It has been unexpected found that the machinability and corrosion resistance of powder metal parts can be greatly improved by incorporating calcium aluminoferrite powder, such as naturally occurring brownmillerite powder (Ca.sub.2(Al,Fe).sub.2O.sub.5), into the part. Improved machinability is of enormous value in manufacturing countless parts where it is necessary or desirable to machine the part after it has been sintered, such as is frequently the case with gears, rotors and sprockets. In the practice of this invention, calcium aluminoferrite powder can also be incorporated into parts which will not necessarily be machined for the sole purpose of attaining better corrosion resistance. Surprisingly, the incorporation of the calcium aluminoferrite powder into such parts does not significantly compromise the strength, durability, or wear characteristics of the part and generally improves the service life of the part by providing better corrosion resistance.

A gear includes a sintered body, in which Fe is contained as a principal component, Ni is contained in a proportion of 2 mass % or more and 20 mass % or less, Si is contained in a proportion of 0.3 mass % or more and 5.0 mass % or less, C is contained in a proportion of 0.005 mass % or more and 0.3 mass % or less, and one element selected from the group consisting of Ti, V, Y, Zr, Nb, Hf, and Ta is defined as a first element, that is contained in a proportion of 0.01 mass % or more and 0.7 mass % or less.

A method and apparatus for surface densification of powder metal annular preforms is described. A forming tool has external helical teeth corresponding to internal helical teeth of the preform. A die correspondingly configured to the external splines of the preform circumferentially surrounds the forming tool. The forming tool, die and lower punch(es) collectively define an aperture dimensioned to receive the preform. Upper punch(es) encase the preform in the aperture. Surface densification of the internal surface of the preform is achieved by movement of the preform axially over the forming tool. External splines of the preform and corresponding die splines direct the preform axially while internal helical teeth and corresponding forming teeth direct the forming tool to rotate as the preform moves. The forming teeth have varying dimensions in the circumferential and radial directions to apply compression and relaxation to densify the surface of the preform helical teeth.

A method and apparatus for surface densification of powder metal annular preforms is described. A forming tool has external helical teeth corresponding to internal helical teeth of the preform. A die correspondingly configured to the external splines of the preform circumferentially surrounds the forming tool. The forming tool, die and lower punch(es) collectively define an aperture dimensioned to receive the preform. Upper punch(es) encase the preform in the aperture. Surface densification of the internal surface of the preform is achieved by movement of the preform axially over the forming tool. External splines of the preform and corresponding die splines direct the preform axially while internal helical teeth and corresponding forming teeth direct the forming tool to rotate as the preform moves. The forming teeth have varying dimensions in the circumferential and radial directions to apply compression and relaxation to densify the surface of the preform helical teeth.

A method and device for manufacturing a bevelled stone, particularly for a timepiece are disclosed. A precursor is produced from a mixture of at least one material in powder form with a binder. The method includes pressing the precursor so as to form a green body, using a top die and a bottom die comprising a protruding rib, sintering the green body so as to form a body of the future stone in at least one material, the body including a peripheral face and a bottom face provided with a groove, and machining the body including a substep of planning the peripheral face up to the groove, such that an inner wall of the groove forms at least a flared part of the peripheral face of the stone.

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 sintered body manufacturing apparatus includes a compacting apparatus configured to press a raw powder containing a metal powder into a green compact, a machining apparatus configured to perform a cutting operation on the green compact to produce an unsintered materials, and a green compact conveying path configured to connect the compacting apparatus in series to the machining apparatus to convey green compacts one by one from the compacting apparatus to the machining apparatus.

A method for making small diameter NiTi metal alloy components, including balls, comprising providing a metal powder comprising nickel, titanium, and a transition metal, consolidating the metal powder into cylindrical rods, and cutting the cylindrical rods into segments. The segments are then machined into spheres slightly larger than the finished ball size diameter. The spheres are heat treated to solutionize and dissolve all phases and subsequently cooled without the need for rapid quenching due to the influence of the transition metal to suppresses the formation of soft phases in the spheres, wherein such soft phases prevent hardening, to achieve a Rockwell hardness of HRC 58-62. Finally, the hardened spheres are polished until the desired finished ball size diameter and surface finish is achieved.

A method for making small diameter NiTi metal alloy components, including balls, comprising providing a metal powder comprising nickel, titanium, and a transition metal, consolidating the metal powder into cylindrical rods, and cutting the cylindrical rods into segments. The segments are then machined into spheres slightly larger than the finished ball size diameter. The spheres are heat treated to solutionize and dissolve all phases and subsequently cooled without the need for rapid quenching due to the influence of the transition metal to suppresses the formation of soft phases in the spheres, wherein such soft phases prevent hardening, to achieve a Rockwell hardness of HRC 58-62. Finally, the hardened spheres are polished until the desired finished ball size diameter and surface finish is achieved.