JPH04209504A - Rare-earth permanent magnet - Google Patents
Rare-earth permanent magnetInfo
- Publication number
- JPH04209504A JPH04209504A JP2404028A JP40402890A JPH04209504A JP H04209504 A JPH04209504 A JP H04209504A JP 2404028 A JP2404028 A JP 2404028A JP 40402890 A JP40402890 A JP 40402890A JP H04209504 A JPH04209504 A JP H04209504A
- Authority
- JP
- Japan
- Prior art keywords
- rare earth
- permanent magnet
- earth elements
- kinds
- elements
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 229910052761 rare earth metal Inorganic materials 0.000 title claims abstract description 33
- 150000002910 rare earth metals Chemical class 0.000 title claims description 6
- 229910052692 Dysprosium Inorganic materials 0.000 claims abstract description 4
- 229910052691 Erbium Inorganic materials 0.000 claims abstract description 4
- 229910052688 Gadolinium Inorganic materials 0.000 claims abstract description 4
- 229910052689 Holmium Inorganic materials 0.000 claims abstract description 4
- 229910052772 Samarium Inorganic materials 0.000 claims abstract description 4
- 229910052771 Terbium Inorganic materials 0.000 claims abstract description 4
- 229910052775 Thulium Inorganic materials 0.000 claims abstract description 4
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 4
- 229910052735 hafnium Inorganic materials 0.000 claims abstract description 4
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 4
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 4
- 229910052715 tantalum Inorganic materials 0.000 claims abstract description 4
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 4
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 4
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 4
- 229910052684 Cerium Inorganic materials 0.000 claims abstract description 3
- 229910052765 Lutetium Inorganic materials 0.000 claims abstract description 3
- 229910052779 Neodymium Inorganic materials 0.000 claims abstract description 3
- 229910052777 Praseodymium Inorganic materials 0.000 claims abstract description 3
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 3
- 229910052693 Europium Inorganic materials 0.000 claims description 3
- 239000013078 crystal Substances 0.000 claims description 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 abstract description 10
- 150000001875 compounds Chemical class 0.000 abstract description 7
- 229910045601 alloy Inorganic materials 0.000 abstract description 6
- 239000000956 alloy Substances 0.000 abstract description 6
- 239000000203 mixture Substances 0.000 abstract description 5
- 230000005415 magnetization Effects 0.000 abstract description 4
- 229910052742 iron Inorganic materials 0.000 abstract description 3
- 229910052799 carbon Inorganic materials 0.000 abstract description 2
- 239000002184 metal Substances 0.000 abstract description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 abstract 1
- 150000002739 metals Chemical class 0.000 abstract 1
- 230000007423 decrease Effects 0.000 description 7
- 230000004907 flux Effects 0.000 description 5
- 238000010438 heat treatment Methods 0.000 description 5
- 238000000034 method Methods 0.000 description 5
- 238000004519 manufacturing process Methods 0.000 description 4
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- 229910017112 Fe—C Inorganic materials 0.000 description 2
- 229910000765 intermetallic Inorganic materials 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 238000004663 powder metallurgy Methods 0.000 description 2
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 229910001873 dinitrogen Inorganic materials 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 238000009499 grossing Methods 0.000 description 1
- 230000007774 longterm Effects 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000005551 mechanical alloying Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
Classifications
-
- 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
- H01F1/058—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IVa elements, e.g. Gd2Fe14C
Landscapes
- Chemical & Material Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Inorganic Chemistry (AREA)
- Engineering & Computer Science (AREA)
- Power Engineering (AREA)
- Hard Magnetic Materials (AREA)
Abstract
Description
［０００１１ [00011
【産業上の利用分野］本発明は、希土類−鉄系永久磁石
に関するものであり、とくに従来の技術では困難であっ
た高エネルギー積を焼結体において実現するものである
。
［ｏ ｏ Ｏ２］
【従来の技術］ Ｒ２Ｆｅ＋４Ｃ（ただしＲは希土類元
素を示す。）のキュリー温度はＲ２Ｆｅ＋４Ｃよりもや
や低いが異方性磁界は大きく、新しい永久磁石材料の候
補として注目されている。 （Ｒ，Ｇｒｏｓｓ ｉｎｇ
ｅ ｒ他：Ｊ、 Ｍａｇｎ、Ｍａｇｎ、Ｍａ ｔ、８３
．１９９０．１３０〜１３２頁）。例えば５ｔａｄｅ
１ｍａ ｉｅ ｒ他はバルクのＤｙ−Ｆｅ−Ｃ合金にお
いて、鋳造後、熱処理をすることによって１Ｈｃ＝１２
．５ｋＯｅの保磁力を得たことを報告している。 （Ｈ
，Ｈ，Ｓ ｔ ａｄｅ １ｍａ ｉ Ｃｒ他： Ｍａｔ
、Ｌｅｔｔｅｒｓ ４．１９８６．３７７〜３８０頁
）。しかし、Ｒが重希土類元素の場合にはＦｅのモーメ
ントとＲのモーメントが反平行に結合するため、軽希土
類元素の場合にくらべて飽和磁化が小さくなってしまう
。したがって、Ｒは軽希土類元素を主成分とすることが
望ましい。ところがＲが軽希土類元素の場合には、Ｒ：
Ｆｅ＋４Ｃ化合物が生成しにくいという問題があり、異
方性磁界の大きな金属間化合物Ｒ２Ｆ ｅ＋４Ｃを主体
とする永久磁石を実現することができない。Ｂｕｓｃｈ
ｏｗ他は、Ｒ２Ｆｅ＋４Ｃを生成させるための熱処理条
件を報告している（Ｋ、Ｈ，Ｂｕｓｃｈｏｗ他：Ｊ、Ｌ
ｅ ｓ ｓ−Ｃｏｍｍｏｎ〜ｆｅｔ、１４２．１９８８
．３４９〜３５７頁）。
［０００３］
【発明が解決しようとする課題】しかし、約８３０℃以
下の温度ではＲ２ＦｅｚＣが生成する反応速度はたいへ
ん遅く、また、希土類元素の種類によって決まるある温
度（例えばＲがＮｄの場合は８９０℃）以上では、Ｒ２
Ｆｅ＋４Ｃが分解してしまう。このようにＲ２Ｆｅ＋４
Ｃが生成する温度範囲はたいへんせまく、その上、生成
反応速度が非常に遅いため長時間の熱処理（例えばＲが
Ｎｄの場合は５００時間）が必要であり、実用上問題が
大きいだけでなく、この長時間の熱処理によって粒成長
が起こり、保磁力を低下させる原因となる問題点がある
。また、製法も超急冷法やメカニカルアロイイング法と
いった量産性に問題のある方法に依らなければ、前記の
ような不安定な金属間化合物を得ることが困難であり、
粉末冶金法を用いることは不可能であった。
［０００４］[Industrial Field of Application] The present invention relates to rare earth-iron permanent magnets, and in particular to realizing a high energy product in a sintered body, which has been difficult with conventional techniques. [o o O2] [Prior Art] The Curie temperature of R2Fe+4C (where R represents a rare earth element) is slightly lower than that of R2Fe+4C, but the anisotropic magnetic field is large, and it is attracting attention as a candidate for a new permanent magnet material. (R, Grossing
e r et al.: J, Magn, Magn, Mat, 83
．． 1990. pp. 130-132). For example, 5tade
1maier et al. is a bulk Dy-Fe-C alloy that is heat treated after casting to achieve 1Hc=12
．． It is reported that a coercive force of 5 kOe was obtained. (H
, H, St ade 1 ma i Cr et al.: Mat
, Letters 4.1986. pp. 377-380). However, when R is a heavy rare earth element, the moment of Fe and the moment of R are coupled antiparallelly, so that the saturation magnetization becomes smaller than when R is a light rare earth element. Therefore, it is desirable that R contains a light rare earth element as a main component. However, when R is a light rare earth element, R:
There is a problem that the Fe+4C compound is difficult to generate, and it is not possible to realize a permanent magnet mainly composed of the intermetallic compound R2Fe+4C with a large anisotropic magnetic field. Busch
ow et al. have reported heat treatment conditions for generating R2Fe+4C (K, H, Buschow et al.: J, L
e s s-Common~fet, 142.1988
．． pp. 349-357). [0003] [Problems to be Solved by the Invention] However, the reaction rate for producing R2FezC is very slow at temperatures below about 830°C, and at a certain temperature determined by the type of rare earth element (for example, when R is Nd, ℃) or higher, R2
Fe+4C will decompose. In this way R2Fe+4
The temperature range in which C is produced is very narrow, and the production reaction rate is very slow, requiring a long heat treatment (for example, 500 hours when R is Nd), which not only poses a serious problem in practical terms. There is a problem in that this long-term heat treatment causes grain growth, which causes a decrease in coercive force. In addition, it is difficult to obtain the unstable intermetallic compounds described above unless the manufacturing method relies on methods that have problems with mass production, such as ultra-quenching methods and mechanical alloying methods.
It was not possible to use powder metallurgy methods. [0004]
【課題を解決するための手段】本発明は、このような欠
点を解消し、Ｒ２Ｆｅｔ４Ｃ系合金の焼結体において高
エネルギー積を得ることを可能にしたものである。具体
的には本発明は、大きな飽和磁化を有する（ＨＲ，ＬＲ
）２ （Ｆ ｅ、 Ｔ） １４ｃ化合物を短時間のうち
に生成させると同時に、粒成長を抑制し、Ｒ２Ｆｅ＋４
Ｃ系合金による高エネルギー積異方性焼結磁石を実現す
る方法を提供するものである。すなわち、本発明の希土
類永久磁石は組成式： （ＨＲａ ＬＲ＋ｏｏ −ａ
） Ｉ Ｆ ｅｌｏｏ −ｘ−ｙ −、Ｔｙ ＣＸ（た
だし、ＨＲはＧｄ、 Ｔｂ、 Ｄｙ、 Ｈｏ、 Ｅｒ、
Ｔｍ、Ｌｕからなる重希土類元素の中から選んだ少な
くとも１種または２種以上、ＬＲはＣｅ、 Ｐｒ、 Ｎ
ｄ、 Ｓｍ、Ｅｕからなる軽希土類元素の中から選んだ
少なくとも１種または２種以上、ＴはＴ ｉ、 Ｖ 、
Ｃｒ、 Ｍｎ。
Ｚｒ、Ｎｂ、Ｍｏ、Ｈｆ、Ｔａ、Ｗの１種または２種以
上であり、原子百分率においてＸは１０〜１５％、ｙは
１０％以下，ｚは４〜１０％、ａは５〜５０％）で表さ
れることを特徴とする希土類永久磁石である。そして、
製法は粉末冶金法によることを特徴とする。
［０００５１以下これについて詳しく説明する。本発明
の永久磁石はＨＲ−ＬＲ−Ｆｅ−Ｔ−Ｃの５元系合金か
らなるもので、ＨＲはＧｄ、 Ｔｂ、 Ｄｙ、 Ｈｏ、
Ｅｒ、 Ｔｍ、Ｌｕからなる重希土類元素の中から選
んだ少なくとも１種または２種以上。ＬＲはＣｅ、 Ｐ
ｒ、 Ｎｄ、 Ｓｍ、Ｅｕからなる軽希土類元素の中か
ら選んだ少なくとも１種または２種以上。ＴはＴ ｉ、
Ｖ 、 Ｃｒ、 Ｍｎ。
Ｚｒ、Ｎｂ、Ｍｏ、Ｈｆ、Ｔａ、Ｗの各々１種以上であ
り、 （ＨＲ，ＬＲ）２Ｆｅ＋４Ｃ化合物を含んだもの
である。 （元素Ｔがある量までＦｅを置換する場合も
ある。
上記一般式において、希土類元素の総量は１０から１５
原子％の範囲とした。希土類元素の総量が少なすぎると
残留磁束密度（Ｂｒ）は向上するものの、保磁力が極端
に減少するため最大エネルギー積（（ＢＨ） ｍａｘ）
は減少する。したがって希土類元素の総量は１０原子％
以上とした。希土類元素の総量が多すぎると、残留磁束
密度（Ｂｒ）が減少し、この場合も最大エネルギー積（
（ＢＨ） ｍａｘ）が減少するので、１５原子％以下と
した。重希土類元素の量は少ないと （ＨＲ，ＬＲ）
２Ｆｅ１４ｃ化合物が生成しないので保磁力が大きくな
らない。
よって重希土類を５％以上置換することが必要である。
一方、重希土類が多いほど保磁力は大きくなるが、磁化
が減少するので軽希土類元素の量を越えないことが望ま
しい。よって、ａは５０％以下とした。
［０００６］さらに元素Ｔを添加すると、粒成長が抑制
され平均の結晶粒径を１０１００Ｌ以下にすることが可
能である。これによって保磁力の向上を図ることができ
る。しかし、１゛の量が多すぎると残留磁束密度（Ｂｒ
）が減少してしまい大きな最大エネルギー積（（ＢＨ）
ｍａＸ）が得られないので、Ｔ量は１０原子％以下で
なければならない。
（０００７］また、Ｃ量が多すぎると、残留磁束密度（
Ｂｒ）、および保磁力が減少し大きな最大エネルギー積
（（ＢＨ） ｍａｘ）が得られない。ｃ４が少なすぎる
と（ＨＲ，Ｌ Ｒ） ２ Ｆ ｅ １４ Ｃ化合物が生
成しないので、高保磁力が得られない。したがってＣ量
を４〜１０原子％とじた。
［０００８］なお、この発明では特性を維持しながら、
キュリー温度の上昇と耐食性を改善するのに、Ｃｏ、Ｎ
ｉの各々１種以上をＦｅに対して５０％まで置換するこ
とができる。[Means for Solving the Problems] The present invention eliminates these drawbacks and makes it possible to obtain a high energy product in a sintered body of an R2Fet4C alloy. Specifically, the present invention has large saturation magnetization (HR, LR
)2 (F e, T) 14c compound is generated in a short time, grain growth is suppressed, and R2Fe+4
The present invention provides a method for realizing a high-energy product anisotropic sintered magnet using a C-based alloy. That is, the rare earth permanent magnet of the present invention has a composition formula: (HRa LR+oo -a
) IF eloo -x-y -, Ty CX (however, HR is Gd, Tb, Dy, Ho, Er,
At least one or two or more selected from heavy rare earth elements consisting of Tm and Lu, LR is Ce, Pr, N
At least one or two or more light rare earth elements selected from light rare earth elements consisting of d, Sm, and Eu; T is Ti, V,
Cr, Mn. One or more of Zr, Nb, Mo, Hf, Ta, and W, and in terms of atomic percentage, X is 10 to 15%, y is 10% or less, z is 4 to 10%, and a is 5 to 50%. ) It is a rare earth permanent magnet characterized by the following. and,
The manufacturing method is characterized by a powder metallurgy method. [00051 This will be explained in detail below. The permanent magnet of the present invention is made of a quinary alloy of HR-LR-Fe-T-C, where HR is Gd, Tb, Dy, Ho,
At least one or two or more heavy rare earth elements selected from Er, Tm, and Lu. LR is Ce, P
At least one or two or more light rare earth elements selected from the group consisting of r, Nd, Sm, and Eu. T is T i,
V, Cr, Mn. It is one or more of each of Zr, Nb, Mo, Hf, Ta, and W, and contains a (HR, LR)2Fe+4C compound. (Element T may be substituted for Fe up to a certain amount. In the above general formula, the total amount of rare earth elements is 10 to 15
The range is atomic percent. If the total amount of rare earth elements is too small, the residual magnetic flux density (Br) will improve, but the coercive force will be extremely reduced, so the maximum energy product ((BH) max) will increase.
decreases. Therefore, the total amount of rare earth elements is 10 at%
That's all. If the total amount of rare earth elements is too large, the residual magnetic flux density (Br) will decrease, and in this case also the maximum energy product (
(BH) max) decreases, so the content was set to 15 atomic % or less. The amount of heavy rare earth elements is small (HR, LR)
Since no 2Fe14c compound is generated, the coercive force does not increase. Therefore, it is necessary to replace 5% or more of heavy rare earth elements. On the other hand, as the amount of heavy rare earth elements increases, the coercive force increases, but magnetization decreases, so it is desirable not to exceed the amount of light rare earth elements. Therefore, a was set to 50% or less. [0006] Furthermore, when element T is added, grain growth is suppressed and it is possible to reduce the average crystal grain size to 10100L or less. This makes it possible to improve the coercive force. However, if the amount of 1゛ is too large, the residual magnetic flux density (Br
) decreases, resulting in a large maximum energy product ((BH)
ma (0007) Also, if the amount of C is too large, the residual magnetic flux density (
Br) and coercive force decrease, making it impossible to obtain a large maximum energy product ((BH) max). If c4 is too small, the (HR, L R) 2 Fe 14 C compound will not be generated, and a high coercive force will not be obtained. Therefore, the amount of C was limited to 4 to 10 at%. [0008] In addition, in this invention, while maintaining the characteristics,
Co and N are used to increase the Curie temperature and improve corrosion resistance.
One or more of each of i can be substituted up to 50% with respect to Fe.
【実施例】表１に示す合金組成になるように純度９９゜
９％のＤｙ、Ｐｒ、ＦｅおよびＦｅ５Ｃを用いて、前訃
記組成のインゴットをアーク溶解で作成した。このイン
ゴットを窒素ガス雰囲気中でジェットミルにより平均程
径２〜１０μｍの大きさに微粉砕した。得られた微粉を
１０ｋＯｅの磁場中で配向後、１．５ｔ、−’Ｃｍ２の
圧力てプレス成形した。この成形体をアルゴンガス中で
、１０００〜１２００℃で１時間焼結を行った後、５０
０〜９００℃でさらに２時間熱処理した後、急冷した。
熱処均後の異方性焼結体の残留磁束密度、保磁力、最大
エネルギー積を測定したところ、表２に示す結果が得ら
れた。
試料Ｎｏ、４は比較例である。本発明に係る永久磁石Ｃ
磁気特性の優れていることが判る。EXAMPLE An ingot having the composition described above was prepared by arc melting using Dy, Pr, Fe and Fe5C with a purity of 99.9% so as to have the alloy composition shown in Table 1. This ingot was pulverized to an average diameter of 2 to 10 μm using a jet mill in a nitrogen gas atmosphere. The obtained fine powder was oriented in a magnetic field of 10 kOe and then press-molded at a pressure of 1.5 t, -'Cm2. This molded body was sintered at 1000 to 1200°C for 1 hour in argon gas, and then
After further heat treatment at 0 to 900°C for 2 hours, it was rapidly cooled. The residual magnetic flux density, coercive force, and maximum energy product of the anisotropic sintered body after heat treatment were measured, and the results shown in Table 2 were obtained. Sample No. 4 is a comparative example. Permanent magnet C according to the present invention
It can be seen that the magnetic properties are excellent.
【表１］
［００１１１
【発明の効果】本発明によれば、ＬＲ−Ｆｅ−Ｃ系に重
希土類元素ＨＲ，および元素Ｔを所定量加えることによ
り、通常の粉末冶金法によって、 （ＨＲ，ＬＲ） ２
Ｆ ｅＮＣ化合物を安定に生成させると同時に、粒成長
を抑制し保磁力の発生に適した金属組織を実現すること
ができ、大きな最大エネルギー積（（ＢＨ） ｍａｘ）
を有する永久磁石が得られる。[Table 1] [Effect of the invention] According to the present invention, by adding a predetermined amount of heavy rare earth element HR and element T to the LR-Fe-C system, (HR, LR ) 2
It is possible to stably generate FeNC compounds, suppress grain growth, and realize a metal structure suitable for generating coercive force, resulting in a large maximum energy product ((BH) max).
A permanent magnet having the following properties is obtained.
Claims (3)
＿ａ）＿ｘＦｅ＿１＿０＿０＿−＿ｘ＿−＿ｙ＿−＿２
Ｔ＿ｙＣ＿２（ただし、ＨＲはＧｄ，Ｔｂ，Ｄｙ，Ｈｏ
，Ｅｒ，Ｔｍ，Ｌｕからなる重希土類元素の中から選ん
だ少なくとも１種または２種以上、ＬＲはＣｅ，Ｐｒ，
Ｎｄ，Ｓｍ，Ｅｕからなる軽希土類元素の中から選んだ
少なくとも１種または２種以上、ＴはＴｉ，Ｖ，Ｃｒ，
Ｍｎ，Ｚｒ，Ｎｂ，Ｍｏ，Ｈｆ，Ｔａ，Ｗの１種または
２種以上であり、原子百分率においてｘは１０〜１５％
．ｙは１０％以下，ｚは４〜１０％，ａは５〜５０％）
で表されることを特徴とする希土類永久磁石。Claim 1: Compositional formula: (HR_aLR_1_0_0_-
_a)_xFe_1_0_0_-_x_-_y_-_2
T_yC_2 (However, HR is Gd, Tb, Dy, Ho
, Er, Tm, and Lu, and LR is Ce, Pr,
At least one or two or more light rare earth elements selected from the light rare earth elements consisting of Nd, Sm, and Eu; T is Ti, V, Cr,
One or more of Mn, Zr, Nb, Mo, Hf, Ta, W, and x is 10 to 15% in atomic percentage
．． y is 10% or less, z is 4-10%, a is 5-50%)
A rare earth permanent magnet characterized by:
類永久磁石。2. The rare earth permanent magnet according to claim 1, which is an anisotropic sintered body.
求項２に記載の希土類永久磁石。3. The rare earth permanent magnet according to claim 2, wherein the average crystal grain size is 100 μm or less.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2404028A JPH04209504A (en) | 1990-12-03 | 1990-12-03 | Rare-earth permanent magnet |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2404028A JPH04209504A (en) | 1990-12-03 | 1990-12-03 | Rare-earth permanent magnet |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH04209504A true JPH04209504A (en) | 1992-07-30 |
Family
ID=18513723
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2404028A Pending JPH04209504A (en) | 1990-12-03 | 1990-12-03 | Rare-earth permanent magnet |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH04209504A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP1085531A3 (en) * | 1999-09-14 | 2001-08-29 | Yingchang Yang | Multielement interstitial hard magnetic material and process for producing magnetic powder and magnet using the same |
-
1990
- 1990-12-03 JP JP2404028A patent/JPH04209504A/en active Pending
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP1085531A3 (en) * | 1999-09-14 | 2001-08-29 | Yingchang Yang | Multielement interstitial hard magnetic material and process for producing magnetic powder and magnet using the same |
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