Some variations provide an aluminum alloy feedstock for additive manufacturing, the aluminum alloy feedstock comprising from 79.8 wt % to 88.3 wt % aluminum; from 1.1 wt % to 2.1 wt % copper; from 3.0 wt % to 4.6 wt % magnesium; from 7.1 wt % to 9.0 wt % zinc; and from 0.5 wt % to 2.8 wt % zirconium as a grain-refiner element. The aluminum alloy feedstock may be in the form of an ingot powder. In some variations, the aluminum alloy feedstock comprises from 81.3 wt % to about 87.8 wt % aluminum; from 1.2 wt % to 2.0 wt % copper; from 3.2 wt % to 4.4 wt % magnesium; from 7.3 wt % to 8.7 wt % zinc; and from 0.5 wt % to 2.8 wt % zirconium.

The present disclosure relates generally to a method for improving the performance of sintered NdFeB magnet. A method of preparing a sintered NdFeB magnet therefore comprises the steps of: a) preparing alloy flakes from a raw material of the NdFeB magnet by a strip casting process; and b) preparing a coarse alloy powder from the alloy flakes by a hydrogen decrepitation process, the hydrogen decrepitation process including treatment of the alloy flakes under a hydrogen pressure of 0.10 MPa to 0.25 MPa for a duration of 1 to 3.5 hours, then degassing the hydrogen at a predetermined temperature between 300° C. to 400° C. for a duration time of 0.5 to 5 hours, and then mixing the resulting coarse alloy powder with a lubricant.

The present disclosure relates generally to a method for improving the performance of sintered NdFeB magnet. A method of preparing a sintered NdFeB magnet therefore comprises the steps of: a) preparing alloy flakes from a raw material of the NdFeB magnet by a strip casting process; and b) preparing a coarse alloy powder from the alloy flakes by a hydrogen decrepitation process, the hydrogen decrepitation process including treatment of the alloy flakes under a hydrogen pressure of 0.10 MPa to 0.25 MPa for a duration of 1 to 3.5 hours, then degassing the hydrogen at a predetermined temperature between 300° C. to 400° C. for a duration time of 0.5 to 5 hours, and then mixing the resulting coarse alloy powder with a lubricant.

An isostatic pressing canister for use in manufacturing a component by isostatic pressing is described. The canister comprises: a canister wall enclosing an internal cavity, the canister wall having an internal surface facing the internal cavity; a filling point for filling the internal cavity with powdered material, the filling point comprising a hole in the canister; and a structure supported within the internal cavity and located between the hole and the portion of the internal surface opposite the hole. A portion of the internal surface of the canister wall opposite the hole is shaped so that, during the filling of the internal cavity, powdered material falling from the hole and towards the portion of the internal surface is deflected away from the portion of the internal surface. A method of manufacturing a component using the canister is also described.

An isostatic pressing canister for use in manufacturing a component by isostatic pressing is described. The canister comprises: a canister wall enclosing an internal cavity, the canister wall having an internal surface facing the internal cavity; a filling point for filling the internal cavity with powdered material, the filling point comprising a hole in the canister; and a structure supported within the internal cavity and located between the hole and the portion of the internal surface opposite the hole. A portion of the internal surface of the canister wall opposite the hole is shaped so that, during the filling of the internal cavity, powdered material falling from the hole and towards the portion of the internal surface is deflected away from the portion of the internal surface. A method of manufacturing a component using the canister is also described.

The present invention relates to a method for producing a molybdenum alloy target, and solves the problem of low density and coarser grains of the molybdenum alloy targets in the prior art. The present invention comprises subjecting a mixed powder with a mass ratio depending upon the formula composition of a molybdenum alloy to a pre-press forming process to obtain a preformed molybdenum alloy target blank; placing the preformed molybdenum alloy target blank in a capsule and subjecting the capsule to processes of preheating for degassing and vacuum seal welding; subjecting the target blank to a hot isostatic pressing process to obtain a densified molybdenum alloy prefabricated target; removing the capsule; and subjecting the molybdenum alloy prefabricated target with the capsule removed to a temperature-rising and pressure-decreasing process, followed by finish machining to obtain a molybdenum alloy target.

The present invention relates to a method for producing a molybdenum alloy target, and solves the problem of low density and coarser grains of the molybdenum alloy targets in the prior art. The present invention comprises subjecting a mixed powder with a mass ratio depending upon the formula composition of a molybdenum alloy to a pre-press forming process to obtain a preformed molybdenum alloy target blank; placing the preformed molybdenum alloy target blank in a capsule and subjecting the capsule to processes of preheating for degassing and vacuum seal welding; subjecting the target blank to a hot isostatic pressing process to obtain a densified molybdenum alloy prefabricated target; removing the capsule; and subjecting the molybdenum alloy prefabricated target with the capsule removed to a temperature-rising and pressure-decreasing process, followed by finish machining to obtain a molybdenum alloy target.

A soft magnetic composite comprising an iron or iron alloy ferromagnetic material coated with an oxide material. An interface between the ferromagnetic material and the layer of oxide contains antiphase domain boundaries. Two processes for producing a soft magnetic composite are also provided. One process includes depositing an oxide layer onto an iron or iron alloy ferromagnetic material by molecular beam epitaxy at a partial oxygen pressure of from 1×10.sup.−5 Torr to 1×10.sup.−7 Torr to form a coated composite. The other process includes milling an iron or iron alloy ferromagnetic material powder and an oxide powder by high-energy milling to form a mixture; compacting the mixture and curing in an inert gas atmosphere at a temperature from 500° C. to 1200° C. to form a soft magnetic composite.

A soft magnetic composite comprising an iron or iron alloy ferromagnetic material coated with an oxide material. An interface between the ferromagnetic material and the layer of oxide contains antiphase domain boundaries. Two processes for producing a soft magnetic composite are also provided. One process includes depositing an oxide layer onto an iron or iron alloy ferromagnetic material by molecular beam epitaxy at a partial oxygen pressure of from 1×10.sup.−5 Torr to 1×10.sup.−7 Torr to form a coated composite. The other process includes milling an iron or iron alloy ferromagnetic material powder and an oxide powder by high-energy milling to form a mixture; compacting the mixture and curing in an inert gas atmosphere at a temperature from 500° C. to 1200° C. to form a soft magnetic composite.

The sheath (3) is a material, which includes an aluminium (Al) matrix, in which nanometric aluminium oxide particles (Al.sub.2O.sub.3) are homogenously dispersed, the content of Al.sub.2O.sub.3 is 0.25 to 5 vol. % and the balance is Al. It is preferred that Al.sub.2O.sub.3 originates from the surface layer present on Al powder used as feedstock material for consolidation. The superconductor based on magnesium diboride (MgB.sub.2) core (1) is fabricated by powder-in-tube or internal magnesium diffusion to boron technology, while the tube is the Al+Al.sub.2O.sub.3 composite, which is a product of powder metallurgy. A loose Al powder is pressed by cold isostatic pressing, and then the powder billet is degassed at elevated temperature and under vacuum, and then is hot extruded into a tube. A thin diffusion barrier (2) tube filled up with a mixture of Mg and B powders or Mg wire surrounded with B powder is placed into the Al+Al.sub.2O.sub.3 composite tube under inert gas or vacuum. Such composite unit is cold worked into a thin wire and then annealed at 625-655° C. for 8-90 min, what results in a formation superconducting MgB.sub.2 in a wire's core (1).