WO2010007929A1 - 層状化合物及び超伝導体並びにそれらの製造方法 - Google Patents
層状化合物及び超伝導体並びにそれらの製造方法 Download PDFInfo
- Publication number
- WO2010007929A1 WO2010007929A1 PCT/JP2009/062500 JP2009062500W WO2010007929A1 WO 2010007929 A1 WO2010007929 A1 WO 2010007929A1 JP 2009062500 W JP2009062500 W JP 2009062500W WO 2010007929 A1 WO2010007929 A1 WO 2010007929A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- powder
- superconductor
- mixed
- layered compound
- group
- Prior art date
Links
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01G—COMPOUNDS CONTAINING METALS NOT COVERED BY SUBCLASSES C01D OR C01F
- C01G49/00—Compounds of iron
- C01G49/009—Compounds containing, besides iron, two or more other elements, with the exception of oxygen or hydrogen
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01G—COMPOUNDS CONTAINING METALS NOT COVERED BY SUBCLASSES C01D OR C01F
- C01G53/00—Compounds of nickel
- C01G53/006—Compounds containing, besides nickel, two or more other elements, with the exception of oxygen or hydrogen
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01G—COMPOUNDS CONTAINING METALS NOT COVERED BY SUBCLASSES C01D OR C01F
- C01G55/00—Compounds of ruthenium, rhodium, palladium, osmium, iridium, or platinum
- C01G55/002—Compounds containing, besides ruthenium, rhodium, palladium, osmium, iridium, or platinum, two or more other elements, with the exception of oxygen or hydrogen
-
- 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
-
- 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
- C04B35/5154—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 phosphides
-
- 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
- C04B35/553—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 fluorides
-
- H—ELECTRICITY
- H10—SEMICONDUCTOR DEVICES; ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
- H10N—ELECTRIC SOLID-STATE DEVICES NOT OTHERWISE PROVIDED FOR
- H10N60/00—Superconducting devices
- H10N60/80—Constructional details
- H10N60/85—Superconducting active materials
- H10N60/855—Ceramic materials
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2002/00—Crystal-structural characteristics
- C01P2002/30—Three-dimensional structures
- C01P2002/34—Three-dimensional structures perovskite-type (ABO3)
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2002/00—Crystal-structural characteristics
- C01P2002/50—Solid solutions
- C01P2002/52—Solid solutions containing elements as dopants
-
- 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
- C01P2002/00—Crystal-structural characteristics
- C01P2002/70—Crystal-structural characteristics defined by measured X-ray, neutron or electron diffraction data
- C01P2002/76—Crystal-structural characteristics defined by measured X-ray, neutron or electron diffraction data by a space-group or by other symmetry indications
-
- 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
- C01P2002/77—Crystal-structural characteristics defined by measured X-ray, neutron or electron diffraction data by unit-cell parameters, atom positions or structure diagrams
-
- 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
- C01P2002/78—Crystal-structural characteristics defined by measured X-ray, neutron or electron diffraction data by stacking-plane distances or stacking sequences
-
- 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
- C01P2004/80—Particles consisting of a mixture of two or more inorganic phases
-
- 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
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2006/00—Physical properties of inorganic compounds
- C01P2006/42—Magnetic 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
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3205—Alkaline earth oxides or oxide forming salts thereof, e.g. beryllium oxide
- C04B2235/3208—Calcium oxide or oxide-forming salts thereof, e.g. lime
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3205—Alkaline earth oxides or oxide forming salts thereof, e.g. beryllium oxide
- C04B2235/3213—Strontium oxides or oxide-forming salts thereof
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/40—Metallic constituents or additives not added as binding phase
-
- 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
- C04B2235/401—Alkaline earth 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
- C04B2235/40—Metallic constituents or additives not added as binding phase
- C04B2235/405—Iron group 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
- C04B2235/44—Metal salt constituents or additives chosen for the nature of the anions, e.g. hydrides or acetylacetonate
- C04B2235/444—Halide containing anions, e.g. bromide, iodate, chlorite
- C04B2235/445—Fluoride containing anions, e.g. fluosilicate
-
- 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
- C04B2235/44—Metal salt constituents or additives chosen for the nature of the anions, e.g. hydrides or acetylacetonate
- C04B2235/446—Sulfides, tellurides or selenides
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/50—Constituents or additives of the starting mixture chosen for their shape or used because of their shape or their physical appearance
- C04B2235/54—Particle size related information
- C04B2235/5418—Particle size related information expressed by the size of the particles or aggregates thereof
- C04B2235/5436—Particle size related information expressed by the size of the particles or aggregates thereof micrometer sized, i.e. from 1 to 100 micron
-
- 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
- C04B2235/6581—Total pressure below 1 atmosphere, e.g. vacuum
-
- 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
- C04B2235/76—Crystal structural characteristics, e.g. symmetry
Definitions
- the present invention relates to a layered compound having a transition metal element (at least one of Fe, Ru, Os, Ni, Pd, and Pt) in a skeleton structure, a superconductor composed of the compound, and a method for producing the same.
- a transition metal element at least one of Fe, Ru, Os, Ni, Pd, and Pt
- Non-Patent Documents 1 and 2 The understanding of the mechanism of superconductivity of perovskite-type copper oxide is also progressing (for example, Non-Patent Documents 1 and 2).
- Patent Documents 2 and 3 Patent Documents 2 and 3
- a strongly correlated electron compound in which the interaction between conduction electrons is larger than the conduction band width may be a superconductor having a high superconducting transition temperature when the number of d electrons is a specific value. It is known to be expensive.
- the strongly correlated electron system is realized by a layered compound having a transition metal ion in a skeleton structure. Many of these layered compounds are Mott insulators with electrical conductivity, and an antiferromagnetic interaction is acting between the spins of electrons in an antiparallel manner.
- Patent Document 4 Non-Patent Document 7
- the strong electron correlation system when the number of d electrons is a specific value, it becomes an itinerant electronic state indicating metal conduction, and when the temperature is lowered, it transitions to a superconducting state at a specific temperature (superconducting transition temperature) or lower.
- the transition temperature of this superconductor varies from 5K to 40K depending on the number of conductive carriers.
- the electron pair (Cooper pair) based on the thermal fluctuation (lattice vibration) of the crystal lattice is the superconductivity generation mechanism (BCS mechanism).
- BCS mechanism superconductivity generation mechanism
- an electron pair based on thermal fluctuation of electron spin is considered as a superconductivity generation mechanism.
- Ln (TM) OPn compound [Ln is Y and a lanthanoid element (La, Ce, Pr, Nd, Sm, Eu, Gd, Tb, Dy, Ho, Er). , Tm, Yb, Lu), TM is at least one of transition metal elements (Fe, Ru, Os, Ni, Pd, Pt), and Pn is pnicogen element (N, P, As, It is at least one of Sb).
- Patent Document 5 Non-Patent Documents 8 to 10).
- the present inventors have also disclosed an A (TM) 2 (Pn) 2 compound [A is at least one group 2 element of the long-period periodic table, and TM is Fe, Ru, Os, Ni, Pd, Pt. At least one transition metal element selected from the group consisting of Pn is at least one group 15 element (pnicogen element) in the long-period periodic table. ], Found a superconductor and applied for a patent (Patent Document 6, Non-Patent Document 11).
- the present inventors realized a superconductor in a layered compound represented by AF (TM) Pn.
- the superconductor of the present invention is provided by a non-oxide-based layered compound represented by the chemical formula AF (TM) Pn.
- A is at least one group 2 element of the long-period periodic table
- F is a fluorine ion
- TM is at least one transition metal element selected from Fe, Ru, Os, Ni, Pd, and Pt.
- Pn is at least one of group 15 elements (pnictogen) in the long-period periodic table.
- Electrons can be generated in the AF layer by doping the layered compound with trivalent cations, and the electrons move to the (TM) Pn layer. Further, by doping the F site of the layered compound with a divalent anion, holes are generated, and the holes move to the (TM) Pn layer and change the hole concentration of the layer.
- the present invention relates to (1) chemical formula AF (TM) Pn (where A is at least one group 2 element of the long periodic table, F is a fluorine ion, TM is Fe, Ru, Os, At least one transition metal element selected from Ni, Pd, and Pt, Pn is at least one group 15 element in the long-period periodic table), and is of the ZrCuSiAs type (space group P4 / nmm) A layered compound characterized by having a crystal structure and becoming a superconductor by doping with a trivalent cation or a divalent anion.
- the present invention is also characterized in that (2) A is at least one of Ca and Sr, TM is Ni or Fe, and Pn is at least one of P, As, and Sb. ) Layered compound.
- the present invention is (3) a superconductor characterized in that the layered compound of (1) is doped with Sc, Y, La, Nd, or Gd ions as trivalent cations.
- the present invention is (4) a superconductor characterized in that the layered compound of (1) above is doped with O, S, or Se ions as divalent anions.
- the present invention also includes (5) a raw material of A element powder, TM element powder, Pn element powder, and fluorine compound powder of these elements, and the mixed powder is mixed in an inert atmosphere or in vacuum.
- the method for producing a layered compound according to the above (1) characterized by sintering at ⁇ 1200 ° C.
- the present invention provides (6) raw materials such as A element powder, TM element powder, Pn element powder, fluorine compound powder of these elements, and trivalent cation element powder or trivalent cation.
- (3) The method for producing a superconductor according to (3), wherein the fluorine compound powder of the element is mixed and the mixed powder is sintered at 900 to 1200 ° C. in an inert atmosphere or vacuum.
- a element powder, TM element powder, Pn element powder, and fluorine compound powder of these elements are mixed as raw materials, and further, A element oxide powder and sulfide powder are mixed.
- FIG. 2 is an X-ray diffraction pattern of a sintered body obtained in Synthesis Example 1 of Example 1.
- FIG. 4 is a graph showing a temperature change in electrical resistance of the sintered body obtained in Synthesis Example 1 of Example 1.
- 6 is a graph showing a change in temperature of the magnetic susceptibility of the sintered body obtained in Synthesis Example 1 of Example 1. It is a graph which shows the temperature change of the electrical resistance of the non-doped and the La-doped sintered body obtained in Example 1. It is a graph which shows the temperature change of the magnetic susceptibility of the sintered compact which doped 10 atomic% of La obtained in Example 1.
- FIG. 4 is a graph showing a temperature change in electrical resistance of the sintered body obtained in Synthesis Example 1 of Example 1.
- 6 is a graph showing a change in temperature of the magnetic susceptibility of the sintered body obtained in Synthesis Example 1 of Example 1. It is a graph which shows the temperature change of the electrical resistance of the non-doped and the La-doped
- FIG. 1 shows a crystal structure model of a layered compound represented by AF (TM) Pn that provides the superconductor of the present invention.
- the compound represented by AF (TM) Pn has a structure in which the (TM) Pn layer of the conductive layer and the AF layer of the insulating layer are alternately overlapped. Some electrons have moved from the AF layer to the (TM) Pn layer, the AF layer is positively charged, the (TM) Pn layer is negatively charged, and both layers are ionically bonded.
- the (TM) Pn layer has a structure in which (TM) (Pn) 4 tetrahedrons are closely coupled, and has a strong two-dimensionality.
- the (TM) 3d electrons have a large itinerant property, and the magnetic moment is significantly reduced as compared to free ions.
- the strong two-dimensionality and the reduced magnetic moment have an advantageous effect on the development of superconductivity.
- the AF layer contains fluorine ions, it is easy to make a chemical equivalent ratio composition.
- A is a divalent metal (cation) ion, electrons can be easily generated by substituting a part of A with a trivalent cation such as La 3+ . Further, holes can be easily generated by doping the F site with divalent anions such as O, S, or Se ions.
- Examples of the group A element of the long-period periodic table of the compound represented by the chemical formula AF (TM) Pn include Be, Mg, Ca, Sr, Ba, and Ra. Ca, Sr and mixed crystals thereof are preferable in that electrons can be generated from the difference in electronegativity of both metals, and mixed crystals are formed in the entire composition region.
- TM is at least one of transition metal elements of Fe, Ru, Os, Ni, Pd, and Pt. These transition metals have the common feature that the number of d electrons is an even number and the magnetic moment can be made almost zero.
- Fe and Ni are preferable in that the main quantum number is the minimum (3) and the effective mass of electrons does not increase.
- Pn is at least one selected from the group 15 elements of the long-period periodic table, that is, N, P, As, Sb, and Bi, and these elements are referred to as pnicogen elements.
- Specific examples of the compound represented by the chemical formula AF (TM) Pn include SrFFeAs, CaFFeAs, (SrCa) FFeAs, and the like.
- TM trivalent cation
- the concentration of the trivalent cation in which the superconducting state appears is about 8 to 30 atomic%, preferably about 10 to 20 atomic% with respect to the A metal, and the superconducting transition temperature (Tc) is about 15 atomic%. The highest temperature.
- Examples of the trivalent cation include Sc, Y and lanthanoid (atomic number 57 to 71) element ions of Group 3 elements of the long-period periodic table.
- lanthanoid elements La, Nd, and Gd are preferable in that the ionic radius is close to that of the A metal ion.
- Specific examples of the compound include SrFFeAs: La, SrFFeAs: Nd, (SrCa) FFeAs: Gd, Sr (FO) FeAs, and the like.
- B, Al, Ga, In, and Tl element ions of group 13 elements of the long-period periodic table can be used as the trivalent cation. *
- the layered compound of the present invention is prepared by mixing, as raw materials, an A element powder, a TM element powder, a Pn element powder, and a fluorine compound powder of these elements, preferably an inorganic fluoride powder. It can be produced by heating and sintering in an active atmosphere or vacuum to synthesize a polycrystalline sintered body of AF (TM) Pn.
- TM polycrystalline sintered body of AF
- a sintered body having a density of about 80% is obtained by sintering.
- the sintered body contains many thin single crystals of about 50 ⁇ m square.
- Sintering is preferable in that it can be pre-fired at a relatively low temperature and the temperature can be increased to reduce the number of heterogeneous phases. Further, in order to obtain a complete AF (TM) Pn phase having superconductivity, it is preferable in that a single phase can be obtained by once pulverizing the sintered body into a powder and then sintering it again. .
- the sintering reaction formula is shown as follows. Sr + 2Fe + 2As + SrF 2 ⁇ 2SrFFeAs
- a metal powder of a trivalent cation element or a fluoride of a trivalent cation element, for example, LaF 3 is added to a metal A 3.
- the same heating reaction process as described above may be performed by adding to the raw material powder so that La of the valent cation is about 8 to 30 atomic% and mixing.
- a compound of a divalent anion and an A metal such as an A element oxide powder, sulfide powder, selenide powder, or sulfur powder, or selenium
- a divalent anion powder such as powder may be added to the raw material powder, mixed, and subjected to the same heating reaction process as described above.
- the A metal is Ca
- the CaO, CaS, or CaSe powder is added to the raw material powder so that the divalent anion O, S, or Se is about 5 to 40 atomic% with respect to the Ca metal. . *
- FIG. 2 shows the results of measuring the electrical resistance of the SrFFeAs obtained above in the range of 2K to 300K by forming the electrode with silver paste and using the four probe method.
- FIG. 4 shows the temperature change of the magnetic susceptibility. A decrease in electrical resistance is observed near 170K, but the superconducting state cannot be confirmed.
- FIG. 5 shows the results of measuring the electrical resistance of the La-doped SrFFeAs sintered body obtained above in the range of 2K to 300K by forming electrodes with a silver paste and using the four-terminal method. In samples containing 10 atomic% and 20 atomic% of La, a rapid decrease in electrical resistance was confirmed at around 30K.
- FIG. 6 shows the temperature change of the magnetic susceptibility of the SrFFeAs sintered body doped with 10 atomic% La. It can be seen that this sintered body has a superconducting transition temperature of about 30K.
Abstract
Description
Sr+2Fe+2As+SrF2→2SrFFeAs
<SrFFeAsの合成例1>
Sr(粒径10~500μm)、Fe(粒径1~100μm)、As(粒径1~100μm)、SrF2(粒径1~100μm)の各粉末をSr:F:Fe:Asの原子比が1:1:1:1:となるように酸素濃度0.1ppm未満、湿度0.01%程度のグローブボックス中で乳鉢を用いて乾式混合した。約1gの混合物を真空中、400℃で12時間仮焼し、次いで、1000℃で12時間加熱して焼結した。焼結体を粉砕して粒径5~100μmの粉末とし、得られた粉末を封管し、真空中、1000℃で12時間焼結した。
Laを上記合成例1の原料混合粉末に対して、La金属粉末(粒径10~500μm)を、Sr金属に対して5原子%、10原子%、20原子%ドープした3種類の混合粉末を作成し、上記合成例1と同じ条件で焼成し、3種類のSrFFeAs:La焼結体を合成した。
Claims (7)
- 化学式AF(TM)Pn(ただし、Aは、長周期型周期表の2族元素の少なくとも1種、Fは、フッ素イオン、TMは、Fe,Ru,Os,Ni,Pd,Ptから選ばれる遷移金属元素の少なくとも1種、Pnは、長周期型周期表の15族元素の少なくとも1種である。)で示され、ZrCuSiAs型(空間群P4/nmm)の結晶構造を有し、3価の陽イオン又は2価の陰イオンをドープすることにより超伝導体となることを特徴とする層状化合物。
- AがCa,Srの少なくも一種であり、TMがNi又はFeであり、PnがP,As,Sbの少なくとも1種であることを特徴とする請求項1記載の層状化合物。
- 請求項1記載の層状化合物に3価の陽イオンとしてSc,Y,La,Nd,又はGdイオンをドープしたことを特徴とする超伝導体。
- 請求項1記載の層状化合物に2価の陰イオンとしてO,S, 又はSeイオンをドープしたことを特徴とする超伝導体。
- 原料として、A元素の粉末、TM元素の粉末、Pn元素の粉末、及びこれらの元素のフッ素化合物粉末を混合し、混合粉末を不活性雰囲気又は真空中、900~1200℃で焼結することを特徴とする請求項1に記載の層状化合物の製造方法。
- 原料として、A元素の粉末、TM元素の粉末、Pn元素の粉末、これらの元素のフッ素化合物粉末、及び3価の陽イオンの元素粉末又は3価の陽イオンの元素のフッ素化合物粉末を混合し、混合粉末を不活性雰囲気又は真空中、900~1200℃で焼結することを特徴とする請求項3に記載の超伝導体の製造方法。
- 原料として、A元素の粉末、TM元素の粉末、Pn元素の粉末、これらの元素のフッ素化合物粉末を混合し、さらに、A元素の酸化物粉末、硫化物粉末、セレン化物粉末、イオウ粉末、又はセレン粉末を追加して混合し、混合粉末を不活性雰囲気又は真空中、900~1200℃で焼結することを特徴とする請求項4に記載の超伝導体の製造方法。
Priority Applications (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2010520839A JP5440879B2 (ja) | 2008-07-16 | 2009-07-09 | 層状化合物及び超伝導体並びにそれらの製造方法。 |
US13/003,149 US8288321B2 (en) | 2008-07-16 | 2009-07-09 | Layered compound, superconductor and method for producing same |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2008184843 | 2008-07-16 | ||
JP2008-184843 | 2008-07-16 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2010007929A1 true WO2010007929A1 (ja) | 2010-01-21 |
Family
ID=41550332
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2009/062500 WO2010007929A1 (ja) | 2008-07-16 | 2009-07-09 | 層状化合物及び超伝導体並びにそれらの製造方法 |
Country Status (3)
Country | Link |
---|---|
US (1) | US8288321B2 (ja) |
JP (1) | JP5440879B2 (ja) |
WO (1) | WO2010007929A1 (ja) |
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN102074311A (zh) * | 2010-12-08 | 2011-05-25 | 中国科学院电工研究所 | 一种制备高密度铁基化合物超导带材的方法 |
WO2015045733A1 (ja) * | 2013-09-26 | 2015-04-02 | 国立大学法人岡山大学 | 鉄系超電導物質及びその製造方法 |
CN105405531A (zh) * | 2015-12-18 | 2016-03-16 | 常熟市东方特种金属材料厂 | 一种新型超导材料的制备方法 |
CN109810574A (zh) * | 2017-11-21 | 2019-05-28 | 深圳Tcl工业研究院有限公司 | 无机纳米材料印刷油墨及其制备方法和应用 |
Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2006098432A1 (ja) * | 2005-03-18 | 2006-09-21 | Japan Science And Technology Agency | 磁性半導体材料 |
JP2007320829A (ja) * | 2006-06-02 | 2007-12-13 | Japan Science & Technology Agency | 超伝導化合物及びその製造方法 |
Family Cites Families (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
GB301690A (en) * | 1928-04-04 | 1928-12-06 | Carl Alrik Hult | Improvements in rotary compressor, pump or motor |
US5175140A (en) * | 1987-03-19 | 1992-12-29 | Sumitomo Electric Industries, Ltd. | High Tc superconducting material |
CA1340168C (en) * | 1987-07-28 | 1998-12-08 | Rosa Young | Method of aligning grains of a multi-grained superconducting material |
US5426092A (en) * | 1990-08-20 | 1995-06-20 | Energy Conversion Devices, Inc. | Continuous or semi-continuous laser ablation method for depositing fluorinated superconducting thin film having basal plane alignment of the unit cells deposited on non-lattice-matched substrates |
US5482917A (en) * | 1993-09-21 | 1996-01-09 | E. I. Du Pont De Nemours And Company | T1-M-Cu-O-F superconductors |
JP3575004B2 (ja) | 2001-01-09 | 2004-10-06 | 独立行政法人 科学技術振興機構 | マグネシウムとホウ素とからなる金属間化合物超伝導体及びその金属間化合物を含有する合金超伝導体並びにこれらの製造方法 |
JP4041883B2 (ja) | 2003-01-27 | 2008-02-06 | 独立行政法人物質・材料研究機構 | 水和ナトリウムコバルト酸化物とその製造方法 |
JP4370382B2 (ja) | 2004-06-14 | 2009-11-25 | 独立行政法人物質・材料研究機構 | 水和ナトリウムコバルト酸化物 |
JP5518295B2 (ja) | 2008-03-27 | 2014-06-11 | 独立行政法人科学技術振興機構 | 層状化合物からなる超伝導体及びその製造方法 |
-
2009
- 2009-07-09 US US13/003,149 patent/US8288321B2/en not_active Expired - Fee Related
- 2009-07-09 JP JP2010520839A patent/JP5440879B2/ja not_active Expired - Fee Related
- 2009-07-09 WO PCT/JP2009/062500 patent/WO2010007929A1/ja active Application Filing
Patent Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2006098432A1 (ja) * | 2005-03-18 | 2006-09-21 | Japan Science And Technology Agency | 磁性半導体材料 |
JP2007320829A (ja) * | 2006-06-02 | 2007-12-13 | Japan Science & Technology Agency | 超伝導化合物及びその製造方法 |
Non-Patent Citations (2)
Title |
---|
MATSUISHI S. ET AL: "Cobal-Substitution-Induced Superconductivity in a New Compound with ZrCuSiAs-Type Structure, SrFeAsF.", J. PHYS. SOC. JPN., vol. 77, no. 11, November 2008 (2008-11-01), pages 113709-1 - 113709-3 * |
MATSUISHI S. ET AL: "Superconductivity Induced by Co-Doping in Quarternary Fluoroarsenide CaFeAsF.", J. AM. CHEM. SOC., vol. 130, no. 44, 8 December 2008 (2008-12-08), pages 14428 - 14429 * |
Cited By (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN102074311A (zh) * | 2010-12-08 | 2011-05-25 | 中国科学院电工研究所 | 一种制备高密度铁基化合物超导带材的方法 |
WO2015045733A1 (ja) * | 2013-09-26 | 2015-04-02 | 国立大学法人岡山大学 | 鉄系超電導物質及びその製造方法 |
JPWO2015045733A1 (ja) * | 2013-09-26 | 2017-03-09 | 国立大学法人 岡山大学 | 鉄系超電導物質及びその製造方法 |
CN105405531A (zh) * | 2015-12-18 | 2016-03-16 | 常熟市东方特种金属材料厂 | 一种新型超导材料的制备方法 |
CN109810574A (zh) * | 2017-11-21 | 2019-05-28 | 深圳Tcl工业研究院有限公司 | 无机纳米材料印刷油墨及其制备方法和应用 |
Also Published As
Publication number | Publication date |
---|---|
US20110111965A1 (en) | 2011-05-12 |
JP5440879B2 (ja) | 2014-03-12 |
US8288321B2 (en) | 2012-10-16 |
JPWO2010007929A1 (ja) | 2012-01-05 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
Zhu et al. | Effects of Dy and Yb co-doping on thermoelectric properties of CaMnO3 ceramics | |
Kahraman et al. | Enhancement of mechanical and thermoelectric properties of Ca3Co4O9 by Ag addition | |
Xu et al. | Thermoelectric performance of textured Ca3− xYbxCo4O9− δ ceramics | |
US8435473B2 (en) | Superconducting compound and method for producing the same | |
JP5196339B2 (ja) | 超伝導化合物及びその製造方法 | |
Liu et al. | Achieving enhanced thermoelectric performance of Ca1− x− yLaxSryMnO3 via synergistic carrier concentration optimization and chemical bond engineering | |
Delorme et al. | Promising high temperature thermoelectric properties of dense Ba2Co9O14 ceramics | |
Choi et al. | Thermoelectric properties of the Ca 1− x R x MnO 3 perovskite system (R: Pr, Nd, Sm) for high-temperature applications | |
Bousnina et al. | Synthesis, sintering, and thermoelectric properties of the solid solution La 1–x Sr x CoO 3±δ (0≤ x≤ 1) | |
Lin et al. | Preparation and thermoelectric properties of Nd and Dy co-doped SrTiO3 bulk materials | |
JP5440879B2 (ja) | 層状化合物及び超伝導体並びにそれらの製造方法。 | |
JP7298869B2 (ja) | 超電導体 | |
Carreira et al. | Laser processing as a tool for designing donor-substituted calcium manganite-based thermoelectrics | |
JP5518295B2 (ja) | 層状化合物からなる超伝導体及びその製造方法 | |
JP6619180B2 (ja) | 層状ビスマスカルコゲナイド系熱電変換材料及びその製造方法 | |
Radhika et al. | Synthesis, Structural Characterization and Thermoelectric Properties Of Sr2 (Srn-1TinO3n+ 1) n-Type Ceramic Materials | |
Toyoda et al. | High-temperature thermoelectric property of layered La2-2xCa1+ 2xMn2O7 manganites (0.75≤ x≤ 1.0) | |
Nakatsugawa et al. | High-temperature thermoelectric properties of Pr1− xSrxFeO3 (0.1≤ x≤ 0.7) | |
Klyndyuk et al. | Thermoelectric properties of some perovskite oxides | |
Buntham et al. | Effects of Bi0. 5Na0. 5TiO3 Dopant on Microstructure and Thermoelectric Properties of Na x CoO2 Ceramics | |
Hao et al. | Thermoelectric characteristics of Pb-and La-doped Bi2Ba2Co2Oy ceramics | |
Bakhshi et al. | Highly dense Sr 0.95 Sm 0.0125 Dy 0.0125□ 0.025 Ti 0.90 Nb 0.10 O 3±δ/ZrO 2 composite preparation directly through spark plasma sintering and its thermoelectric properties | |
Klyndyuk et al. | Spin-state transition in the layered barium cobaltite derivatives and their thermoelectric properties | |
Dahiya et al. | Study of high-temperature superconductivity | |
Giovannelli et al. | Thermoelectric properties of La7Mo7O30 sintered by reactive spark plasma sintering |
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: 09797854 Country of ref document: EP Kind code of ref document: A1 |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2010520839 Country of ref document: JP |
|
WWE | Wipo information: entry into national phase |
Ref document number: 13003149 Country of ref document: US |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
122 | Ep: pct application non-entry in european phase |
Ref document number: 09797854 Country of ref document: EP Kind code of ref document: A1 |