Disclosed are an R-T-B-based permanent magnet material, a preparation method therefor and the use thereof. The R-T-B-based permanent magnet material comprises R, B, M, Fe, Co, X and inevitable impurities, wherein: (1) R is a rare earth element, and the R includes at least Nd and RH, M being one or more of Ti, Zr and Nb, and X including Cu, “Al and/or Ga”; and (2) in percentage by weight, R: 30.5-32.0 wt%, B: 0.95-0.99 wt%, M: 0.3-0.6 wt%, X: 0.8-1.8 wt%, and Cu: 0.35-0.50 wt%, and the balance is Fe, Co and inevitable impurities. According to the present invention, under the condition of 0.3-0.6 wt% of a high melting point metal, a permanent magnet material with an excellent magnet performance and a good squareness is obtained.

Disclosed are an R-T-B-based permanent magnet material, a preparation method therefor and the use thereof. The R-T-B-based permanent magnet material comprises R, B, M, Fe, Co, X and inevitable impurities, wherein: (1) R is a rare earth element, and the R includes at least Nd and RH, M being one or more of Ti, Zr and Nb, and X including Cu, “Al and/or Ga”; and (2) in percentage by weight, R: 30.5-32.0 wt%, B: 0.95-0.99 wt%, M: 0.3-0.6 wt%, X: 0.8-1.8 wt%, and Cu: 0.35-0.50 wt%, and the balance is Fe, Co and inevitable impurities. According to the present invention, under the condition of 0.3-0.6 wt% of a high melting point metal, a permanent magnet material with an excellent magnet performance and a good squareness is obtained.

The present disclosure discloses a preparation method of a powder metallurgy (PM) superalloy with high strength and plasticity. Under the multi-field coupling action of a thermal field and a force field, the PM superalloy is obtained in a high-temperature graphite mold by using the method of conducting heat preservation and oscillating-pressure sintering in two steps. Under the action of a circulating pressure, rearrangement of powders and discharge of pores are promoted, and therefore, the PM superalloy is sintered and formed. The present disclosure further discloses a PM superalloy prepared by using the method above. The PM superalloy has the characteristics of low grade of prior particle boundary defects, uniform grain refinement and high density. The sintered PM superalloy obtained in the present disclosure has a yield strength of 955 MPa, a tensile strength of 1,437 MPa and an elongation of 31.9%, and has high strength and plasticity.

The present disclosure discloses a preparation method of a powder metallurgy (PM) superalloy with high strength and plasticity. Under the multi-field coupling action of a thermal field and a force field, the PM superalloy is obtained in a high-temperature graphite mold by using the method of conducting heat preservation and oscillating-pressure sintering in two steps. Under the action of a circulating pressure, rearrangement of powders and discharge of pores are promoted, and therefore, the PM superalloy is sintered and formed. The present disclosure further discloses a PM superalloy prepared by using the method above. The PM superalloy has the characteristics of low grade of prior particle boundary defects, uniform grain refinement and high density. The sintered PM superalloy obtained in the present disclosure has a yield strength of 955 MPa, a tensile strength of 1,437 MPa and an elongation of 31.9%, and has high strength and plasticity.

A composite VC heat sink containing a copper/diamond composite wick structure and a method for preparing the same are provided. The VC heat sink includes a lower shell plate. The lower shell plate is provided with a recess at a center position of an inner surface and provided with a boss with a same plane size as the recess at a center position of an outer surface, and a surface of the boss or a surface of the recess is provided with a copper/diamond composite plate. The copper/diamond composite wick structure has a three-dimensional porous structure and uses a copper/diamond sintered body as a matrix, a surface of the matrix is provided with a diamond layer, and a surface of the diamond layer is provided with a metal hydrophilic layer. The heat dissipation performance of the composite VC heat sink is maximized under the cooperation of structure and materials.

A vacuum pump that evacuates an inside of a vacuum chamber and powder capturing devices disposed on an intake side of the vacuum pump are included. The powder capturing devices include a plurality of flow path forming units that form a continuous gas flow path from an intake unit located on the vacuum chamber side to an exhaust unit located on the vacuum pump side. The plurality of flow path forming units include a first flow path forming unit having a first catching unit that causes the powder sucked from the intake unit to collide and then catch the powder, and a second flow path forming unit having a second catching unit that causes the powder passing through the first flow path forming unit to collide and then catch the powder.

A vacuum pump that evacuates an inside of a vacuum chamber and powder capturing devices disposed on an intake side of the vacuum pump are included. The powder capturing devices include a plurality of flow path forming units that form a continuous gas flow path from an intake unit located on the vacuum chamber side to an exhaust unit located on the vacuum pump side. The plurality of flow path forming units include a first flow path forming unit having a first catching unit that causes the powder sucked from the intake unit to collide and then catch the powder, and a second flow path forming unit having a second catching unit that causes the powder passing through the first flow path forming unit to collide and then catch the powder.

Described herein are compositions, methods, and systems for printing metal three-dimensional objects. In an example, described is a method of printing a three-dimensional object comprising: (i) depositing a metal powder build material, wherein the metal powder build material has an average particle size of from about 10 μm to about 250 μm; (ii) selectively applying a binder fluid on at least a portion of the metal powder build material, wherein the binder fluid comprises an aqueous liquid vehicle and latex polymer particles dispersed in the aqueous liquid vehicle; (iii) heating the selectively applied binder fluid on the metal powder build material to a temperature of from about 40° C. to about 180° C.; and (iv) repeating (i), (ii), and (iii) at least one time to form the three-dimensional object.

Described herein are compositions, methods, and systems for printing metal three-dimensional objects. In an example, described is a method of printing a three-dimensional object comprising: (i) depositing a metal powder build material, wherein the metal powder build material has an average particle size of from about 10 μm to about 250 μm; (ii) selectively applying a binder fluid on at least a portion of the metal powder build material, wherein the binder fluid comprises an aqueous liquid vehicle and latex polymer particles dispersed in the aqueous liquid vehicle; (iii) heating the selectively applied binder fluid on the metal powder build material to a temperature of from about 40° C. to about 180° C.; and (iv) repeating (i), (ii), and (iii) at least one time to form the three-dimensional object.

Methodologies and manufacturing processes to manufacture components by electron beam melting additive manufacturing, particularly components of molybdenum or a molybdenum-based alloy and particularly of complex nuclear component geometries. Input parameters are provided for controlling electron beam melting additive manufacturing equipment, such as electron beam melting machines. The input parameters relate to various process steps, including build set-up, initial thermal treatment, initial layering of powder, pre-consolidation thermal treatment, consolidation, post-consolidation thermal treatment, indexing of layers, and post-build thermal treatment. The methodologies and manufacturing processes allow manufacture of components of molybdenum having a purity of ≥99.0% and a density of ≥99.75%. Metallographic cross-sections of the manufactured molybdenum components were porosity-free and crack-free.