
- the entire container was placed in an electric furnace maintained at 1150 ° C., and heat treatment was performed for 24 hours. After the heat treatment, the quartz tube was taken out of the electric furnace, cooled to room temperature at a temperature lowering rate of 100 ° C. per hour, then the sealing was broken, and the internal monolith was taken out.
- Monolith A which was white before the heat treatment, changed to black after the heat treatment.
- FIG. 8 An observation image of the monolith thus produced by SEM is shown in FIG. 8, and a diffraction peak by XRD of the material constituting the skeleton is shown in FIG. What is shown as “Ti 3 O 4.9 N 0.1 ” in FIG. 9 is the result for the oxynitride monolith produced in Example 3.
- the obtained monolith had a skeleton composed of titanium oxynitride (Ti 3 O 4.9 N 0.1 ). Further, the diffraction peak of the crystal was sharp and detected at almost the same position as the theoretical diffraction angle 2 ⁇ (shown by a broken line in FIG. 9), and diffraction peaks based on other crystal phases were not observed. From this, it was confirmed that the skeleton was composed of single-phase Ti 3 O 4.9 N 0.1 . From the results shown in FIG. 8, it was confirmed that the obtained monolith was a porous monolith having a co-continuous structure of a skeleton and a macropore. Further, considering the situation of the skeleton and macropores shown in FIG. 8 and the result of Example 1 together, the obtained monolith includes the monolith A which is a precursor, including high uniformity of the macropore diameter. It is presumed that the structure of is maintained.
- Example 4 Preparation of nitride monolith
- a monolithic nitride was produced from the monolith A dioxide produced as described above. Specifically, it was produced by the following procedure.
- Monolith dioxide A was accommodated in a quartz tube having an internal volume of 4.5 ⁇ 10 5 mL to which a tube for injecting ammonia was connected.
- the whole vessel was placed in an electric furnace maintained at 1000 ° C. while ammonia was allowed to flow inside the quartz tube at a flow rate of 200 mL / min, and heat treatment was performed for 24 hours.
- the quartz tube was taken out of the electric furnace, cooled to room temperature at a temperature drop rate of 100 ° C. per hour, and then the monolith inside the quartz tube was taken out.
- Monolith A which was white before heat treatment, changed to brown after heat treatment.
- FIG. 10 shows an observation image of the monolith thus produced by SEM
- FIG. 9 shows the diffraction peak by XRD of the material constituting the skeleton. What is shown as “TiN” in FIG. 9 is the result for the nitrided monolith fabricated in Example 4.
- the obtained monolith had a skeleton composed of titanium nitride (TiN). Further, the diffraction peak of the crystal was sharp and detected at almost the same position as the theoretical diffraction angle 2 ⁇ (shown by a broken line in FIG. 9), and diffraction peaks based on other crystal phases were not observed. From this, it was confirmed that the skeleton was composed of single-phase TiN. From the results shown in FIG. 10, it was confirmed that the obtained monolith was a porous monolith having a co-continuous structure of a skeleton and macropores. Further, considering the situation of the skeleton and macropores shown in FIG. 10 together with the result of Example 1, the obtained monolith includes a monolith A which is a precursor including high uniformity of the macropore diameter. It is presumed that the structure of is maintained.
- a monolith A which is a precursor including high uniformity of the macropore diameter. It is presumed that the structure of is maintained.
- Oxygen-deficient monoliths in which carbon particles are arranged in the skeleton and on the surface of the skeleton were prepared from carbon dioxide monoliths arranged in the skeleton and on the surface of the skeleton. Specifically, it was produced by the following procedure.
- a wet gel was obtained according to the production method of monolith dioxide A.
- the resulting gel was subjected to solvent replacement and standing in water at 60 ° C. for 24 hours in the same manner as in the production of monolithic dioxide A, and then the gel was treated with an aqueous solution of polyacrylic acid which is a precursor of carbon particles. It was immersed in (concentration 10% by weight) and then dried at 40 ° C. for 48 hours to obtain a dried gel. Next, the obtained dried gel was baked at 600 ° C. for 2 hours in a nitrogen stream (flow rate: 1 L / min) to have a skeleton composed of titanium dioxide, and carbon particles were present in the skeleton and on the surface of the skeleton. Arranged monolithic dioxide C was obtained.
- FIG. 11 An observation image of the obtained monolith dioxide C by SEM is shown in FIG. 11, a nitrogen adsorption / desorption isotherm measurement result by the nitrogen adsorption / desorption measurement method is shown in FIG. 12, and a pore distribution measurement result by the measurement method is shown in FIG.
- FIGS. 11-13 what is indicated as “TiO 2 —C” is the result for monolith C2.
- FIGS. 12 and 13 what is indicated as “TiO 2 ” is the result for the monolith A dioxide.
- the nitrogen adsorption / desorption measurement in Example 5 was performed using a nitrogen adsorption / desorption measuring device (BELSORP-mini II, manufactured by Nippon Bell Co., Ltd.).
- the monolith C2 was a macroporous monolith having a co-continuous structure of a skeleton composed of titanium dioxide and macropores, like the monolith A. From the results shown in FIGS. 12 and 13, it was confirmed that the monolith C2 has increased micropores and mesopores compared to the monolith A. The increase in micropores is confirmed by the fact that the adsorption volume Va increases in the region where the relative pressure p / p0 is small in the graph shown in FIG. These increases were estimated to be due to the carbon particles, and it was confirmed that the carbon particles were arranged in the monolith C. More specifically, it is estimated that the increase in micropores is due to the pores of the carbon particles themselves.
- mesopores it is estimated that by arranging carbon particles in the skeleton, the size of the crystal grains of the titanium compound changed due to physical obstacles, and mesopores corresponding to voids between the crystal grains increased.
- polyvinylpyrrolidone was used instead of polyacrylic acid as a precursor, a similar monolithic dioxide C could be produced.
- an oxygen-deficient monolith in which a skeleton was composed of Ti 4 O 7 and carbon particles were arranged in the skeleton and on the surface of the skeleton was produced from the monolithic dioxide C produced as described above. Specifically, it was produced by the following procedure.
- Monolith dioxide C and zirconium foil (average thickness 100 ⁇ m) were accommodated in a quartz tube, and the quartz tube was sealed.
- the amount of the zirconium foil accommodated in the quartz tube was an excess amount of 10% by weight of the stoichiometric ratio of reducing the titanium dioxide constituting the monolithic skeleton to change to Ti 4 O 7 .
- the inside of the quartz tube was evacuated at a pressure of 4 ⁇ 10 ⁇ 2 Pa, and thereafter, the quartz tube was sealed to prevent gas from entering and exiting the quartz tube.
- the entire container was placed in an electric furnace, the furnace was heated at a heating rate of 100 ° C. per hour, and heat treatment was performed at 1050 ° C. for 24 hours.
- the temperature inside the furnace is cooled to room temperature at a rate of temperature decrease of 100 ° C., then the quartz tube is taken out from the electric furnace, waits for the quartz tube to cool naturally, breaks the seal, and the internal monolith is removed. I took it out.
- FIG. 11 The SEM observation image of the Ti 4 O 7 monolith thus produced is shown in FIG. 11, and the nitrogen adsorption / desorption isotherm and pore distribution measurement results by the nitrogen adsorption / desorption measurement method are shown in FIGS. 12 and 13, respectively.
- FIGS. 11-13 what is shown as “Ti 4 O 7 —C” is the result for a Ti 4 O 7 monolith made from the monolith C2 dioxide.
- FIGS. 12 and 13 what is indicated as “Ti 4 O 7 ” is the result for the Ti 4 O 7 monolith prepared in Example 1. It was confirmed separately by XRD measurement similar to Example 1 that the skeleton of the oxygen-deficient monolith prepared in Example 5 was composed of Ti 4 O 7 .
- the obtained Ti 4 O 7 monolith is a macroporous monolith having a co-continuous structure of a skeleton and macropores, and is a precursor including high uniformity of macropore diameters. It was confirmed that the structure of monolith C was maintained. Note that fine irregularities are observed on the surface of the skeleton of the Ti 4 O 7 monolith in FIG. 11. This is because the growth of Ti 4 O 7 crystals is physically hindered by the presence of carbon particles, and adjacent crystal grains are It is presumed that each crystal grain was observed on the surface without fusing. As shown in FIGS.
- thermogravimetric (TG) measurement result with respect to the produced carbon-arranged Ti 4 O 7 monolith is shown in FIG.
- TG measurement a differential type differential thermal balance (Thermo Plus EVO TG8120, manufactured by Rigaku Corporation) is used on a sample (weight 1.86 mg) obtained by pulverizing a monolith to be measured with a mortar, and an air flow of 100 mL / The measurement was performed under the measurement conditions of 5 minutes / minute and a heating rate of 5 ° C./minute.
- the weight loss up to a temperature of 100 ° C. is derived from the evaporation of water adsorbed on the monolith, and the weight loss from 100 ° C. to 400 ° C.
- the amount of carbon particles in the monolith estimated from this TG curve was approximately 9% by weight of the total weight of the monolith.
- Figure 15 shows the measurement results of Raman spectroscopic analysis of carbon arranged Ti 4 O 7 monoliths prepared.
- Raman spectroscopy was performed using a Raman microscope (XploRA, manufactured by Horiba, Ltd.) under measurement conditions of a laser wavelength of 532 nm, a filter of 1%, a grid of 2400T, an exposure time of 2 seconds, and an integration count of 20 times.
- the wave number 1340cm carbon around -1 D band (sp 3 carbon) and a wavenumber 1600cm carbon G band around -1 (sp 2 carbon) is measured, the carbon to Ti 4 O 7 monoliths The arrangement of was confirmed.
- Example 6 considering the use of the macroporous monolith as an electrode, the electrochemical stability of the monolith and the specific application of the monolith as an electrode were confirmed.
- the electrochemical characteristics of an electrode composed of a macroporous monolith (hereinafter referred to as a monolith electrode) were evaluated using a potentiostat / galvanostat (manufactured by Hokuto Denko, HSV-110) and a triode cell. did.
- the Ti 4 O 7 monolith prepared in Example 1 was prepared as an evaluation target.
- a cyclic voltammogram (CV) of the monolith electrode in a sulfuric acid electrolyte solution (concentration: 0.1 mol / L) is shown in FIGS.
- Evaluation of CV was carried out using a Ti 4 O 7 monolith electrode disposed on the working electrode, a platinum wire as the counter electrode, and an Ag / AgCl reference electrode (manufactured by ALS) as the reference electrode.
- FIG. 16 it was confirmed that the Ti 4 O 7 monolith electrode showed high hydrogen overvoltage and oxygen overvoltage and had a wide potential window in the sulfuric acid electrolyte.
- FIG. 16 it was confirmed that the Ti 4 O 7 monolith electrode showed high hydrogen overvoltage and oxygen overvoltage and had a wide potential window in the sulfuric acid electrolyte.
- FIG. 18 shows an SEM observation image of the monolith electrode after electroplating. As shown in FIG. 18, it was confirmed that an infinite number of platinum particles having a diameter of about several hundred nanometers were supported on the surface of the monolith skeleton.
- FIG. 19 shows a CV curve of a Ti 4 O 7 monolith electrode carrying platinum particles in a sulfuric acid electrolyte (concentration: 0.1 mol / L). Evaluation of CV was carried out in a tripolar cell using a platinum-supported monolith electrode disposed on the working electrode, a platinum wire as the counter electrode, and an Ag / AgCl reference electrode (manufactured by ALS) as the reference electrode. The cut-off potential was ⁇ 0.7V to 2.0V. As shown in FIG. 19, due to the catalytic action of platinum particles supported on the monolith, the current resulting from the generation of oxygen at a potential of about 1.5 V or more is caused by the generation of hydrogen at a potential of about ⁇ 0.3 V or less. It was confirmed that the current to flow through.
- FIG. 20 shows a linear sweep voltammetry (LSV) curve in a methanolic sulfuric acid aqueous solution (methanol concentration: 1.0 mol / L, sulfuric acid concentration: 0.1 mol / L) of a Ti 4 O 7 monolith electrode on which platinum is supported.
- LSV linear sweep voltammetry
- Evaluation of LSV was carried out in a tripolar cell using a platinum-supported monolith electrode disposed on the working electrode, a platinum wire as the counter electrode, and an Ag / AgCl reference electrode (manufactured by ALS) as the reference electrode. Scanning was from 0.40V to 1.30V.
- a comparison experiment using Ti 4 O 7 monolith before supporting platinum as a reference electrode was also performed. The evaluation results are shown in FIG. In FIG. 20, the solid line shows the LSV curve of the platinum-supporting monolith electrode, and the dotted line shows the LSV curve of the monolith electrode not supporting platinum particles.
- the current due to the oxidation of methanol could not be clearly confirmed in the monolith electrode before platinum support, whereas the oxidation of methanol at a potential of 0.90 V or more in the platinum support monolith electrode. It was confirmed that the current value increased due to.
- the catalyst can be applied to various applications including the reactive electrode by arranging the catalyst in the monolith.
- the macroporous titanium compound monolith formed by the production method of the present invention can be widely used for electrochemical elements such as battery electrodes and gas sensor electrodes, catalysts such as photocatalysts, and electronic devices.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Organic Chemistry (AREA)
- Ceramic Engineering (AREA)
- Materials Engineering (AREA)
- Structural Engineering (AREA)
- Inorganic Chemistry (AREA)
- Nanotechnology (AREA)
- Physics & Mathematics (AREA)
- Manufacturing & Machinery (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Environmental & Geological Engineering (AREA)
- Life Sciences & Earth Sciences (AREA)
- Geology (AREA)
- General Life Sciences & Earth Sciences (AREA)
- Thermal Sciences (AREA)
- Composite Materials (AREA)
- Dispersion Chemistry (AREA)
- Crystallography & Structural Chemistry (AREA)
- Condensed Matter Physics & Semiconductors (AREA)
- General Physics & Mathematics (AREA)
- Electrochemistry (AREA)
- Metallurgy (AREA)
- Catalysts (AREA)
- Porous Artificial Stone Or Porous Ceramic Products (AREA)
- Inorganic Compounds Of Heavy Metals (AREA)
Abstract
Description
本発明のマクロ多孔性酸素欠損型酸化チタンモノリス(以下、酸素欠損モノリス)の製造方法では、前駆体であるマクロ多孔性二酸化チタンモノリス(以下、二酸化モノリス)と、チタン還元能を有する金属とを使用する。
(1)骨格内および/または骨格の表面に粒子が配置された二酸化モノリスに対して上記気相還元を実施することで、骨格内および/または骨格の表面に粒子が配置された酸素欠損モノリスを得る方法;
(2)骨格内および/または骨格の表面に粒子前駆体が配置された二酸化モノリスに対する上記気相還元の実施を経て、骨格内および/または骨格の表面に粒子が配置された酸素欠損モノリスを得る方法;および
(3)二酸化モノリスに対する上記気相還元の実施により酸素欠損モノリスを得た後に、得られた酸素欠損モノリスの骨格内および/または骨格の表面に粒子を配置する方法;を含む。(1)、(2)、(3)のいずれの方法も、カーボン粒子の配置および金属粒子の配置に適用できる。(1)の方法において、二酸化モノリス内にカーボン粒子を配置した場合においても、上記気相還元の進行により、カーボン粒子による二酸化モノリス骨格からの酸素の引き抜き(カーボン粒子の酸化)が抑えられる。このため、単相の酸素欠損モノリスを得ることができる。
本発明の酸素欠損モノリスは、単相の(単一の結晶相)の酸素欠損型酸化チタンから構成される骨格とマクロ孔との共連続構造を有し、酸素欠損型酸化チタンに基づく電子伝導性を有する。この共連続構造は、上述のように、マクロ孔の直径の均一性が高く、孤立孔を有さない。酸素欠損型酸化チタンは、例えば、式TinO2n-1(nは2,3,4または6)により示される酸化チタンである。電子伝導性の程度は、当該モノリスの骨格を構成する酸素欠損型酸化チタン自体の物性による。電気抵抗率は、例えば103Ω・cm以下であり、常温において103Ω・cm以下であることが好ましく、当該モノリスの骨格を構成する酸素欠損型酸化チタンの組成および温度域によっては、例えば102Ω・cm以下、10Ω・cm以下、1Ω・cm以下、さらには10-1Ω・cm以下となる。
本発明のマクロ多孔性酸窒化チタンモノリス(以下、酸窒化モノリス)の製造方法では、前駆体である二酸化モノリスまたは酸素欠損モノリスと、金属窒化物とを使用する。
本発明の酸窒化モノリスは、酸窒化チタンから構成される骨格とマクロ孔との共連続構造を有し、酸窒化チタンに基づく電子伝導性を有する。この共連続構造は、上述のように、マクロ孔の直径の均一性が高く、孤立孔を有さない。電子伝導性の程度は、当該モノリスの骨格を構成する酸窒化チタン自体の物性による。
本発明のマクロ多孔性窒化チタンモノリス(以下、窒化モノリス)の製造方法では、前駆体である二酸化モノリス、酸素欠損モノリスまたは酸窒化モノリスと、アンモニアとを使用する。
本発明の窒化モノリスは、窒化チタンから構成される骨格とマクロ孔との共連続構造を有し、窒化チタンに基づく電子伝導性を有する。この共連続構造は、上述のように、マクロ孔の直径の均一性が高く、孤立孔を有さない。電子伝導性の程度は、当該モノリスの骨格を構成する窒化チタン自体の物性による。
前駆体である二酸化モノリスを、George Hasegawa et al.文献に開示の方法に従って作製した。具体的には、以下の手順で作製した。
上記のように作製した二酸化モノリスAから酸素欠損モノリスを作製した。具体的には、以下の手順で作製した。
乾燥ゲルの焼成温度を800℃とした以外は上述した前駆体モノリスの作製方法に従って、二酸化モノリスBを得た。この二酸化モノリスBに対して、SEMによる観察、水銀圧入法による細孔分布測定、および骨格を構成する材料のXRD回折ピークの評価を行った。図7Aに、二酸化モノリスBの骨格を構成する材料のXRD回折ピークを示す。図7Aにおいて、「TiO2」と示されているものが、二酸化モノリスBに対する結果である。なお、図7Aにおいて、2つの破線のうち下方の破線はルチル型TiO2の理論上の回折ピーク、実線は二酸化モノリスBおよび当該モノリスを気相還元して得た酸素欠損モノリスに対して実際に測定された回折ピークである。これらの評価結果から、二酸化モノリスBがルチル型二酸化チタンから構成される骨格とマクロ孔との共連続構造を有するマクロ多孔性モノリスであること、二酸化モノリスAと同様に、二酸化モノリスBにおけるマクロ孔の直径の均一性が高いことが確認された。
上記のように作製した二酸化モノリスAから、酸窒化モノリスを作製した。具体的には、以下の手順で作製した。
上記のように作製した二酸化モノリスAから、窒化モノリスを作製した。具体的には、以下の手順で作製した。
カーボン粒子が骨格内および骨格の表面に配置された二酸化モノリスから、カーボン粒子が骨格内および骨格の表面に配置された酸素欠損モノリスを作製した。具体的には、以下の手順で作製した。
実施例6では、マクロ多孔性モノリスの電極としての使用を考慮し、電気化学的な当該モノリスの安定性、および当該モノリスの電極としての具体的な応用を確認した。実施例6における、マクロ多孔性モノリスにより構成される電極(以下、モノリス電極)の電気化学特性は、ポテンショスタット/ガルバノスタット(北斗電工社製、HSV-110)および三極式セルを用いて評価した。
白金粒子を担持させたTi4O7モノリス電極の硫酸電解液(濃度0.1mol/L)中におけるCV曲線を図19に示す。CVの評価は、白金担持モノリス電極を作用極に配置し、対極に白金線を、参照極にAg/AgCl参照電極(ALS社製)をそれぞれ使用して、三極式セルにおいて実施した。カットオフ電位は-0.7Vから2.0Vとした。図19に示すように、モノリスに担持された白金粒子による触媒作用により、およそ1.5V以上の電位で酸素の発生に起因する電流が、およそ-0.3V以下の電位で水素の発生に起因する電流が流れることが確認された。
白金を担持させたTi4O7モノリス電極のメタノール硫酸水溶液(メタノール濃度1.0mol/L、硫酸濃度0.1mol/L)中におけるリニアスイープボルタンメトリー(LSV)曲線を図20に示す。LSVの評価は、白金担持モノリス電極を作用極に配置し、対極に白金線を、参照極にAg/AgCl参照電極(ALS社製)をそれぞれ使用して、三極式セルにおいて実施した。走査は0.40Vから1.30Vまでとした。比較のために、白金担持前のTi4O7モノリスを参照極に使用した対比実験を併せて実施した。評価結果を図20に示す。図20において、実線が白金担持モノリス電極のLSV曲線を示し、点線が白金粒子を担持していないモノリス電極のLSV曲線を示す。
Claims (19)
- 単相の酸素欠損型酸化チタンから構成される骨格とマクロ孔との共連続構造を有し、
前記酸素欠損型酸化チタンに基づく電子伝導性を有するマクロ多孔性チタン化合物モノリス。 - 電気抵抗率が103Ω・cm以下である、請求項1に記載のマクロ多孔性チタン化合物モノリス。
- カーボン粒子および/または金属粒子が、前記骨格内および/または前記骨格の表面に配置されている、請求項1に記載のマクロ多孔性チタン化合物モノリス。
- 電極である、請求項1に記載のマクロ多孔性チタン化合物モノリス。
- 二酸化チタンから構成される骨格とマクロ孔との共連続構造を有するマクロ多孔性二酸化チタンモノリスと、チタン還元能を有する金属と、を容器に収容し、
前記容器内を真空雰囲気または不活性ガス雰囲気とし、
前記モノリスおよび前記金属を加熱することで、前記金属を酸素ゲッターとして、前記モノリスを構成する二酸化チタンから酸素原子を奪う気相還元を行って、
酸素欠損型酸化チタンから構成される骨格と前記マクロ孔との共連続構造を有し、前記酸素欠損型酸化チタンに基づく電子伝導性を有するマクロ多孔性酸素欠損型酸化チタンモノリスを得る、マクロ多孔性チタン化合物モノリスの製造方法。 - 箔状の前記金属を前記容器に収容する請求項5に記載のマクロ多孔性チタン化合物モノリスの製造方法。
- 前記金属がジルコニウム(Zr)およびハフニウム(Hf)から選ばれる少なくとも1種である請求項5に記載のマクロ多孔性チタン化合物モノリスの製造方法。
- 前記加熱の温度が900~1300℃である請求項7に記載のマクロ多孔性チタン化合物モノリスの製造方法。
- 前記マクロ多孔性二酸化チタンモノリスの骨格を構成する二酸化チタンがアナターゼ型である請求項5に記載のマクロ多孔性チタン化合物モノリスの製造方法。
- 酸窒化チタンから構成される骨格とマクロ孔との共連続構造を有し、
前記酸窒化チタンに基づく電子伝導性を有するマクロ多孔性チタン化合物モノリス。 - 二酸化チタンまたは酸素欠損型酸化チタンから構成される骨格とマクロ孔との共連続構造を有するマクロ多孔性チタン化合物モノリスと、金属窒化物と、を容器に収容し、
前記容器内を真空雰囲気または不活性ガス雰囲気とし、
前記モノリスおよび前記金属窒化物を加熱することで、前記金属窒化物を酸素ゲッターおよび窒素供給源として、前記モノリスを構成するチタン化合物から酸素原子を奪うとともに窒素原子を供給する気相還元を行って、
酸窒化チタンから構成される骨格と前記マクロ孔との共連続構造を有し、前記酸窒化チタンに基づく電子伝導性を有するマクロ多孔性酸窒化チタンモノリスを得る、マクロ多孔性チタン化合物モノリスの製造方法。 - 粉末状の前記金属窒化物を前記容器に収容する請求項11に記載のマクロ多孔性チタン化合物モノリスの製造方法。
- 前記金属窒化物が、窒化チタン、窒化ジルコニウムおよび窒化ハフニウムから選ばれる少なくとも1種である請求項11に記載のマクロ多孔性チタン化合物モノリスの製造方法。
- 前記加熱の温度が950~1200℃である請求項13に記載のマクロ多孔性チタン化合物モノリスの製造方法。
- 二酸化チタンから構成される骨格と前記マクロ孔との共連続構造を有するマクロ多孔性二酸化チタンモノリスと、前記金属窒化物と、を前記容器に収容する請求項11に記載のマクロ多孔性チタン化合物モノリスの製造方法。
- 窒化チタンから構成される骨格とマクロ孔との共連続構造を有し、
前記窒化チタンに基づく電子伝導性を有するマクロ多孔性チタン化合物モノリス。 - 二酸化チタン、酸素欠損型酸化チタンまたは酸窒化チタンから構成される骨格とマクロ孔との共連続構造を有するマクロ多孔性チタン化合物モノリスを、アンモニアを含む雰囲気においてアンモニアの熱分解温度以上で熱処理して、前記モノリスを構成するチタン化合物から酸素原子を奪うとともに窒素原子を供給する気相還元を行って、
窒化チタンから構成される骨格と前記マクロ孔との共連続構造を有し、前記窒化チタンに基づく電子伝導性を有するマクロ多孔性窒化チタンモノリスを得る、マクロ多孔性チタン化合物モノリスの製造方法。 - 前記熱処理の温度が1000℃以上である請求項17に記載のマクロ多孔性チタン化合物モノリスの製造方法。
- 二酸化チタンから構成される骨格と前記マクロ孔との共連続構造を有するマクロ多孔性二酸化チタンモノリスを、アンモニアを含む雰囲気においてアンモニアの熱分解温度以上で熱処理する請求項17に記載のマクロ多孔性チタン化合物モノリスの製造方法。
Priority Applications (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US14/379,218 US9902623B2 (en) | 2012-02-17 | 2013-02-18 | Macroporous titanium compound monolith and method for producing same |
JP2014500117A JP5986187B2 (ja) | 2012-02-17 | 2013-02-18 | マクロ多孔性チタン化合物モノリスとその製造方法 |
EP13748592.6A EP2816012B1 (en) | 2012-02-17 | 2013-02-18 | Macroporous titanium compound monolith and method for manufacturing same |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2012-032411 | 2012-02-17 | ||
JP2012032411 | 2012-02-17 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2013121801A1 true WO2013121801A1 (ja) | 2013-08-22 |
Family
ID=48983929
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2013/000886 WO2013121801A1 (ja) | 2012-02-17 | 2013-02-18 | マクロ多孔性チタン化合物モノリスとその製造方法 |
Country Status (4)
Country | Link |
---|---|
US (1) | US9902623B2 (ja) |
EP (1) | EP2816012B1 (ja) |
JP (1) | JP5986187B2 (ja) |
WO (1) | WO2013121801A1 (ja) |
Cited By (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2016136799A1 (ja) * | 2015-02-26 | 2016-09-01 | 株式会社エスエヌジー | チタニアからなるモノリス多孔体の製造方法 |
WO2017043449A1 (ja) * | 2015-09-07 | 2017-03-16 | 国立大学法人東京大学 | 酸化チタン凝集体、酸化チタン凝集体の製造方法、酸化チタン粉末体、酸化チタン成形体、電池電極用触媒、電池電極用導電材及びマイクロ波・ミリ波用誘電体 |
JP2017071515A (ja) * | 2015-10-05 | 2017-04-13 | 神奈川県 | 光触媒活性に優れた酸化チタン凝集体及びその製造方法 |
JP2018131370A (ja) * | 2017-02-17 | 2018-08-23 | テイカ株式会社 | 低次酸化チタン及びその製造方法 |
JP2018177553A (ja) * | 2017-04-04 | 2018-11-15 | 東京印刷機材トレーディング株式会社 | 亜酸化チタン粒子を製造する方法及び亜酸化チタン粒子 |
KR20190090811A (ko) * | 2016-12-20 | 2019-08-02 | 생-고뱅 생트레 드 레체르체 에 데투드 유로삐엔 | 아산화 티타늄의 다공성 세라믹 생성물 |
WO2019159608A1 (ja) * | 2018-02-14 | 2019-08-22 | 日本碍子株式会社 | チタニア多孔体及びその製法 |
JP2020117413A (ja) * | 2019-01-21 | 2020-08-06 | 日本碍子株式会社 | 多孔質チタニア粒子の製法 |
WO2022039111A1 (ja) * | 2020-08-21 | 2022-02-24 | デンカ株式会社 | 特定の低次酸化チタンの結晶組成を有する粒子、並びにその製造方法 |
WO2023037953A1 (ja) * | 2021-09-08 | 2023-03-16 | 国立大学法人弘前大学 | 導電性チタン酸化物、金属担持導電性チタン酸化物、膜電極接合体、固体高分子形燃料電池、導電性チタン酸化物の製造方法、及び金属担持導電性チタン酸化物の製造方法 |
Families Citing this family (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP6372586B1 (ja) * | 2017-03-29 | 2018-08-15 | 堺化学工業株式会社 | 電極材料及びその用途 |
CN108380195B (zh) * | 2018-03-26 | 2020-12-11 | 上海师范大学 | 一种基于表面氧缺陷构建的分子氧活化催化剂的制备方法及其应用 |
US10948838B2 (en) * | 2018-08-24 | 2021-03-16 | Canon Kabushiki Kaisha | Electrophotographic photosensitive member, process cartridge and electrophotographic apparatus |
JP7330807B2 (ja) * | 2018-08-24 | 2023-08-22 | キヤノン株式会社 | 電子写真感光体、プロセスカートリッジ及び電子写真装置 |
TWI760963B (zh) * | 2019-12-10 | 2022-04-11 | 美商聖高拜陶器塑膠公司 | 包含馬格涅利相氧化鈦之單塊多孔體及製造該多孔體之方法 |
Citations (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS61127607A (ja) * | 1984-11-24 | 1986-06-14 | Toho Titanium Co Ltd | 窒化チタンの製造方法 |
JPH06505469A (ja) * | 1991-02-21 | 1994-06-23 | アトラバーダ・リミテッド | 導電性亜酸化チタン粒状物 |
JP2000103608A (ja) * | 1998-09-30 | 2000-04-11 | Japan Science & Technology Corp | 窒化チタンの製造方法 |
JP2000239709A (ja) * | 1999-02-25 | 2000-09-05 | Aisin Chem Co Ltd | 直接通電焼結法および焼結装置 |
JP2002154823A (ja) * | 2000-11-10 | 2002-05-28 | Toyota Central Res & Dev Lab Inc | 無機系酸窒化物の製造方法および無機系酸窒化物 |
WO2003002458A1 (fr) | 2001-06-29 | 2003-01-09 | Japan Science And Technology Corporation | Procede de preparation d'une matiere inorganique poreuse |
WO2007021037A1 (ja) | 2005-08-19 | 2007-02-22 | Kyoto University | 無機系多孔質体及びその製造方法 |
JP2011518094A (ja) * | 2007-12-19 | 2011-06-23 | ザ ボード オブ トラスティーズ オブ ザ ユニヴァーシティー オブ イリノイ | 共ドープ酸化チタン発泡体および水殺菌装置 |
Family Cites Families (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
GB1219580A (en) * | 1967-08-02 | 1971-01-20 | Foseco Int | Titanium oxides in electroslag processes |
US5976454A (en) | 1996-04-01 | 1999-11-02 | Basf Aktiengesellschaft | Process for producing open-celled, inorganic sintered foam products |
DE10121928A1 (de) | 2001-05-05 | 2002-11-14 | Univ Friedrich Alexander Er | Verfahren zur Herstellung lokal verstärkter Leichtmetallteile |
US20100324155A1 (en) | 2003-07-08 | 2010-12-23 | Los Alamos National Security, Llc | Preparation of inorganic foam |
-
2013
- 2013-02-18 EP EP13748592.6A patent/EP2816012B1/en active Active
- 2013-02-18 US US14/379,218 patent/US9902623B2/en active Active
- 2013-02-18 JP JP2014500117A patent/JP5986187B2/ja active Active
- 2013-02-18 WO PCT/JP2013/000886 patent/WO2013121801A1/ja active Application Filing
Patent Citations (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS61127607A (ja) * | 1984-11-24 | 1986-06-14 | Toho Titanium Co Ltd | 窒化チタンの製造方法 |
JPH06505469A (ja) * | 1991-02-21 | 1994-06-23 | アトラバーダ・リミテッド | 導電性亜酸化チタン粒状物 |
JP2000103608A (ja) * | 1998-09-30 | 2000-04-11 | Japan Science & Technology Corp | 窒化チタンの製造方法 |
JP2000239709A (ja) * | 1999-02-25 | 2000-09-05 | Aisin Chem Co Ltd | 直接通電焼結法および焼結装置 |
JP2002154823A (ja) * | 2000-11-10 | 2002-05-28 | Toyota Central Res & Dev Lab Inc | 無機系酸窒化物の製造方法および無機系酸窒化物 |
WO2003002458A1 (fr) | 2001-06-29 | 2003-01-09 | Japan Science And Technology Corporation | Procede de preparation d'une matiere inorganique poreuse |
WO2007021037A1 (ja) | 2005-08-19 | 2007-02-22 | Kyoto University | 無機系多孔質体及びその製造方法 |
JP2011518094A (ja) * | 2007-12-19 | 2011-06-23 | ザ ボード オブ トラスティーズ オブ ザ ユニヴァーシティー オブ イリノイ | 共ドープ酸化チタン発泡体および水殺菌装置 |
Non-Patent Citations (6)
Cited By (23)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US10435305B2 (en) | 2015-02-26 | 2019-10-08 | Sng Inc. | Method for producing monolithic porous body comprising titania |
JP6176557B2 (ja) * | 2015-02-26 | 2017-08-09 | 株式会社エスエヌジー | チタニアからなるモノリス多孔体の製造方法 |
WO2016136799A1 (ja) * | 2015-02-26 | 2016-09-01 | 株式会社エスエヌジー | チタニアからなるモノリス多孔体の製造方法 |
JPWO2016136799A1 (ja) * | 2015-02-26 | 2017-08-10 | 株式会社エスエヌジー | チタニアからなるモノリス多孔体の製造方法 |
JP2017052659A (ja) * | 2015-09-07 | 2017-03-16 | 国立大学法人 東京大学 | 酸化チタン凝集体、酸化チタン凝集体の製造方法、酸化チタン粉末体、酸化チタン成形体、電池電極用触媒、電池電極用導電材及びマイクロ波・ミリ波用誘電体 |
WO2017043449A1 (ja) * | 2015-09-07 | 2017-03-16 | 国立大学法人東京大学 | 酸化チタン凝集体、酸化チタン凝集体の製造方法、酸化チタン粉末体、酸化チタン成形体、電池電極用触媒、電池電極用導電材及びマイクロ波・ミリ波用誘電体 |
JP2017071515A (ja) * | 2015-10-05 | 2017-04-13 | 神奈川県 | 光触媒活性に優れた酸化チタン凝集体及びその製造方法 |
KR20190090811A (ko) * | 2016-12-20 | 2019-08-02 | 생-고뱅 생트레 드 레체르체 에 데투드 유로삐엔 | 아산화 티타늄의 다공성 세라믹 생성물 |
JP2020502037A (ja) * | 2016-12-20 | 2020-01-23 | サン−ゴバン サントル ドゥ ルシェルシェ エ デトゥードゥ ユーロペン | 亜酸化チタンの多孔質セラミック生成物 |
KR102478403B1 (ko) | 2016-12-20 | 2022-12-19 | 생-고뱅 생트레 드 레체르체 에 데투드 유로삐엔 | 아산화 티타늄의 다공성 세라믹 생성물 |
JP7084940B2 (ja) | 2016-12-20 | 2022-06-15 | サン-ゴバン サントル ドゥ ルシェルシェ エ デトゥードゥ ユーロペン | 亜酸化チタンの多孔質セラミック生成物 |
JP2018131370A (ja) * | 2017-02-17 | 2018-08-23 | テイカ株式会社 | 低次酸化チタン及びその製造方法 |
JP2018177553A (ja) * | 2017-04-04 | 2018-11-15 | 東京印刷機材トレーディング株式会社 | 亜酸化チタン粒子を製造する方法及び亜酸化チタン粒子 |
JP6994684B2 (ja) | 2017-04-04 | 2022-01-14 | 東京印刷機材トレーディング株式会社 | 亜酸化チタン粒子を製造する方法及び亜酸化チタン粒子 |
US11772983B2 (en) | 2018-02-14 | 2023-10-03 | Ngk Insulators, Ltd. | Titania porous body and method for producing same |
JP7032744B2 (ja) | 2018-02-14 | 2022-03-09 | 日本碍子株式会社 | チタニア多孔体及びその製法 |
JPWO2019159608A1 (ja) * | 2018-02-14 | 2021-01-07 | 日本碍子株式会社 | チタニア多孔体及びその製法 |
WO2019159608A1 (ja) * | 2018-02-14 | 2019-08-22 | 日本碍子株式会社 | チタニア多孔体及びその製法 |
JP7295510B2 (ja) | 2019-01-21 | 2023-06-21 | 日本碍子株式会社 | 多孔質チタニア粒子の製法 |
JP2020117413A (ja) * | 2019-01-21 | 2020-08-06 | 日本碍子株式会社 | 多孔質チタニア粒子の製法 |
WO2022039111A1 (ja) * | 2020-08-21 | 2022-02-24 | デンカ株式会社 | 特定の低次酸化チタンの結晶組成を有する粒子、並びにその製造方法 |
CN115835912A (zh) * | 2020-08-21 | 2023-03-21 | 电化株式会社 | 具有特定的低价氧化钛的晶体组成的粒子及其制造方法 |
WO2023037953A1 (ja) * | 2021-09-08 | 2023-03-16 | 国立大学法人弘前大学 | 導電性チタン酸化物、金属担持導電性チタン酸化物、膜電極接合体、固体高分子形燃料電池、導電性チタン酸化物の製造方法、及び金属担持導電性チタン酸化物の製造方法 |
Also Published As
Publication number | Publication date |
---|---|
EP2816012A1 (en) | 2014-12-24 |
US9902623B2 (en) | 2018-02-27 |
US20150037236A1 (en) | 2015-02-05 |
EP2816012A4 (en) | 2015-11-04 |
JPWO2013121801A1 (ja) | 2015-05-11 |
EP2816012B1 (en) | 2021-12-15 |
JP5986187B2 (ja) | 2016-09-06 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP5986187B2 (ja) | マクロ多孔性チタン化合物モノリスとその製造方法 | |
Li et al. | A-site perovskite oxides: an emerging functional material for electrocatalysis and photocatalysis | |
Wang et al. | In situ synthesis of ordered mesoporous Co-doped TiO 2 and its enhanced photocatalytic activity and selectivity for the reduction of CO 2 | |
KR101970073B1 (ko) | 촉매 지지체, 및 금속 나노 입자로 피복된 다공성의 흑연화된 탄소 재료의 제조 방법 | |
Wang et al. | Niobium doped TiO2 with mesoporosity and its application for lithium insertion | |
Weidenkaff et al. | Ln1-x A x CoO3 (Ln= Er, La; A= Ca, Sr)/carbon nanotube composite materials applied for rechargeable Zn/air batteries | |
JP5331011B2 (ja) | 触媒用担体、触媒およびその製造方法 | |
US7670679B2 (en) | Core-shell ceramic particulate and method of making | |
Durgasri et al. | Nanosized CeO 2–Gd 2 O 3 mixed oxides: study of structural characterization and catalytic CO oxidation activity | |
Ashok et al. | Influence of fuel ratio on the performance of combustion synthesized bifunctional cobalt oxide catalysts for fuel cell application | |
Savic et al. | Hard template synthesis of nanomaterials based on mesoporous silica | |
Su et al. | A top-down strategy for the synthesis of mesoporous Ba0. 5Sr0. 5Co0. 8Fe0. 2O3− δ as a cathode precursor for buffer layer-free deposition on stabilized zirconia electrolyte with a superior electrochemical performance | |
Ng et al. | Enhancing the performance of 3D porous N-doped carbon in oxygen reduction reaction and supercapacitor via boosting the meso-macropore interconnectivity using the “exsolved” dual-template | |
CA2721138A1 (en) | Catalyst, method for producing the same, and use of the same | |
Wang et al. | Synthesis of α-MnO 2 nanowires modified by Co 3 O 4 nanoparticles as a high-performance catalyst for rechargeable Li–O 2 batteries | |
Tan et al. | N, S-containing MOF-derived dual-doped mesoporous carbon as a highly effective oxygen reduction reaction electrocatalyst | |
Yang et al. | Well-defined gold nanoparticle@ N-doped porous carbon prepared from metal nanoparticle@ metal–organic frameworks for electrochemical sensing of hydrazine | |
Ma et al. | Bandgap and defects regulation of La2− xAxNi1− yByO4+ δ (A= K, Sr, B= Co, Mn) Ruddlesden-Popper type perovskites for efficient photocatalytic hydrogen evolution | |
Milikić et al. | Efficient bifunctional cerium-zeolite electrocatalysts for oxygen evolution and oxygen reduction reactions in alkaline media | |
JP4869926B2 (ja) | 多孔質アルミナ粒子およびその製造方法 | |
KR101760649B1 (ko) | 금속헤테로원소로 기능화된 탄소 구조체 및 이의 제조방법 | |
Mihaiu et al. | The structure properties correlation in the Ce-doped SnO2 materials obtained by different synthesis routes | |
Yang et al. | Boosting visible-light-driven water splitting over LaTaON2 via Al doping | |
JP6162010B2 (ja) | メソポーラス酸化タングステンの製造方法、光触媒の製造方法、及びメソポーラス酸化タングステン電極の製造方法 | |
Fuentes et al. | A Nb-doped TiO2 electrocatalyst for use in direct methanol fuel cells |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 13748592 Country of ref document: EP Kind code of ref document: A1 |
|
DPE2 | Request for preliminary examination filed before expiration of 19th month from priority date (pct application filed from 20040101) | ||
ENP | Entry into the national phase |
Ref document number: 2014500117 Country of ref document: JP Kind code of ref document: A |
|
WWE | Wipo information: entry into national phase |
Ref document number: 14379218 Country of ref document: US |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2013748592 Country of ref document: EP |