A method comprising sintering a Mn and Bi powder compact at a first temperature for a first predetermined duration, based on the first temperature, and sintering the compact at a second temperature, less than the first temperature, for a second predetermined duration, greater than the first duration, is disclosed. The sintering at a first temperature for a first predetermined duration generates a predetermined MnBi LTP transition driving force to decrease a formation energy barrier for transition to MnBi LTP. Sintering the compact at the second temperature for the second predetermined duration forms a magnet containing the MnBi LTP.

A method comprising sintering a Mn and Bi powder compact at a first temperature for a first predetermined duration, based on the first temperature, and sintering the compact at a second temperature, less than the first temperature, for a second predetermined duration, greater than the first duration, is disclosed. The sintering at a first temperature for a first predetermined duration generates a predetermined MnBi LTP transition driving force to decrease a formation energy barrier for transition to MnBi LTP. Sintering the compact at the second temperature for the second predetermined duration forms a magnet containing the MnBi LTP.

Disclosed are an MnBi sintered magnet exhibiting excellent thermal stability as well as excellent magnetic characteristics at high temperature, an MnBi anisotropic complex sintered magnet, and a method of preparing the same.

Disclosed are an MnBi sintered magnet exhibiting excellent thermal stability as well as excellent magnetic characteristics at high temperature, an MnBi anisotropic complex sintered magnet, and a method of preparing the same.

Provided is a refined Goss-grain aluminum alloy plate and a preparation method thereof. The refined Goss-grain aluminum alloy plate includes the following compositions: 3.7-4.8 wt % of Cu, 1.2-1.7 wt % of Mg, 0.3-0.8 wt % of Mn, 0.03-0.10 wt % of Ti, and the balance of Al. The refined Goss-grain aluminum alloy plate is prepared by a method including subjecting an AlCuMg alloy ingot with a certain composition to a homogenizing at a temperature of 470-505 C., a hot rolling at high temperature of 465-495 C. with a large deformation of 80%-98% and a high final temperature, then directly to a cold rolling with a small or medium deformation of 5% to 50%, and then to a recrystallization and annealing treatment at a temperature of 300-450 C., a solid solution treatment at a temperature of 460-505 C., and a natural aging treatment for at least 96 hours.

Provided is a refined Goss-grain aluminum alloy plate and a preparation method thereof. The refined Goss-grain aluminum alloy plate includes the following compositions: 3.7-4.8 wt % of Cu, 1.2-1.7 wt % of Mg, 0.3-0.8 wt % of Mn, 0.03-0.10 wt % of Ti, and the balance of Al. The refined Goss-grain aluminum alloy plate is prepared by a method including subjecting an AlCuMg alloy ingot with a certain composition to a homogenizing at a temperature of 470-505 C., a hot rolling at high temperature of 465-495 C. with a large deformation of 80%-98% and a high final temperature, then directly to a cold rolling with a small or medium deformation of 5% to 50%, and then to a recrystallization and annealing treatment at a temperature of 300-450 C., a solid solution treatment at a temperature of 460-505 C., and a natural aging treatment for at least 96 hours.

A coated metallic substrate is provided, including, at least; one layer of oxides, such layer being directly topped by an intermediate coating layer comprising Fe, Ni, Cr and Ti wherein the amount of Ti is above or equal to 5 wt. % and wherein the following equation is satisfied: 8 wt. %<Cr+Ti<40 wt. %, the balance being Fe and Ni, such intermediate coating layer being directly topped by a coating layer being an anticorrosion metallic coating.

A tribological system may include a valve seat ring composed of a sintered material and a valve having a surface at least in a seat region that may be at least one of (i) untreated, (ii) hardened, and (iii) plated. The sintered material may be a pressed and sintered powder mixture having a composition that may include (i) 5 to 45 wt % of at least one Fe-based hard phase, (ii) 0 to 2 wt % of each of graphite particles, MnS powder, MoS.sub.2 powder, and FeP powder, (iii) 0 to 7 wt % copper powder and 0 to 4 wt % Co powder, (iv) 0.1 to 1.0 wt % of a pressing aid, (v) a high-speed steel having a composition including 14-18 wt % Cr, 1.2-1.9 wt % C, 0.1-0.9 wt % Si, 0.5-2.5 wt % of each of V, W, and Mo, and (vi) a balance of Fe and production-related impurities in quantities of <1.5 wt %.

A tribological system may include a valve seat ring composed of a sintered material and a valve having a surface at least in a seat region that may be at least one of (i) untreated, (ii) hardened, and (iii) plated. The sintered material may be a pressed and sintered powder mixture having a composition that may include (i) 5 to 45 wt % of at least one Fe-based hard phase, (ii) 0 to 2 wt % of each of graphite particles, MnS powder, MoS.sub.2 powder, and FeP powder, (iii) 0 to 7 wt % copper powder and 0 to 4 wt % Co powder, (iv) 0.1 to 1.0 wt % of a pressing aid, (v) a high-speed steel having a composition including 14-18 wt % Cr, 1.2-1.9 wt % C, 0.1-0.9 wt % Si, 0.5-2.5 wt % of each of V, W, and Mo, and (vi) a balance of Fe and production-related impurities in quantities of <1.5 wt %.

Identifying a stable phase of a binary alloy comprising a solute element and a solvent element. In one example, at least two thermodynamic parameters associated with grain growth and phase separation of the binary alloy are determined, and the stable phase of the binary alloy is identified based on the first thermodynamic parameter and the second thermodynamic parameter, wherein the stable phase is one of a stable nanocrystalline phase, a metastable nanocrystalline phase, and a non-nanocrystalline phase. In different aspects, an enthalpy of mixing of the binary alloy may be calculated as a first thermodynamic parameter, and an enthalpy of segregation of the binary alloy may be calculated as a second thermodynamic parameter. In another example, a diagram delineating a plurality of regions respectively representing different stable phases of at least one binary alloy is employed, wherein respective regions of the plurality of regions are delineated by at least one boundary determined as a function of at least two thermodynamic parameters associated with grain growth and phase separation of the at least one binary alloy.