Abstract: Provided is a magnetic refrigeration material whose magnetic transition temperature has been adjusted with high accuracy and which includes at least a first predetermined magnetic refrigeration material and a second predetermined magnetic refrigeration material which differs from the first magnetic refrigeration material. The absolute value of the difference between the magnetic transition temperature of the present magnetic refrigeration material and a target magnetic transition temperature is 0.7 K or less. The content of the first magnetic refrigeration material and the content of the second magnetic refrigeration material are determined by the magnetic transition temperatures of the first magnetic refrigeration material and the second magnetic refrigeration material and by a target magnetic transition temperature of the magnetic refrigeration material.

Abstract: An insulation layer forming-composition including boehmite, a binder, and an organic solvent, wherein when a thermogravimetric analysis is performed on the boehmite and measurement is conducted at a temperature elevation rate of 10° C./min under an air flow, the weight reduction percentage in a range of 200-450° C. is 10.0 mass % or less, and the weight reduction percentage in a range of 450-600° C. is 5.0-13.5 mass %.

Abstract: Provided is a magnetic refrigeration material whose magnetic transition temperature has been adjusted with high accuracy and which includes at least a first predetermined magnetic refrigeration material and a second predetermined magnetic refrigeration material which differs from the first magnetic refrigeration material. The absolute value of the difference between the magnetic transition temperature of the present magnetic refrigeration material and a target magnetic transition temperature is 0.7 K or less. The content of the first magnetic refrigeration material and the content of the second magnetic refrigeration material are determined by the magnetic transition temperatures of the first magnetic refrigeration material and the second magnetic refrigeration material and by a target magnetic transition temperature of the magnetic refrigeration material.

Abstract: There are provided a method for producing a magnetic refrigeration material whose magnetic transition temperature can be adjusted with high accuracy, and a magnetic refrigeration material whose magnetic transition temperature has been adjusted with high accuracy. The magnetic refrigeration material production method of the present invention includes the steps of: preparing a first predetermined magnetic refrigeration material and a second predetermined magnetic refrigeration material which differs from the first magnetic refrigeration material; and mixing the first magnetic refrigeration material and the second magnetic refrigeration material to obtain a third magnetic refrigeration material.

Abstract: There are provided a method for producing a magnetic refrigeration material whose magnetic transition temperature can be adjusted with high accuracy, and a magnetic refrigeration material whose magnetic transition temperature has been adjusted with high accuracy. The magnetic refrigeration material production method of the present invention includes the steps of: preparing a first predetermined magnetic refrigeration material and a second predetermined magnetic refrigeration material which differs from the first magnetic refrigeration material; and mixing the first magnetic refrigeration material and the second magnetic refrigeration material to obtain a third magnetic refrigeration material.

Abstract: The present invention provides a rare-earth sintered magnet that is characterized in that: R (R indicates one or more elements selected from rare-earth elements, wherein Nd is essential), T (T indicates one or more elements selected from iron-group elements, wherein Fe is essential), X (X indicates one or two elements selected from B and C, wherein B is essential), M1 (M1 indicates one or more elements selected from Al, Si, Cr, Mn, Cu, Zn, Ga, Ge, Mo, Sn, W, Pb, and Bi), 0.1 mass % or less of O, 0.05 mass % or less of N, and 0.07 mass % or less of C are contained; the average crystal grain size is 4.0 ?m or less; and relational expression (1) 0.26×D+97?Or?0.26×D+99 is satisfied assuming that the degree of orientation is Or [%] and that the average crystal grain size is D [?m]. With this rare-earth sintered magnet, it is possible to achieve superior magnetic characteristics in which both high Br and high HcJ are achieved.

Abstract: The present invention provides a rare earth sintered magnet which contains R (R represents one or more rare earth elements essentially including Nd), T (T represents one or more iron group elements essentially including Fe), B, M1 (M1 represents one or more elements selected from among Al, Si, Cr, Mn, Cu, Zn, Ga, Ge, Mo, Sn, W, Pb and Bi) and M2 (M2 represents one or more elements selected from among Ti, V, Zr, Nb, Hf and Ta), while comprising an R2T14B phase as the main phase. This rare earth sintered magnet is characterized in that: the M1 is in an amount of from 0.5% by atom to 2% by atom; if (R), (T), (M2) and (B) are the respective atomic percentages of the above-described R, T, M2 and B, the relational expression (1) ((T)/14)+(M2)?(B)?((R)/2)+((M2)/2) is satisfied; and from 0.1% by volume to 10% by volume of all grain boundary phases in the magnet is composed of an R6T13M1 phase.

Abstract: An R—Fe—B base sintered magnet is provided comprising a main phase containing an HR rich phase of (R?,HR)2(Fe,(Co))14B wherein R? is an element selected from yttrium and rare earth elements exclusive of Dy, Tb and Ho, and essentially contains Nd, and HR is an element selected from Dy, Tb and Ho, and a grain boundary phase containing a (R?,HR)—Fe(Co)-M1 phase in the form of an amorphous phase and/or nanocrystalline phase, the (R?,HR)—Fe(Co)-M1 phase consisting essentially of 25-35 at % of (R?,HR), 2-8 at % of M1 which is at least one element selected from Si, Al, Mn, Ni, Cu, Zn, Ga, Ge, Pd, Ag, Cd, In, Sn, Sb, Pt, Au, Hg, Pb, and Bi, up to 8 at % of Co, and the balance of Fe. The HR rich phase has a higher HR content than the HR content of the main phase at its center. The magnet produces a high coercivity despite a low content of Dy, Tb and Ho.

Abstract: An R—Fe—B base sintered magnet is provided consisting essentially of R (which is at least two rare earth elements and essentially contains Nd and Pr), M1 which is at least two of Si, Al, Mn, Ni, Cu, Zn, Ga, Ge, Pd, Ag, Cd, In, Sn, Sb, Pt, Au, Hg, Pb, and Bi, M2 which is at least one of Ti, V, Cr, Zr, Nb, Mo, Hf, Ta, and W, boron, and the balance of Fe, and containing an intermetallic compound R2(Fe,(Co))14B as a main phase. The magnet contains an R—Fe(Co)-M1 phase as a grain boundary phase, the R—Fe(Co)-M1 phase contains A phase which is crystalline with crystallites of at least 10 nm formed at grain boundary triple junctions, and B phase which is amorphous and/or nanocrystalline with crystallites of less than 10 nm formed at intergranular grain boundaries and optionally grain boundary triple junctions.

Abstract: A rare earth sintered magnet is prepared by a method comprising the steps of melting raw materials to form an alloy, pulverizing the alloy into a fine powder, shaping the fine powder into a compact, and sintering the compact. The pulverizing step includes a coarse pulverizing step including hydrogen decrepitation and a fine pulverizing step, and further includes the step of adding a lubricant. The sintering step includes an atmosphere heat treatment including heating the compact at a temperature from the lubricant decomposition temperature to the sintering temperature and holding at the temperature for a time, in an inert gas atmosphere, and a vacuum heat treatment. The sintered magnet has a low impurity concentration and a narrow carbon concentration distribution.

Abstract: An R—Fe—B base sintered magnet is prepared through the steps of providing an alloy fine powder having a predetermined composition, compression shaping the alloy fine powder in an applied magnetic field into a compact, sintering the compact at a temperature of 900-1,250° C. into a sintered body, cooling the sintered body to 400° C. or below, high-temperature heat treatment including placing a metal, compound or intermetallic compound containing HR which is Dy, Tb and/or Ho, on the surface of the sintered body, heating at a temperature from more than 950° C. to 1,100° C., for causing grain boundary diffusion of HR into the sintered body, and cooling to 400° C. or below, and low-temperature heat treatment including heating at a temperature of 400-600° C. and cooling to 300° C. or below. The sintered magnet produces a high coercivity despite a low content of Dy, Tb and Ho.

Abstract: An R—Fe—B base sintered magnet is provided comprising a main phase containing an HR rich phase of (R?,HR)2(Fe,(Co))14B wherein R? is an element selected from yttrium and rare earth elements exclusive of Dy, Tb and Ho, and essentially contains Nd, and HR is an element selected from Dy, Tb and Ho, and a grain boundary phase containing a (R?,HR)—Fe(Co)-M1 phase in the form of an amorphous phase and/or nanocrystalline phase, the (R?,HR)—Fe(Co)-M1 phase consisting essentially of 25-35 at % of (R?,HR), 2-8 at % of M1 which is at least one element selected from Si, Al, Mn, Ni, Cu, Zn, Ga, Ge, Pd, Ag, Cd, In, Sn, Sb, Pt, Au, Hg, Pb, and Bi, up to 8 at % of Co, and the balance of Fe. The HR rich phase has a higher HR content than the HR content of the main phase at its center. The magnet produces a high coercivity despite a low content of Dy, Tb and Ho.

Abstract: An R—Fe—B base sintered magnet is provided comprising a main phase containing an HR rich phase of (R?, HR)2(Fe,(Co))14B wherein R? is an element selected from yttrium and rare earth elements exclusive of Dy, Tb and Ho, and essentially contains Nd, and HR is an element selected from Dy, Tb and Ho, and a grain boundary phase containing a (R?, HR)—Fe(Co)-M1 phase in the form of an amorphous phase and/or nanocrystalline phase, the (R?, HR)—Fe(Co)-M1 phase consisting essentially of 25-35 at % of (R?, HR), 2-8 at % of M1 which is at least one element selected from Si, Al, Mn, Ni, Cu, Zn, Ga, Ge, Pd, Ag, Cd, In, Sn, Sb, Pt, Au, Hg, Pb, and Bi, up to 8 at % of Co, and the balance of Fe. The HR rich phase has a higher HR content than the HR content of the main phase at its center. The magnet produces a high coercivity despite a low content of Dy, Tb and Ho.

Abstract: The invention provides an R—Fe—B sintered magnet consisting essentially of 12-17 at % of Nd, Pr and R, 0.1-3 at % of M1, 0.05-0.5 at % of M2, 4.8+2*m to 5.9+2*m at % of B, and the balance of Fe, containing R2(Fe,(Co))14B intermetallic compound as a main phase, and having a core/shell structure that the main phase is covered with a grain boundary phases. The sintered magnet has an average grain size of less than 6 ?m, a crystal orientation of more than 98%, and a degree of magnetization of more than 96%, and exhibits a coercivity of at least 10 kOe despite a low or nil content of Dy, Tb, and Ho.

Abstract: The invention provides an R—Fe—B sintered magnet consisting essentially of 12-17 at % of Nd, Pr and R, 0.1-3 at % of M1, 0.05-0.5 at % of M2, 4.8+2*m to 5.9+2*m at % of B, and the balance of Fe, containing R2(Fe,(Co))14B intermetallic compound as a main phase, and having a core/shell structure that the main phase is covered with grain boundary phases. The sintered magnet exhibits a coercivity of at least 10 kOe despite a low or nil content of Dy, Tb and Ho.

Abstract: An R—Fe—B base sintered magnet is provided comprising a main phase containing an HR rich phase of (R?, HR)2(Fe,(Co))14B wherein R? is an element selected from yttrium and rare earth elements exclusive of Dy, Tb and Ho, and essentially contains Nd, and HR is an element selected from Dy, Tb and Ho, and a grain boundary phase containing a (R?, HR)—Fe(Co)-M1 phase in the form of an amorphous phase and/or nanocrystalline phase, the (R?, HR)—Fe(Co)-M1 phase consisting essentially of 25-35 at % of (R?, HR), 2-8 at % of M1 which is at least one element selected from Si, Al, Mn, Ni, Cu, Zn, Ga, Ge, Pd, Ag, Cd, In, Sn, Sb, Pt, Au, Hg, Pb, and Bi, up to 8 at % of Co, and the balance of Fe. The HR rich phase has a higher HR content than the HR content of the main phase at its center. The magnet produces a high coercivity despite a low content of Dy, Tb and Ho.

Abstract: An R—Fe—B base sintered magnet is prepared through the steps of providing an alloy fine powder having a predetermined composition, compression shaping the alloy fine powder in an applied magnetic field into a compact, sintering the compact at a temperature of 900-1,250° C. into a sintered body, cooling the sintered body to 400° C. or below, high-temperature heat treatment including placing a metal, compound or intermetallic compound containing HR which is Dy, Tb and/or Ho, on the surface of the sintered body, heating at a temperature from more than 950° C. to 1,100° C., for causing grain boundary diffusion of HR into the sintered body, and cooling to 400° C. or below, and low-temperature heat treatment including heating at a temperature of 400-600° C. and cooling to 300° C. or below. The sintered magnet produces a high coercivity despite a low content of Dy, Tb and Ho.

Abstract: The invention provides an R—Fe—B sintered magnet consisting essentially of 12-17 at % of R, 0.1-3 at % of M1, 0.05-0.5 at % of M2, 4.8+2*m to 5.9+2*m at % of B, and the balance of Fe, containing R2(Fe,(Co))14B intermetallic compound as a main phase, and having a core/shell structure that the main phase is covered with a HR-rich layer and a (R,HR)—Fe(Co)-M1 phase wherein HR is Tb, Dy or Ho. The sintered magnet exhibits a coercivity ?10 kOe despite a low content of Dy, Tb, and Ho.

Abstract: An R—Fe—B base sintered magnet is provided consisting essentially of R (which is at least two rare earth elements and essentially contains Nd and Pr), M1 which is at least two of Si, Al, Mn, Ni, Cu, Zn, Ga, Ge, Pd, Ag, Cd, In, Sn, Sb, Pt, Au, Hg, Pb, and Bi, M2 which is at least one of Ti, V, Cr, Zr, Nb, Mo, Hf, Ta, and W, boron, and the balance of Fe, and containing an intermetallic compound R2(Fe,(Co))14B as a main phase. The magnet contains an R—Fe(Co)-M1 phase as a grain boundary phase, the R—Fe(Co)-M1 phase contains A phase which is crystalline with crystallites of at least 10 nm formed at grain boundary triple junctions, and B phase which is amorphous and/or nanocrystalline with crystallites of less than 10 nm formed at intergranular grain boundaries and optionally grain boundary triple junctions.

Abstract: A carbon porous body has a micropore volume, calculated from an ?s plot analysis of a nitrogen adsorption isotherm at a temperature of 77 K, of 0.1 cm3/g or less, the micropore volume being smaller than a mesopore volume calculated by subtracting the micropore volume from a nitrogen adsorption amount at a nitrogen relative pressure P/P0 of 0.97 on the nitrogen adsorption isotherm, wherein a nitrogen adsorption amount at a nitrogen relative pressure P/P0 of 0.5 on the nitrogen adsorption isotherm is within a range of 500 cm3 (STP)/g or less, and a nitrogen adsorption amount at a nitrogen relative pressure P/P0 of 0.85 on the nitrogen adsorption isotherm is within a range of 600 cm3 (STP)/g or more and 1100 cm3 (STP)/g or less.