The present invention relates to an alloy with formula of RE-M-B—Fe as defined herein and oxygen content less than 0.9 wt %, wherein said RE is in the range of 29.0 weight % to 33.0 weight %; M is in the range of 0.25 weight % to 1.0 weight %; B is in the range of 0.8 weight % to 1.1 weight %; and Fe makes up the balance. The present invention also relates to a method for preparing a RE-M-Fe—B magnetic powder, as defined herein comprising the steps of: (a) melt spinning a RE-M-Fe—B alloy composition to obtain a melt-spun powder; (b) pressing the melt-spun powder of step (a) to obtain a compact body; (c) hot deforming the compact body of step (b) to obtain a die-upset magnet; (d) crushing the die-upset magnet of step (c) to obtain a powder; (e) milling and sieving the powder of step (d); and (f) passivating the powder of step (e) to obtain a magnetic powder; wherein: each of steps (d) to (f) is performed under a low oxygen environment and transfer between each of steps (d) to (f) is a sealed transfer; and wherein the oxygen content of the low oxygen environment and during each sealed transfer is below 0.5 weight %.

The present invention relates to an alloy with formula of RE-M-B—Fe as defined herein and oxygen content less than 0.9 wt %, wherein said RE is in the range of 29.0 weight % to 33.0 weight %; M is in the range of 0.25 weight % to 1.0 weight %; B is in the range of 0.8 weight % to 1.1 weight %; and Fe makes up the balance. The present invention also relates to a method for preparing a RE-M-Fe—B magnetic powder, as defined herein comprising the steps of: (a) melt spinning a RE-M-Fe—B alloy composition to obtain a melt-spun powder; (b) pressing the melt-spun powder of step (a) to obtain a compact body; (c) hot deforming the compact body of step (b) to obtain a die-upset magnet; (d) crushing the die-upset magnet of step (c) to obtain a powder; (e) milling and sieving the powder of step (d); and (f) passivating the powder of step (e) to obtain a magnetic powder; wherein: each of steps (d) to (f) is performed under a low oxygen environment and transfer between each of steps (d) to (f) is a sealed transfer; and wherein the oxygen content of the low oxygen environment and during each sealed transfer is below 0.5 weight %.

A production method of particulate materials, through centrifugal atomization (CA) is disclosed. The method is suitable for obtaining fine spherical powders with exceptional morphological quality and extremely low content, or even absence, of nonspherical shape particles and internal voids. An appropriate cost effective method for industrial scale production of metal alloy, intermetallic, metal matrix composite or metal-like material powders in large batches is also disclosed. The atomization technique can be extended to other than the centrifugal atomization with rotating element techniques.

A spherical powder for manufacturing a three-dimensional component. The spherical powder is an alloy powder which has at least two refractory metals. The alloy powder has a homogeneous microstructure and at least two crystalline phases.

A spherical powder for manufacturing a three-dimensional component. The spherical powder is an alloy powder which has at least two refractory metals. The alloy powder has a homogeneous microstructure and at least two crystalline phases.

A Super Invar alloy includes Ni of 30 to 35 percent by mass, Co of 3 to 6 percent by mass, Ti of 0.02 to 1.0 percent by mass, Mn of 0 to 0.2 percent by mass, an inevitable impurity including S, and the balance Fe. The Super Invar alloy does not include an additive other than Ti and Mn, as an additive. The Super Invar alloy includes the Ni of 32.3 to 32.5 percent by mass, the Co of 4.4 to 5.1 percent by mass, the Ti of 0.02 to 1.0 percent by mass, and the S of 0.007 to 0.1 percent by mass. The Super Invar alloy is an alloy having good high temperature ductility, low hot crack sensitivity, and low thermal expansibility of equal to or lower than 1 ppm/° C. It is applicable to use Zr or Hf instead of Ti.

Example embodiments relate to alloys having high corrosion resistance and high wear resistance. In particular, example embodiments relate to an iron-based alloy including 20 wt % to 50 wt % Cr; 0 wt % to 15 wt % Mo; 0 wt % to 15 wt % W; 3 wt % to 6 wt % B; and a balance of iron and impurities. In example embodiments, the pitting resistance equivalent number (PREN) is greater than 30 at 1300 K under substantially equilibrium solidification conditions. In example embodiments, the mole fraction of a hard phase of the alloy is between 45% and 80% at 1300K under substantially equilibrium solidification conditions. The liquidus of the alloy may be less than 2000K under substantially equilibrium solidification conditions.

A lead-based alloy containing alloying additions of bismuth, antimony, arsenic, and tin is used for the production of doped leady oxides, lead-acid battery active materials, lead-acid battery electrodes, and lead-acid batteries.

Provided is a sputtering target to be used for forming a granular magnetic thin film in which FePt magnetic grains are isolated by an oxide and which constitutes a heat-assisted magnetic recording medium having enhanced uniaxial magnetic anisotropy, thermal stability, and SNR (signal-to-noise ratio).

The sputtering target for a heat-assisted magnetic recording medium contains an FePt alloy and a nonmagnetic material as main components, where the nonmagnetic material is an oxide having a melting point of 800° C. or higher and 1100° C. or lower.

Provided is a sputtering target to be used for forming a granular magnetic thin film in which FePt magnetic grains are isolated by an oxide and which constitutes a heat-assisted magnetic recording medium having enhanced uniaxial magnetic anisotropy, thermal stability, and SNR (signal-to-noise ratio).

The sputtering target for a heat-assisted magnetic recording medium contains an FePt alloy and a nonmagnetic material as main components, where the nonmagnetic material is an oxide having a melting point of 800° C. or higher and 1100° C. or lower.