A preparation method of cemented carbide with FeCoCu medium-entropy alloy as binding phase is provided. The preparation method includes: 1) preparing FeCoCu precursor powders by solution combustion synthesis; 2) preparing FeCoCu medium-entropy alloy powders by mechanical alloying; 3) evenly mixing the FeCoCu medium-entropy alloy powders with ultra-fine WC powders and a binder to obtain mixed powders and pressing the mixed powders into a shaped green body; 4) preparing a WC-FeCoCu cemented carbide by microwave sintering after removing the binder from the shaped green body. The preparation method reduces sintering temperature and time and obtains a new-type cemented carbide with fine grains, high hardness and good toughness while reducing the cost.

Reactor configurations may include one or more staged inlets and/or one or more staged outlets for gaseous and solid feedstocks. In one embodiment of the present disclosure, a reactor design for gas-solid reaction with one or more additional outlet for gas and/or solid phase is provided. In yet another embodiment, the design for a gas-solid reactor with one side inlet and two outlets for gas phase is described. In one embodiment, a reactor design with pairs of inlet and outlet for both gas and solid phase is provided. In another embodiment, a reactor design with one or more side inlets but only one outlet for gas phase is provided. In yet another embodiment, a reactor design with two inlets at the top/bottom of reactor and two side outlets for gaseous phase is described. In yet another embodiment, a reactor design with one or more side inlets and outlets for both gas and solid phases is provided.

Reactor configurations may include one or more staged inlets and/or one or more staged outlets for gaseous and solid feedstocks. In one embodiment of the present disclosure, a reactor design for gas-solid reaction with one or more additional outlet for gas and/or solid phase is provided. In yet another embodiment, the design for a gas-solid reactor with one side inlet and two outlets for gas phase is described. In one embodiment, a reactor design with pairs of inlet and outlet for both gas and solid phase is provided. In another embodiment, a reactor design with one or more side inlets but only one outlet for gas phase is provided. In yet another embodiment, a reactor design with two inlets at the top/bottom of reactor and two side outlets for gaseous phase is described. In yet another embodiment, a reactor design with one or more side inlets and outlets for both gas and solid phases is provided.

A powder for producing a superconducting component. The powder includes Nb.sub.xSn.sub.y, where 1≤x≤6 and 1≤y≤5. The powder does not have any separate NbO phases and/or SnO phases.

A powder for producing a superconducting component. The powder includes Nb.sub.xSn.sub.y, where 1≤x≤6 and 1≤y≤5. The powder does not have any separate NbO phases and/or SnO phases.

A powder for the production of a superconducting component. The powder includes Nb.sub.xSn.sub.y, where 1≤x≤6 and 1≤y≤5, and three-dimensional agglomerates having a particle size D90 of less than 400 μm, as determined via a laser light scattering. The three-dimensional agglomerates have primary particles which have an average particle diameter of less than 15 μm, as determined via a scanning electron microscopy, and pores of which at least 90% have a diameter of from 0.1 to 20 μm, as determined via a mercury porosimetry.

A powder for the production of a superconducting component. The powder includes Nb.sub.xSn.sub.y, where 1≤x≤6 and 1≤y≤5, and three-dimensional agglomerates having a particle size D90 of less than 400 μm, as determined via a laser light scattering. The three-dimensional agglomerates have primary particles which have an average particle diameter of less than 15 μm, as determined via a scanning electron microscopy, and pores of which at least 90% have a diameter of from 0.1 to 20 μm, as determined via a mercury porosimetry.

A powder for the production of a superconducting component. The powder includes Nb.sub.xSn.sub.y, where 1≤x≤6 and 1≤y≤5, and three-dimensional agglomerates having a particle size D90 of less than 400 μm, as determined via a laser light scattering. The three-dimensional agglomerates have primary particles which have an average particle diameter of less than 15 μm, as determined via a scanning electron microscopy, and pores of which at least 90% have a diameter of from 0.1 to 20 μm, as determined via a mercury porosimetry.

Disclosed is a nano dispersion copper alloy with high air-tightness and low free oxygen content and a brief manufacturing process thereof, wherein alloy comprises the following components: Al.sub.2O.sub.3, Ca and La. The manufacturing process comprises the following steps of: preparing Cu—Al.sub.2O.sub.3 alloy powder by an internal oxidation method; mixing the Cu—Al.sub.2O.sub.3 alloy powder with Cu—Ca—La alloy powder; sheathing the mixed powder under protection of argon; performing hot extrusion and then rotary forging; vacuumizing the sheath after the rotary forging; and sealing and placing the sheath in a nitrogen atmosphere with a temperature of 450° C. to 550° C. and a pressure intensity of 40 Mpa to 60 Mpa for 3 hours to 5 hours. The dispersion copper prepared by the present disclosure has the advantages of low free oxygen content (≤15 ppm), high dimensional stability, good air-tightness and an air leakage rate≤1.0×10.sup.−10 Pa m.sup.3/s after hydrogen annealing.

Disclosed is a nano dispersion copper alloy with high air-tightness and low free oxygen content and a brief manufacturing process thereof, wherein alloy comprises the following components: Al.sub.2O.sub.3, Ca and La. The manufacturing process comprises the following steps of: preparing Cu—Al.sub.2O.sub.3 alloy powder by an internal oxidation method; mixing the Cu—Al.sub.2O.sub.3 alloy powder with Cu—Ca—La alloy powder; sheathing the mixed powder under protection of argon; performing hot extrusion and then rotary forging; vacuumizing the sheath after the rotary forging; and sealing and placing the sheath in a nitrogen atmosphere with a temperature of 450° C. to 550° C. and a pressure intensity of 40 Mpa to 60 Mpa for 3 hours to 5 hours. The dispersion copper prepared by the present disclosure has the advantages of low free oxygen content (≤15 ppm), high dimensional stability, good air-tightness and an air leakage rate≤1.0×10.sup.−10 Pa m.sup.3/s after hydrogen annealing.