A sintered magnet body (R.sub.aT.sup.1.sub.bM.sub.cB.sub.d) coated with a powder mixture of an intermetallic compound (R.sup.1.sub.iM.sup.1.sub.j, R.sup.1.sub.xT.sup.2.sub.yM.sup.1.sub.z, R.sup.1.sub.iM.sup.1.sub.jH.sub.k), alloy (M.sup.1.sub.dM.sup.2.sub.e) or metal (M.sup.1) powder and a rare earth (R.sup.2) oxide is diffusion treated. The R.sup.2 oxide is partially reduced during the diffusion treatment, so a significant amount of R.sup.2 can be introduced near interfaces of primary phase grains within the magnet through the passages in the form of grain boundaries. The coercive force is increased while minimizing a decline of remanence.

A sintered magnet body (R.sub.aT.sup.1.sub.bM.sub.cB.sub.d) coated with a powder mixture of an intermetallic compound (R.sup.1.sub.iM.sup.1.sub.j, R.sup.1.sub.xT.sup.2.sub.yM.sup.1.sub.z, R.sup.1.sub.iM.sup.1.sub.jH.sub.k), alloy (M.sup.1.sub.dM.sup.2.sub.e) or metal (M.sup.1) powder and a rare earth (R.sup.2) oxide is diffusion treated. The R.sup.2 oxide is partially reduced during the diffusion treatment, so a significant amount of R.sup.2 can be introduced near interfaces of primary phase grains within the magnet through the passages in the form of grain boundaries. The coercive force is increased while minimizing a decline of remanence.

A sintered magnet body (R.sub.aT.sup.1.sub.bM.sub.cB.sub.d) coated with a powder mixture of an intermetallic compound (R.sup.1.sub.iM.sup.1.sub.j, R.sup.1.sub.xT.sup.2.sub.yM.sup.1.sub.z, R.sup.1.sub.iM.sup.1.sub.jH.sub.k), alloy (M.sup.1.sub.dM.sup.2.sub.e) or metal (M.sup.1) powder and a rare earth (R.sup.2) oxide is diffusion treated. The R.sup.2 oxide is partially reduced during the diffusion treatment, so a significant amount of R.sup.2 can be introduced near interfaces of primary phase grains within the magnet through the passages in the form of grain boundaries. The coercive force is increased while minimizing a decline of remanence.

A sintered magnet body (R.sub.aT.sup.1.sub.bM.sub.cB.sub.d) coated with a powder mixture of an intermetallic compound (R.sup.1.sub.iM.sup.1.sub.j, R.sup.1.sub.xT.sup.2.sub.yM.sup.1.sub.z, R.sup.1.sub.iM.sup.1.sub.jH.sub.k), alloy (M.sup.1.sub.dM.sup.2.sub.e) or metal (M.sup.1) powder and a rare earth (R.sup.2) oxide is diffusion treated. The R.sup.2 oxide is partially reduced during the diffusion treatment, so a significant amount of R.sup.2 can be introduced near interfaces of primary phase grains within the magnet through the passages in the form of grain boundaries. The coercive force is increased while minimizing a decline of remanence.

The production of steel components in an additive process using a steel powder having a mean grain diameter of 5-150 m, and comprising (in wt % ) 0.08-0.35% C, up to 0.80% Si, 0.20-2.00% Mn, up to 4.00% Cr, 0.3-3.0% Mo, 0.004-0.020% N, 0.004-0.050% Al, up to 0.0025% B, up to 0.20% Nb, up to 0.02% Ti, up 0.40% V, up to 1.5% Ni, up to 0.3% Cu, up to 2.0% Co, at least one of Nb, Ti, V, and S, wherein Nb is 0.003-0.20%, Ti is 0.001-0.02%, V is 0.02-0.40% and/or S is 0.001-0.4%, and the remainder being iron and unavoidable impurities, where % Al/27+% Nb/45+% Ti/48+% V/25>% N/3.5. The steel component has a structure including at least 80 vol % of bainite, with the remainder being retained austenite, ferrite, perlite and/or martensite. and after shaping and before an optional heat treatment, has a tensile strength of 900 MPa, a yield strength of 560 MPa and an elongation at break A5.65 of 8%.

Hydrogen storage materials being inexpensive and having hydrogen absorption (storage) and desorption properties suitable for hydrogen storage are provided. The hydrogen storage materials have alloys with an elemental composition of Formula (1), a hydrogen storage container containing the hydrogen storage material, and a hydrogen supply apparatus including the hydrogen storage container:

La.sub.aCe.sub.bSm.sub.cNi.sub.dM.sub.e (1)

wherein M is Mn or both of Mn and Co, a satisfies 0.60a0.90, b satisfies 0b0.30, c satisfies 0.05c0.25, d satisfies 4.75d5.20, e satisfies 0.05e0.40, a+b+c=1, and d+e satisfies 5.10d+e5.35.

A method is provided for the heat treatment of an object comprising at least one rare-earth element with a high vapor pressure. One or more objects comprising at least one rare-earth element with a high vapor pressure are arranged in an interior of a package. An external source of the at least one rare-earth element is arranged so as to compensate for the evaporation of this same rare-earth element from the object and/or to increase the vapor pressure of the rare-earth element in the interior of the package, and the package is heat treated.

A permanent magnet having excellent magnetic properties and a device including such a permanent magnet are provided. A permanent magnet consists of a sintered compact having a composition consisting of R: 23 to 27 wt % (R is a sum total of rare-earth elements including at least Sm), Fe: 22 to 27 wt %, Mn: 0.3 to 2.5 wt %, Cu: 4.0 to 5.0 wt %, and a remainder consisting of Co and unavoidable impurities, in which the sintered compact contains a plurality of crystal grains and grain boundary phases, and a concentration of Cu in at least a part of the grain boundary phases is 45 at % or higher.

Formulations of reactive materials, such as aluminum, magnesium and alloys thereof, with combustible additives such as wood derivatives or charcoal, provide a composition for neutralizing energetic materials via combustion. Specifically, explosive substances such as ammonium nitrate and urea nitrate, which are commonly used as homemade explosives, are rapidly incinerated in a non-propagating manner by the contact with burning reactive material formulations.

Disclosed are a nickel-based superalloy formed by selective laser melting and a preparation method thereof, belonging to the technical field of an additive manufacturing from metal powder. In the disclosure, CrFeNb alloy powder is used as a grain refiner, and its element composition is within the composition range of a nickel-based superalloy powder to ensure that the prepared nickel-based superalloy has the same element composition with the original alloy; the grain size in the nickel-based superalloy could be refined by the addition of CrFeNb alloy powder, such that the anisotropic columnar grain structure in the alloy is transformed to equiaxed grain structure, thereby improving mechanical properties of the alloy. The results of the examples show that the nickel-based superalloy prepared in the disclosure exhibits a yield strength of not less than 710 MPa at room temperature, a tensile strength of not less than 1010 MPa, an elongation of not less than 19%, and a hardness of not less than 330 HV; after the heat treatment, the nickel-based superalloy exhibits a yield strength of not less than 1400 MPa, a tensile strength of not less than 1100 MPa, an elongation of not less than 5.09%, and a hardness of not less than 530 HV.