WO2013104264A1 - 氢化钐纳米粉改性制备高磁能积钐－钴基永磁体的方法 - Google Patents

氢化钐纳米粉改性制备高磁能积钐－钴基永磁体的方法 Download PDF

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WO2013104264A1
WO2013104264A1 PCT/CN2012/088028 CN2012088028W WO2013104264A1 WO 2013104264 A1 WO2013104264 A1 WO 2013104264A1 CN 2012088028 W CN2012088028 W CN 2012088028W WO 2013104264 A1 WO2013104264 A1 WO 2013104264A1
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samarium
smcocufezr
powder
hydride
nanopowder
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French (fr)
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岳明
张久兴
左建华
张东涛
刘卫强
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Beijing University of Technology
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Beijing University of Technology
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/07—Alloys based on nickel or cobalt based on cobalt
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/02—Compacting only
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/10—Sintering only
    • B22F3/1003—Use of special medium during sintering, e.g. sintering aid
    • B22F3/1007—Atmosphere
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/12—Both compacting and sintering
    • B22F3/16—Both compacting and sintering in successive or repeated steps
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/24—After-treatment of workpieces or articles
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/032—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials
    • H01F1/04—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials metals or alloys
    • H01F1/047—Alloys characterised by their composition
    • H01F1/053—Alloys characterised by their composition containing rare earth metals
    • H01F1/055—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5
    • H01F1/0555—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 pressed, sintered or bonded together
    • H01F1/0557—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 pressed, sintered or bonded together sintered

Definitions

  • the invention relates to a preparation method of a samarium-cobalt-based permanent magnet, in particular to a method for preparing a high-magnetic energy-cobalt-based cobalt-based permanent magnet by hydrogenation of yttrium nano-powder, belonging to the technical field of permanent magnet materials.
  • the samarium-cobalt-based permanent magnet material not only has excellent permanent magnet characteristics, but also has good temperature stability, and thus is widely used in room temperature and high temperature environments where magnetic properties are required to be high. Especially this year, with the rapid development of civil and military high-tech industries such as electric vehicles, aerospace and nuclear power industries, the demand for bismuth-cobalt-based permanent magnetic materials has been rapidly developed.
  • the mainstream product of bismuth-cobalt-based permanent magnet materials is 2:17 type SmCoFeCuZr alloy.
  • the temperature stability of SmCoFeCuZr alloy has significant advantages.
  • Conventional NdFeB permanent magnet materials are generally used below 100 ,, up to about 200 after composition adjustment, while SmCoFeCuZr alloys have an operating temperature of up to 350.
  • the magnetic properties of SmCoFeCuZr alloy are quite different from that of NdFeB permanent magnet materials, which is mainly reflected in the remanence and magnetic energy of the magnetic body being only about 2/3 of the latter. Therefore, further improvement of the remanence and magnetic energy of the SmCoFeCuZr alloy has become a hot spot in the development of the permanent magnet materials and industry sectors.
  • a common method for improving the remanence and coercivity of SmCoFeCuZr alloy is to increase the content of Fe > Co in the alloy, but this method will simultaneously cause a significant decrease in the coercive force of the magnet.
  • the use of these methods to improve the magnetic remanence and magnetic energy product has little room for improvement. For this reason, there is an urgent need to develop a new method for improving the remanence and magnetic energy product of SmCoFeCuZr alloy.
  • the object of the present invention is to provide a high magnetic energy enthalpy-cobalt-based permanent magnet by the method of doping modification of hydrazine hydride nanopowder for the above problems.
  • a certain amount of yttrium hydride nanopowder is mixed with samarium cobalt microparticles so that the yttrium hydride nanoparticles are uniformly distributed and dispersed on the surface of the SmCoFeCuZr alloy.
  • the mixed powder is subjected to sintering and solution aging treatment to prepare an SmCoFeCuZr alloy.
  • the SmCoFeCuZr alloy prepared by the method of the present invention has higher remanence and high magnetic energy, and thus has a wider application range.
  • the invention provides a method for preparing a high magnetic energy accumulation ⁇ -cobalt-based permanent magnet, which comprises the following steps:
  • composition of the alloy prepared by smelting is Sm: 25.4 to 26.4 wt.% -, Co: 57.0 to 58.0 wt.%, Fe: 5.5 wt.%, C: 7.8 t%. Zn3, 3 t.% of SmCoCuFeZr alloy ingot;
  • the proportion of the yttrium hydride nanopowder doped is 1 - 3% by weight of the SmCoCuFeZr micron powder, The proportioned mixed powder is placed in a rolling ball mill, and the two powders are thoroughly mixed to obtain a uniformly mixed powder;
  • Step (3) The uniformly mixed powder is placed in a mold and pressed in a magnetic field of a magnetic field of 2T, and then pressed by a pressure of 200 M:Pa to obtain a compact;
  • step (4) The green compact obtained in step (4) is placed in a vacuum sintering furnace, and the sample is pre-fired at 1190 ° C for 30 minutes in vacuum, and then sintered under argon gas protection at 1220 C to i230 ° C for 90 minutes. i i80. C ⁇ i i90. C solution treatment for 210 minutes, then air-cooled to room temperature; finally solid solution aging treatment, first incubated at 840 12 12h, then cooled to 420 ° C at a cooling rate of 0.4 ° C / min, and kept for 10h, then naturally cooled To room temperature, a high-performance sintered magnet doped with yttrium hydride nanopowder is obtained.
  • the hydrazine hydride-modified sintered ⁇ -cobalt-based magnet prepared by the method of the invention has a remanence increase of 1.3% and 5% compared with the undoped magnet of the same composition, and at the same time, the most important index for characterizing the magnetic strength of the magnet.
  • the magnetic energy product has also increased by 3.9% - 21%, which has greatly broadened the use of samarium cobalt permanent magnets. Therefore, the magnets prepared by the method have a wider range of applications.
  • the composition of the smelting alloy is Sm: 25.4 to 26.4 wt.%, Co: 57.0 to 58.0 wt.%, Fe: 5.5 wt.%, Cu: 7.8 wt%, Zr: 3.3 wt.% of the alloy; Sm during smelting The compensation for burning loss is 10wt.%, and the compensation for burning loss of Cu is 5wt.%; the raw material is smelted in a medium frequency induction furnace, and then poured into a water-cooled copper mold to be cooled to obtain a SraCo CuFeZr alloy ingot:
  • Example i The SmCoCuFeZr alloy ingot was prepared by medium frequency induction melting technology with the composition of Sm: 25.4 wt.%; Co: 58.0 wt.%; Fe: 5.5 wt.%; Cu: 7.8 wt%; Zr: 3.3 wt.%, and then It was broken into a powder having an average particle diameter of 3 ⁇ m. Then, a yttrium hydride nanopowder having an average particle diameter of 20 nm, which is a weight percentage of the SmCoCuFeZr micron powder, was doped into the above initial powder, and the two were uniformly mixed.
  • the mixed powder was compression-molded in a magnetic field of 2 Torr, and then pressed under a pressure of 200 MPa to obtain a green compact.
  • the compact was placed in a vacuum sintering furnace, and the sample was first calcined in a vacuum of 1190 Torr for 30 minutes, then argon-protected and sintered at 1220 ° C for 90 minutes, and then solution treated at 1180 ° C for 210 minutes, and then air-cooled to room temperature; After the solution treatment, the solution was first incubated at 840 Torr for 12 h and then at 0.4.
  • the cooling rate of C/mh was cooled to 420 ° C, and kept for 10 h, and then naturally cooled to room temperature to obtain a high-performance sintered magnet doped with yttrium hydride nanopowder.
  • the magnetic properties of the magnet are listed in Table 1.
  • the SmCoCuFeZr alloy ingot was prepared by medium frequency induction melting technology with the composition of Sm: 26.4 wt.%; Co: 57.0 wt.%; Fe: 5.5 t.%; Cu: 7.8 wt%; Zr: 3.3 wt.%, and then It was broken into a powder having an average particle diameter of 4 ⁇ m. Thereafter, a cerium hydride nanopowder having an average particle diameter of 50 nm, which is 2% by weight of the SmCoCuFeZr micron powder, is doped into the above initial powder, and the two are uniformly mixed. The mixed powder was compression-molded in a magnetic field of 2 T, and pressed under a pressure of 200 MPa to obtain a green compact.
  • the SmCoCuFeZr alloy ingot was prepared by medium frequency induction melting technology, and the composition was Sm: 26.0 wt.%; Co: 57.4 wt.%; Fe: 5.5 wt.%; Cu: 7.8 wt%; Zr: 3.3 wt.%, and then It was broken into a powder having an average particle diameter of 5 mm. Thereafter, the SmCoCuFeZr micron powder was doped with 3% by weight of yttrium hydride nanopowder having an average particle diameter of 100 nm into the above initial powder, and the two were uniformly mixed.
  • the mixed powder was compression-molded in a magnetic field of 2 T, and then pressed under a pressure of 200 MPa to obtain a green compact. Then, the compact is placed in a vacuum sintering furnace, and the product is pre-fired at 1190 ° C for 30 minutes, then argon gas is sintered for 12 minutes at 1230 Torr, and then 119 (TC solution treatment for 210 minutes, then air-cooled to After room temperature; then solid solution aging treatment, first 940 ⁇ under the heat for 2h, then cooled to 420 ⁇ at a cooling rate of 0,4 ° C / miii, and kept oh, then naturally cooled to room temperature, get yttrium hydride nano-powder Miscellaneous high-performance sintered magnets, the magnetic properties of the magnets are listed in Table 1 Comparative Example]
  • the SmCoCuFeZr alloy ingot was prepared by medium frequency induction melting technology with the composition of Sm: 26.0 wt.%; Co: 57.4 wt.%; Fe: 5.5 wt.%; Cu: 7.8 wt%: Zr: 3.3 wt.%, and then It was broken into a powder having an average particle diameter of 5 ⁇ m.
  • the powder was compression-molded in a magnetic field of 2 T, and pressed under a pressure of 200 MPa to obtain a compact.
  • the compact is placed in a vacuum sintering furnace, and the sample is pre-fired at 190"C for 30 minutes, then argon-protected at 1230'C for 90 minutes, and then treated with 1190' ⁇ for 210 minutes, then the wind.
  • solid solution aging treatment first at 840 ° C for 12 h, then cooled to 420 ° C at a cooling rate of 0.4 ° C / min, and kept for 10 h, then naturally cooled to room temperature, to obtain lanthanum hydride nano Powder-doped high-performance sintered magnets, the magnetic properties of the magnets are listed in Table i
  • the yttrium hydride-modified sintered samarium-cobalt-based magnet prepared by the method of the present invention has a remanence increase of 1, 3% - 13, 5% compared with the undoped magnet of the same composition, and at the same time, the magnetic properties of the magnet are strong.
  • the weakest and most important indicator magnetic energy product has also increased by 3,9% and 21%, which has greatly broadened the use of samarium cobalt permanent magnets. Therefore, the magnets prepared by the method have a wider range of applications.

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Abstract

氢化钐纳米粉改性制备高磁能积钐-钴基永磁体的方法，属于永磁材料技术领域。制备组成为Sm：25.4〜26.4wt.%、Co：57.0〜58.0wt.%、Fe：5.5wt.%、Cu：7.8wt%、Zr：3.3wt.%的SmCoCuFeZr合金微米颗粒，将1-3%的氢化钐纳米粉与钐钴微米颗粒均匀混合，在2T的磁场中压制成型，后压制成压坯；置入真空烧结炉内烧结，再经固溶处理，风冷至室温；进行固溶时效处理，随后自然冷却至室温即可。采用该方法制备的SmCoFeCuZr合金具有更高的剩磁和高磁能积，具有更广的应用范围。

Description

氢化钐纳米粉改.性制备高磁能积钐―钴基永磁体的方法
技术领域
本发明涉及一种钐 钴基永磁体的制备方法、尤其涉及氢化钐纳米粉改性制 备高磁能积钐 钴基永.磁体的方法， 属于永磁材料技术领域。
背景技术
钐-钴基永磁材料不仅具有优异的永磁特性， 而且温度稳定性好， 因此广泛 的应用于对磁性能要求较高的室温和高温环境下。特别是今年来，随着电动汽车、 航空航天、核能工业等民用和军用高技术产业的快速发展.，使得对于钐-钴基永 磁材料的需要得到快速发展。
目前， 钐-钴基永磁材料的主流产品是 2: 17型 SmCoFeCuZr合金。 与目前 常用的钕铁硼永磁材料相比， SmCoFeCuZr合金的温度稳定性具有显著的优势。 常规的钕铁硼永磁材料一般应用于 100Ό以下，经过成分调整后可达 200 左右， 而 SmCoFeCuZr合金的工作温度最高可达 350。C 另一方面， SmCoFeCuZr合金 的磁性能则与钕铁硼永磁材料存在着较大的差距，突出体现在磁'体的剩磁和磁能 积仅为后者的 2/3左右。 因此， 进一步提高 SmCoFeCuZr合金的剩磁和磁能积成 为当前永磁材料研发和产业部门关注的热点。
一种提高 SmCoFeCuZr合金剩磁和矫顽力的常用方法是提高合金中 Fe > Co 的含量， 但是这种方法会同时造成磁体矫顽力的显著下降。 而且经过长期研究， 采用这.种方法改善.磁体剩磁和磁能积的提升空间已经不大。 为此、 急需开发出提 高 SmCoFeCuZr合金剩磁和磁能积的新方法。
发明内容
本发明的目的是针对上述问题、提出采用氢化钐纳米粉掺杂改性的方法制备 高磁能积钐-钴基永磁体。将一定量的氢化钐纳米粉与钐钴微米颗粒混合， 使得 氢化钐纳米颗粒均匀分布分散于 SmCoFeCuZr合金 ·颗粒表面。 混合后的粉末经 过烧结和固溶时效处理， 制备成 SmCoFeCuZr合金。 与未添加氢化钐纳米粉的 合金相比， 采用本发明方法制备的 SmCoFeCuZr合金具有更高的剩磁和高磁能 积， 因此具有更广的应用范围。
本发明提.供的一种制备高磁能积钐-钴基永磁体的方法，其特征在于， 包括 以下步骤：
(1) 熔炼制备合金成分为 Sm:25.4〜26.4wt.% -, Co:57.0〜58.0wt.%、 Fe:5.5wt.%、 C :7.8 t%. Zn3,3 t.%的 SmCoCuFeZr合金铸锭;
(2) 将步驟（ 1 )制备的 SmCoCuFeZr合金铸锭粉 ·碎、 球磨并千燥得到平均粒径
3 5微米的 SmCoCuFeZr微米粉末；
(3) 将平均粒径 20― 100 纳米的氢化钐纳米粉加入步骤 ( 2 ) 中制备好的 SmCoCuFeZr微米粉末中 , 氢化钐纳米粉掺杂的比例为 SmCoCuFeZr微米粉 末重量的 1 - 3%, 按比例混合后的粉末放入滚动球磨机中， 将两种粉末充分 混合并得到混合均匀的粉末；
(4) 将步驟 ( 3 ) 混合均匀后的粉末放入模具中在磁场为 2T的磁场中压制成型, 再经 200M:Pa的压力等静压压制， 获得压坯；
(5) 将步驟 ( 4 )得到的压坯置入真空烧结炉内、 先将样品在 1190°C真空预烧 30 分钟, 然后在 1220 C〜i230°C氩气保护下烧结 90分钟, 再经 i i80。C〜i i90。C 固溶处理 210分钟， 然后风冷至室温； 最后进行固溶时效处理， 先在 840Ό 下保温 12h， 然后以 0.4°C/min的冷却速度冷至 420°C , 并保温 10h, 随后自 然冷却至室温， 得到氢化钐纳米粉掺杂的高性能烧结磁体 .,
上述步骤 ( 1 )和（2 ) 的方法为本.领域常规技术方法。
采用本发明方法制备的氢化钐改性烧结钐―钴基磁体与相同成分的未掺杂 磁体相比， 其剩磁提高 1.3% 13,5%， 同时， 表征磁体磁性强弱的最重要的指标 磁能积也大幅提高 3.9%― 21%, 从而在很大程度上拓宽了钐钴永磁的使用范围。 因此， 采用本方法制备的磁体具有更加广泛的应用范围。
具体实施方式
( 1 )熔炼合金成分为 Sm:25.4~26.4wt.%, Co:57.0~58.0wt.%, Fe:5.5wt.%, Cu:7.8wt%, Zr:3.3wt.%的合金; 熔炼时 Sm的烧损补偿量为 10wt.%， Cu的烧损 补偿量为 5wt.%; 将原料在中频感应炉中熔炼， 然后浇入水冷铜模中冷却得到 S raCo CuFeZr合金铸锭：
( 2 )将步上迷制备的铸锭块经鄭式破碎机-圓盘粉碎机破碎后过 40 目的筛 子得到小于 380微米的微米粉末， 然后将粉末放入航空汽油为介质的滚动罐中 进行滚动球磨 5 小时， 球料比为 5:1 , 取出后在空气中干燥得到平均 径 3 5 微米的 SmCoCuFeZr微米粉末。
实施例 i 利用 中频感应熔炼技术制备 SmCoCuFeZr 合金铸锭， 成分为 Sm:25.4wt.%; Co:58.0wt.%; Fe:5.5wt.%; Cu:7.8wt%; Zr:3.3wt.%, 然后将其破 碎为平均粒径 3微米的粉末。之后将占 SmCoCuFeZr微米粉末重量百分比 Γ½的、 平均粒径 20纳米的氢化钐纳米粉掺杂到上述初始粉末中 , 并将二者混合均匀。 将混匀后的粉末在 2Τ的磁场中压制成型 , 再经 200MPa的压力等静压压制， 获 得压坯。 将压坯置入真空烧结炉内， 先将样品在 1190Ό真空预烧 30分钟， 然后 在 1220°C氩气保护烧结 90分钟，再经 1180°C固溶处理 210分钟， 然后风冷至室 温； 之后进行固溶时效处理, 先在 840Ό下保温 12h, 然后以 0.4。C/mh】的冷却速 度冷至 420°C , 并保温 10h, 随后自然冷却至室温， 得到氢化钐纳米粉掺杂的高 性能烧结磁体， 磁体的各项磁性能参量列于表 1。
实施例 2
利用中频感应熔炼技术制备 SmCoCuFeZr 合金铸锭， 成分为 Sm: 26.4wt.%; Co: 57.0wt.%; Fe:5.5 t.%; Cu:7.8wt%; Zr:3.3wt.%, 然后将其破碎为 平均粒径 4微米的粉末。 之后将占 SmCoCuFeZr微米粉末重量百分比 2%的、 平 均粒径 50纳米的氢化钐纳米粉掺杂到上述初始粉末中, 并将二者混合均匀。 将 混匀后的粉末在 2T的磁场中压制成型 , 再经 200MPa的压力等静压压制， 获得 压坯。 然后将压坯置入真空烧结炉内、 先将样品在 1190°C真空预烧 30分钟， 然 后在 1225 C氩气保护烧结 90分钟，再经 1185 C固溶处理 210分钟、 然后风冷至 室温； 之后进行固溶时效处理， 先在 840°C下保温 12h， 然后以 0,4°C/miti的冷却 速度冷至 420Ό , 并保温 lObu 随后自然冷却至室温， 得到氢化钐纳米粉掺杂的 高性能烧结磁体， 磁体的各项磁性能参量列于表 1。 实施例 3
利用中频感应熔炼技术制备 SmCoCuFeZr 合金铸锭, 成分为 Sm: 26.0wt.%; Co:57.4wt.%; Fe:5.5wt.%; Cu:7.8wt%; Zr:3.3wt.%, 然后将其破碎为 平均粒径 5徵米的粉末。 之后占 SmCoCuFeZr微米粉末将重量百分比 3%的、 平 均粒径 100纳米的氢化钐纳米粉掺杂到上述初始粉末中, 并将二者混合均匀。将 混匀后的粉末在 2T的磁场中压制成型, 再经 200MPa的压力等静压压制， 获得 压坯。 然后将压坯置入真空烧结炉内， 先将祥品在 1190°C真空预烧 30分钟 然 后在 1230Ό氩气保护烧结 90分钟， 再经 119(TC固溶处理 210分钟, 然后风冷至 室温; 之后进行固溶时效处理， 先在 840Ό下保温】2h, 然后以 0,4°C/miii的冷却 速度冷至 420Ό , 并保温】 Oh, 随后自然冷却至室温、 得到氢化钐纳米粉掺杂的 高性能烧结磁体， 磁体的各项磁性能参量列于表 1 对比例】
利用中频感应熔炼技术制备 SmCoCuFeZr 合金铸锭, 成分为 Sm: 26.0wt.%; Co:57.4wt.%; Fe:5.5wt.%; Cu:7.8wt%: Zr:3.3wt.%, 然后将其破碎为 平均粒径 5微米的粉末。 将粉末在 2T的磁场中压制成型， 再经 200MPa的压力 等静压压制, 获得压坯。 然后将压坯置入真空烧结炉内， 先将样品在 】190"C真 空预烧 30分钟,然后在 1230'C氩气保护烧结 90分钟,再经 1190'Ό固溶处理 210 分钟， 然后风冷至室温； 之后进行固溶时效处理， 先在 840°C下保温 12h, 然后 以 0.4°C/min的冷却速度冷至 420°C , 并保温 10h， 随后自然冷却至室温， 得到氢 化钐纳米粉掺杂的高性能烧结磁体， 磁体的各项磁性能参量列于表 i
Figure imgf000005_0001
以上结果说明，采用本发明方法制备的氢化钐改性烧结钐 钴基磁体与相同 成分的未掺杂磁体相比， 其剩磁提高 1 ,3% - 13,5%, 同时， 表征磁体磁性强弱的 最重要的指标磁能积也大幅提高 3,9% 21%, 从而在很大程度上拓宽了钐钴永 磁的使用范围。 因此, 采用本方法制备的磁体具有更加广泛的应用范围。

Claims

权 利 要 求 书
1、 一种氢化钐纳米粉改性制备高磁能积钐 钴基永磁体的方法， 其特征在于， 包括以下步 驟：
(1) 熔炼制备合金成分为 Sm:25.4~26.4wt.%、 Co:57J)〜58.()wt.%、 Fe:5,5wt,%、 Cu:7.8wt%。
∑『:3.3^1.%的 SmCoCuFeZr合金铸锭；
(2) 将步驟 （ 1 )制备的 SmCoCuFeZr合金铸锭粉碎、 球磨并干燥得到平均粒径 3 5微米的 SmCoCuFeZr微米粉末；
(3) 将平均粒径 20 - 100纳米的氢化钐纳米粉加入步骤 ( 2 )中制备好的 SmCoCuFeZr微米粉 末中, 氢化钐纳米粉摻杂的比例为 SmCoCuFeZr微米粉末重量的 1 - 3%, 按比例混合后 的粉末放入滚动球磨机中， 将两种粉末充分混合并得到混合均匀的粉末；
(4) 将步骤 ( 3 )混合均匀后的粉末放入模具中在磁场为 2T的磁场中压制成型, 再经 200MPa 的压力等静压压制, 获得压坯;
(5) 将步骤（4 )得到的压坯置入真空烧结炉内， 先将祥品在 i:l 90。C真空预烧 30分钟， 然后 在 1220T：〜 1230Ό氩气保护下烧结 90分钟， 再经 1180O〜li90°C固溶处理 210分钟， 然 后风冷至室温； 最后进行固溶时效处理， 先在 840。C下保温 12h, 然后以 0.4°C/min的冷 却速度冷至 420°C , 并保温 10h， 随后自然冷却至室温， 得到氢化钐纳米粉掺杂的高性能 烧结磁体。
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