A method for producing a sintered R-T-B based magnet includes: preparing a sintered R-T-B based magnet work (R is a rare-earth element; and T is at least one selected from the group consisting of Fe, Co, Al, Mn and Si, and contains Fe with no exception); preparing an RL-RH-B-M based alloy; and a diffusion step of performing heat treatment while at least a portion of the RL-RH-B-M based alloy is attached to at least a portion of a surface of the sintered R-T-B based magnet work. In the RL-RH-B-M based alloy, the content of RL is 50 mass % or higher and 95 mass % or lower, the content of RH is 45 mass % or lower (including 0 mass %), the content of B is 0.1 mass % or higher and 3.0 mass % is lower; and the content of M is 4 mass % or higher and 49.9 mass % or lower.

A method for producing a sintered R-T-B based magnet includes: preparing a sintered R-T-B based magnet work (R is a rare-earth element; and T is at least one selected from the group consisting of Fe, Co, Al, Mn and Si, and contains Fe with no exception); preparing an RL-RH-B-M based alloy; and a diffusion step of performing heat treatment while at least a portion of the RL-RH-B-M based alloy is attached to at least a portion of a surface of the sintered R-T-B based magnet work. In the RL-RH-B-M based alloy, the content of RL is 50 mass % or higher and 95 mass % or lower, the content of RH is 45 mass % or lower (including 0 mass %), the content of B is 0.1 mass % or higher and 3.0 mass % is lower; and the content of M is 4 mass % or higher and 49.9 mass % or lower.

The disclosure describes a nanowire for an anode material of a lithium ion cell and a method of preparing the same. The nanowire includes silicon (Si) and germanium (Ge). The nanowire has a content of the silicon (Si) higher than a content of the germanium (Ge) at a surface thereof, and has the content of germanium (Ge) higher than the content of the silicon (Si) at an inner part thereof.

The disclosure describes a nanowire for an anode material of a lithium ion cell and a method of preparing the same. The nanowire includes silicon (Si) and germanium (Ge). The nanowire has a content of the silicon (Si) higher than a content of the germanium (Ge) at a surface thereof, and has the content of germanium (Ge) higher than the content of the silicon (Si) at an inner part thereof.

An object of the present invention is to provide a Mn-based alloy exhibiting metamagnetism over a wide temperature range. A Mn-based alloy according to the present invention is a MnAl alloy having metamagnetism. The metamagnetism refers to a property in which magnetism undergoes transition from paramagnetism or antiferromagnetism to ferromagnetism by a magnetic field. In the MnAl alloy, an antiferromagnetic state is adequately stable, so that by imparting AFM-FM transition type metamagnetism (the type of metamagnetism undergoing transition from antiferromagnetism to ferromagnetism), it is possible to obtain metamagnetism over a wide temperature range, particularly, over a temperature range of −100° C. to 200° C.

An object of the present invention is to provide a Mn-based alloy exhibiting metamagnetism over a wide temperature range. A Mn-based alloy according to the present invention is a MnAl alloy having metamagnetism. The metamagnetism refers to a property in which magnetism undergoes transition from paramagnetism or antiferromagnetism to ferromagnetism by a magnetic field. In the MnAl alloy, an antiferromagnetic state is adequately stable, so that by imparting AFM-FM transition type metamagnetism (the type of metamagnetism undergoing transition from antiferromagnetism to ferromagnetism), it is possible to obtain metamagnetism over a wide temperature range, particularly, over a temperature range of −100° C. to 200° C.

The present disclosure relates to methods for preparing TiMn-based or TiCrMn-based hydrogen storage alloys capable of absorbing and releasing hydrogen. In preferred embodiments the TiMn-based or TiCrMn-based hydrogen storage alloys comprise ferrovanadium (VFc).

A method for making a three-dimensional hierarchical layered porous copper, the method includes providing a copper-zinc alloy precursor being composed of a β′ phase and a γ phase, and treating the copper-zinc alloy precursor by electrochemical dealloying. The present application further provides a three-dimensional hierarchical layered porous copper including a first surface layer, an intermediate layer, and a second surface layer stacked in that order. The first surface layer includes a plurality of micron-scale pores and a plurality of first nanoscale pores. The intermediate layer includes a plurality of second nanoscale pores. The second surface layer includes the plurality of micron-scale pores and the plurality of first nanoscale pores.

A Cr—Ni alloy having high yield strength and high resistance to sulfuric acid general corrosion at a high temperature of 250° C. is provided. The Cr—Ni alloy has a chemical composition consisting of, in mass %, Si: 0.01 to 0.50%, Mn: 0.01 to 1.00%, Cr: 21.0 to 27.0%, Ni: 40.0 to less than 50.0%, Mo: 4.5 to less than 9.0%, W: 2.0 to 6.0%, Cu: more than 2.0% and not more than 6.0%, Co: 0.01 to 2.00%, one or two kinds selected from the group consisting of Ca and Mg: 0.001 to 0.010% in total, sol. Al: 0.005 to 0.200%, N: 0.01 to 0.20%, and the balance being Fe and impurities. The dislocation density in the Cr—Ni alloy satisfies the following Formula (1):
8.00×10.sup.14≤ρ≤2.50×10.sup.15+1.40×10.sup.14×[Cu+Co]  (1)

A Cr—Ni alloy having high yield strength and high resistance to sulfuric acid general corrosion at a high temperature of 250° C. is provided. The Cr—Ni alloy has a chemical composition consisting of, in mass %, Si: 0.01 to 0.50%, Mn: 0.01 to 1.00%, Cr: 21.0 to 27.0%, Ni: 40.0 to less than 50.0%, Mo: 4.5 to less than 9.0%, W: 2.0 to 6.0%, Cu: more than 2.0% and not more than 6.0%, Co: 0.01 to 2.00%, one or two kinds selected from the group consisting of Ca and Mg: 0.001 to 0.010% in total, sol. Al: 0.005 to 0.200%, N: 0.01 to 0.20%, and the balance being Fe and impurities. The dislocation density in the Cr—Ni alloy satisfies the following Formula (1):
8.00×10.sup.14≤ρ≤2.50×10.sup.15+1.40×10.sup.14×[Cu+Co]  (1)