Abstract:
Disclosed is a rare earth magnet in the R-T-B rare earth element-transition metal-boron system that is made from an improved composition and properties of main phase alloy in the R-T-B system containing Pr and a boundary alloy. Disclosed also is a manufacturing method of the rare earth magnet alloy flake by a strip casting method with improved rotating rollers such that the alloy flake has a specified fine surface roughness and has a small and regulated amount of fine R-rich phase regions. Consequently, the alloy flake for the rare earth magnet does non contain alpha-Fe and has a homogeneous morphology so that the rare earth magnet formed by sintering or bonding the alloy flakes exhibits excellent magnetic properties.
Abstract:
Disclosed is a rare earth magnet in the R-T-B (rare earth element-transition metal-boron) system that is made from an improved composition and properties of main phase alloy in the R-T-B system containing Pr and a boundary alloy. Disclosed also is a manufacturing method of the rare earth magnet alloy flake by a strip casting method with improved rotating rollers such that the alloy flake has a specified fine surface roughness and has a small and regulated amount of fine R-rich phase regions. Consequently, the alloy flake for the rare earth magnet does not containing alpha-Fe and has a homogeneous morphology so that the rare earth magnet formed by sintering or bonding the alloy flakes exhibits excellent magnetic properties.
Abstract:
The magnetic properties of rare earth magnet are improved by means of forming a novel structure of the cast alloy used for the production of a rare earth magnet, which contains from 27 to 34% by weight of at least one rare earth element (R) including yttrium, from 0.7 to 1.4% by weight of boron, and the balance being essentially iron and, occasionally any other transition element, and comprises an R2T14B phase, an R-rich phase and optionally at least one ternary phase except for the R2T14B phase and the R-rich phase. The novel structure is that the average grain size of the R2T14B phases along the short axes of the columnar grains is from 10 to 100 mu m, the R-rich phase is lamellar and partially granular is crystallized on a boundary and inside the R2T14B phase, and, further, the average spacing between the adjacent R-rich phases is from 3 to 15 mu m. The average grain size of the R2T14B phase is from 4.4 to 7.0 times of the average spacing between the adjacent R-rich phase lamellars. The novel structure can be formed by means of feeding alloy melt onto a rotary casting roll, cooling in a temperature range of from melting point to 1000 DEG C at a cooling rate of 300 DEG C per second or more, and further cooling in a temperature range of from 800 to 600 DEG C at a cooling rate of 1 DEG C/second or less.
Abstract:
In casting a rare earth alloy into a sheet (6) using a tundish (3, 13), as a refractory for a tundish which can be used for dispensing with a preheating step for the purpose of improving the flow of a melt (2), use is made of a refractory which consists substantially of 70 wt.% or more of Al2O3 and 30 % or less of SiO2 or consists substantially of 70 wt.% or more of ZrO2 and 30 % or less of one or more of Y2O3, Ce2O3, CaO, MgO, Al2O3, TiO2 and SiO2, and h as a bulk density of 1 g/cm3, a thermal conductivity in a temperature range of 1200 to 1400 ~C of 0.5 kcal/(mh ~C) or less, and a heat loss under a heating condition of one hour at 1400 ~C of 0.5 wt.% or less.
Abstract:
Rare-earth alloy is cast into a sheet (6) or the like by using a tundish (3, 13). The refractory material of the tundish used for casting does not necessitate preheating for improving the flowability of the melt (2). The refractory material used essentially consists of 70 wt% or more of Al 2 O 3 and 30 wt% or less of SiO 2 , or 70 wt% or more of ZrO 2 and 30 wt% or less of one or more of Y 2 O 3 , Ce 2 O 3 , CaO, MgO, Al 2 O 3 , TiO 2 and SiO 2 . The refractory material has 1g/cm 3 or less of bulk density, has 0.5 kcal/(mh°C) or less of thermal conductivity in the temperature range of from 1200 to 1400°C, and has 0.5 wt% or less of ratio of ignition weight-loss under the heating condition of 1400°C for 1 hour.
Abstract:
Rare-earth alloy is cast into a sheet (6) or the like by using a tundish (3, 13). The refractory material of the tundish used for casting does not necessitate preheating for improving the flowability of the melt (2). The refractory material used essentially consists of 70 wt% or more of Al 2 O 3 and 30 wt% or less of SiO 2 , or 70 wt% or more of ZrO 2 and 30 wt% or less of one or more of Y 2 O 3 , Ce 2 O 3 , CaO, MgO, Al 2 O 3 , TiO 2 and SiO 2 . The refractory material has 1g/cm 3 or less of bulk density, has 0.5 kcal/(mh°C) or less of thermal conductivity in the temperature range of from 1200 to 1400°C, and has 0.5 wt% or less of ratio of ignition weight-loss under the heating condition of 1400°C for 1 hour.
Abstract:
The magnetic properties of rare earth magnet are improved by means of forming a novel structure of the cast alloy used for the production of a rare earth magnet, which contains from 27 to 34% by weight of at least one rare earth element (R) including yttrium, from 0.7 to 1.4% by weight of boron, and the balance being essentially iron and, occasionally any other transition element, and comprises an R2T14B phase, an R-rich phase and optionally at least one ternary phase except for the R2T14B phase and the R-rich phase. The novel structure is that the average grain size of the R2T14B phases along the short axes of the columnar grains is from 10 to 100 mu m, the R-rich phase is lamellar and partially granular is crystallized on a boundary and inside the R2T14B phase, and, further, the average spacing between the adjacent R-rich phases is from 3 to 15 mu m. The average grain size of the R2T14B phase is from 4.4 to 7.0 times of the average spacing between the adjacent R-rich phase lamellars. The novel structure can be formed by means of feeding alloy melt onto a rotary casting roll, cooling in a temperature range of from melting point to 1000 DEG C at a cooling rate of 300 DEG C per second or more, and further cooling in a temperature range of from 800 to 600 DEG C at a cooling rate of 1 DEG C/second or less.
Abstract:
Segregation in a hydrogen-absorbing alloy is decreased by centrifugal casting which is devised so that the melt fed to the bottom portion of a cylindrical rotary mold (4a) solidifies during one rotation of the mold. The average depositing speed of melt is from approximately 0.005 to 0.1 cm/second.