JPS60171703A - Manufacture of permanent magnet - Google Patents
Manufacture of permanent magnetInfo
- Publication number
- JPS60171703A JPS60171703A JP59028338A JP2833884A JPS60171703A JP S60171703 A JPS60171703 A JP S60171703A JP 59028338 A JP59028338 A JP 59028338A JP 2833884 A JP2833884 A JP 2833884A JP S60171703 A JPS60171703 A JP S60171703A
- Authority
- JP
- Japan
- Prior art keywords
- aging
- rare earth
- sintering
- temperature
- magnetic field
- 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
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
- H01F1/057—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B
- H01F1/0571—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes
- H01F1/0575—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes pressed, sintered or bonded together
- H01F1/0577—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes pressed, sintered or bonded together sintered
Abstract
Description
【発明の詳細な説明】
本発明は主に希土類金Ｒ（以下Ｒと略記する。）とＦｅ
からなる金属間化合物永久磁石材料の製造法に関するも
のである。特にＢ添加によって改良されたＲ−Ｆｅ −
Ｂ系永久磁石材料の製造法に関するものである。Detailed Description of the Invention The present invention mainly focuses on rare earth metals R (hereinafter abbreviated as R) and Fe.
The present invention relates to a method for producing an intermetallic compound permanent magnet material comprising: In particular, R-Fe − improved by B addition
The present invention relates to a method for manufacturing B-based permanent magnet materials.
すでに知られているように、Ｒ−Ｆｅ合金、例えばＲ２
Ｆ ｅｐｙはＲ−Ｇｏ合金よりも高い飽和磁化を有し、
高価なＧｏを含有せず、永久磁石材料として高いポテン
シャルを有する永久磁石材料である。しかしながら、永
久磁石材料として必要な工ＨＣが得られず、長い間装置
されたままであツた。近年、液体急冷技術の進歩にとも
ない、Ｒ−Ｆｅ合金に本方法を利用し、高い保磁力を得
ることに成功している。（例えば、Ｊ、 Ｊ、 Ｃｒｏ
ａｔ。As already known, R-Fe alloys, e.g. R2
Fepy has higher saturation magnetization than R-Go alloy,
It is a permanent magnet material that does not contain expensive Go and has high potential as a permanent magnet material. However, the required HC as a permanent magnet material could not be obtained, and the device remained in use for a long time. In recent years, with the progress of liquid quenching technology, this method has been successfully applied to R-Fe alloys to obtain high coercive force. (For example, J, J, Cro
at.
Ｊｏｕｒｎａｌ ｏｆ Ａｐｐｌｉｅｄ Ｐｈｙｓｉｃ
ｓ ５２（３）Ｍａｒｃｈ １９８１．２５０９“Ｍ
ａｏｎ８ｔｉｃ Ｐ ｒｏｌ）ｆｌｒｔｉｅｓｏｒ ａ
＋ｅ＋ｔ−５ｐｕｎ ｐｒ −Ｆｅ ａｌｌｏｙｓ”）
さらに、Ｎ、、 Ｇ、 Ｋ、ｏｏｎらはＢを微量添加し
たＲ−Ｆｅ−８合金を超急冷し、６００〜８００℃ｋＴ
ＩＬ″ｉ効結晶化させることにより高保磁力を実現して
いる。（Ｎ、 Ｃ，Ｋｏｏｎ ｅｔ ａｌ Ａｐｐｌ、
ＰｈｙｓＬｅｔｔｅｒ３９（１０）１５（１９８１）
８４０ ”ＭａｇｎｅｔｉｃＰｒｏｐｅｒｔｉｅｓ ０
ｆＡＩＯｒｌｌｈＯＩｊＳ ａｎｄ ｃｒｙｓｔａｉ＋
ｚｅｄＦ ｅｏ、ｓｚ Ｆ１ａ、Ｉｇ ＞、、９Ｔ ｂ
ｏ、ｏｓ Ｌ ａｏ、佑”、特開昭５８−１２３８５３
号公報）しかしながら上記作製法においては結晶質と非
晶質の混合状態が必要であり、得られる材料の形態は一
般に粉末ないし薄帯に限定される。Journal of Applied Physics
s 52(3) March 1981.2509 “M
aon8tic Prol) flrtiesor a
+e+t-5pun pr -Fe alloys")
Furthermore, N, G, K, oon et al.
A high coercive force is achieved by crystallizing the IL″i effect. (N, C, Koon et al Appl,
Phys Letter 39 (10) 15 (1981)
840 ”MagneticProperties 0
fAIOrllhOIjS and crystal+
zedF eo, sz F1a, Ig >, 9T b
o, os L ao, Yu”, JP-A-58-123853
However, the above production method requires a mixed state of crystalline and amorphous materials, and the form of the obtained material is generally limited to powder or ribbon.
したがって、永久磁石材料として利用する際には圧縮成
形等によってバルク化をはかってやる必要がある。又、
超急冷による粉末は等方性で角型が悪く着磁が困雌で実
用の際問題が多い。Therefore, when using it as a permanent magnet material, it is necessary to bulk it by compression molding or the like. or,
Powder produced by ultra-quenching is isotropic, has a poor square shape, and is difficult to magnetize, causing many problems in practical use.
一方、併用らは結晶質のＮｄ −Ｆｅ −Ｂを用い磁場
中成形、焼結を用い異方性化をはかり高特性を得た。（
第２９回３ＭＣｏｎｆ、１９８３ ｂｏｏｋｌｅｔ Ｐ
１１０、３ｅｓｓｉｏｎＥ Ｂ、 Ｅ Ｂ −１”Ｎ
ｅｗ Ｍａｔｅｒｉａｌｆｏｒ ｐｅｒｍａｎｅｎｔ
Ｍａｇｎｅｔｓ ｏｎ ａ ｂａｓｅ ｏｆ Ｎ ｄａ
ｎｄ Ｆｅ ” ）得られた磁気特性は、３５〜４０〜
Ｉ Ｇ Ｏｓで希土類磁石の中では最も高い。しかしな
がら水系磁石のキュＩＪ、一点は３００℃前俊であり、
熱安定性に問題があった。すなわち、水系磁石を加熱し
た場合、熱によって磁化の反転が生じ、減磁しやすい傾
向を持つ。本欠点を改良するためには工Ｈ（。On the other hand, in the combination, crystalline Nd-Fe-B was used, and high properties were obtained by molding and sintering in a magnetic field to obtain anisotropy. (
29th 3MConf, 1983 booklet P
110, 3essionE B, E B -1”N
ew Material for permanent
Magnets on a base of N da
nd Fe”) The obtained magnetic properties are 35~40~
IG Os is the highest among rare earth magnets. However, the water-based magnet Kyu IJ, one point is 300℃ Maetoshi,
There was a problem with thermal stability. That is, when a water-based magnet is heated, the heat causes a reversal of magnetization, which tends to cause demagnetization. In order to improve this drawback, it is necessary to
の増加をはかるのが１つの方法である。すでに知られて
いる熱処理法は焼結後６００℃近傍で加熱するというも
のである。（第２９回３ＭＣｏｎｆ、発表）しかしなが
ら、本然処理方法では得られる。ｌ−Ｉ Ｃにも限界が
あり、熱処理による。１−Ｉ Ｃのバラツキも多かった
。One method is to increase the A known heat treatment method involves heating at around 600° C. after sintering. (Presentation at the 29th 3MConf) However, it can be obtained with the original processing method. L-IC also has a limit, which depends on heat treatment. There were also many variations in 1-IC.
本発明はこれらＲ−Ｆｅ −Ｂ合金の＞ＨＣ向上。The present invention improves >HC of these R-Fe-B alloys.
工ｌ−１，０のバラツキの低減を目的になされたもので
、熱処理を焼結温度から５０〜１００℃低い温度範囲か
ら始め、低温側へ順次多段ないし連続冷却で時効を加え
、４００〜６００℃の温度範囲で時効終了後急冷するこ
とにより上記目的を達成したものである。This was done with the purpose of reducing the variation in the sintering temperature, starting at a temperature range of 50 to 100 degrees Celsius lower than the sintering temperature, and then aging to a temperature range of 400 to 600 degrees Celsius through multi-stage or continuous cooling. The above object was achieved by rapidly cooling the material after aging in the temperature range of .degree.
本発明の熱処理は高温側から多段時効ないし連続冷却に
よって行われる。時効開始温度は焼結温度から５０〜１
００℃低い温度領域が選ばれる。焼結温度と時効開始温
度の差が５０℃以下の場合は時効による加熱によって結
晶成長が生じ、ｚＨｏの低干が見られ好ましくない。（
時効開始温度は焼結温度よりも低い。〉焼結温度と時効
開始温度の差が１００℃以上の場合は、高工Ｈｅ、を得
るための初期状態が得られない。時効終了彎の急冷開始
温度は４００〜６００℃が選ばれる。急冷開始温度が４
００℃以下の場合急冷効果が得られず、６００℃以上の
場合は高い＞ＨＣが得られない。The heat treatment of the present invention is performed by multi-stage aging or continuous cooling from the high temperature side. The aging start temperature is 50 to 1 from the sintering temperature.
A temperature range lower than 0.0°C is selected. If the difference between the sintering temperature and the aging start temperature is 50° C. or less, crystal growth will occur due to heating due to aging, which is undesirable because low drying of zHo will be observed. (
The aging start temperature is lower than the sintering temperature. > If the difference between the sintering temperature and the aging start temperature is 100° C. or more, the initial state for obtaining high-quality He cannot be obtained. The quenching start temperature at the end of aging is selected to be 400 to 600°C. Rapid cooling start temperature is 4
If the temperature is 00°C or lower, no quenching effect can be obtained, and if the temperature is 600°C or higher, a high >HC cannot be obtained.
本発明の適用できる永久磁石は一般に溶解によるインゴ
ット作成、粉砕、磁界中成形、焼結、熱処理の工程によ
って製造される。溶解は通常の方法で、Ａｒ中ないし真
空中で行う。Ｂはフェロボロンを用いることも可能であ
る。′ｔ！Ａ砕は粗粉砕と微粉砕に工程的にはわかれる
が、粗粉砕はスタンプミル、ジョークラッシセ、ブラウ
ンミル、ディスクミルで、又微粉砕はジェットミル、振
動ミル。Permanent magnets to which the present invention can be applied are generally manufactured by the steps of melting into an ingot, crushing, forming in a magnetic field, sintering, and heat treatment. The melting is carried out in a conventional manner in Ar or vacuum. It is also possible to use ferroboron for B. 't! Process-wise, A-grinding can be divided into coarse grinding and fine grinding. Coarse grinding involves stamp mills, jaw crushers, brown mills, and disc mills, while fine grinding uses jet mills and vibration mills.
ボールミル等で行われる。いずれも酸化を防ぐために非
酸化性雰囲気中で行うが、有ｍ溶媒や不活性ガスが用い
られる。粉砕粒度は３〜５μｓ （Ｆ。This is done using a ball mill, etc. Both are carried out in a non-oxidizing atmosphere to prevent oxidation, and a solvent or an inert gas is used. The grinding particle size is 3-5 μs (F.
Ｓ、Ｓ、Ｓ、）が望ましい。磁界中成形は配向度向上、
異方性化のために必要で、一般に縦磁場成形（加圧方向
と磁場印加方向が平行）および横磁場成形（加圧方向と
磁場印加方向が垂直）が用いられる。横磁場成形の方が
組繊Ｓ成形よりも配向度は優れている。焼結はＡｒ 、
Ｈｅ等の不活性ガス中又は真空中で行われる。さらに
はＮ２ガス中の焼結も可能である。焼結後の冷却は急冷
が望ましい。S, S, S, ) is desirable. Molding in a magnetic field improves orientation,
This is necessary for anisotropy, and generally vertical magnetic field shaping (the direction of pressure and the direction of magnetic field application are parallel) and transverse magnetic field shaping (the direction of pressure and the direction of magnetic field application are perpendicular) are used. Transverse magnetic field molding has a better degree of orientation than fiber S molding. Sintering is Ar,
It is carried out in an inert gas such as He or in vacuum. Furthermore, sintering in N2 gas is also possible. Rapid cooling is preferable for cooling after sintering.
以下、実施例により本発明を説明する。The present invention will be explained below with reference to Examples.
実施例１
Ｎｄ （Ｆｅα’ｌ Ｂ、１ ）ＥｔＦ、、なる組成を
有する合金をアーク溶解にて作製した。得られたインゴ
ットをスタンプミルおよびディスクミルで粗粉砕した。Example 1 An alloy having a composition of Nd(Feα'l B,1)EtF was produced by arc melting. The obtained ingot was coarsely ground using a stamp mill and a disc mill.
粗粉砕粉をジェットミルを用いて微粉砕した。粉砕媒体
はＮ２ガスであり、粉砕粒度は３．４μ■（Ｆ、Ｓ、Ｓ
、Ｓ、）であった。得られた微粉砕粉な１５ｋＯｅの磁
場中で横磁場成形した。成形圧力は２ｔｏｎ／ ｃｍ”
である。得られた成形体をＡｒ雰囲気中で２段焼結した
。第１段は１０８０℃Ｘ１ｈｒ、第２段は１１００℃×
１ｈ「であり、焼結後Ａ「気流中に急冷した。急冷後の
磁気特性は以下の通りであるＢ「〜１２１００Ｇ
、ｌ−１ｃ 〜８８０００ｓ
ｚＨｃ 〜９３’０００ｅ
（Ｂ Ｈ） ｗａｘ 〜３４，５Ｍ ＧＯｅ本磁石に１
０００℃ｘｌｈｒ ＋ ９００℃×柚ｒ ＋ ８００℃
ｘｌｈｒ ＋ ７００℃ｘｌｈｒ ＋ ６００℃Ｘ１ｈ
ｒ ＋ ５００℃×Ｉｈｒの多段時効を施し急冷したと
ころ、以下の磁気特性を得た。The coarsely ground powder was finely ground using a jet mill. The grinding medium is N2 gas, and the grinding particle size is 3.4μ■ (F, S, S
,S,). The resulting finely pulverized powder was subjected to transverse magnetic field molding in a magnetic field of 15 kOe. Molding pressure is 2ton/cm”
It is. The obtained compact was sintered in two stages in an Ar atmosphere. The first stage is 1080℃×1hr, the second stage is 1100℃×
1h", and after sintering A" was quenched in an air stream.The magnetic properties after quenching are as follows: 5M GOe book magnet 1
000℃xlhr + 900℃×Yuzur + 800℃
xlhr + 700℃xlhr + 600℃X1h
When it was subjected to multi-stage aging at r + 500°C x Ihr and rapidly cooled, the following magnetic properties were obtained.
Ｂｒ−１２１５０Ｇ
ＢＨｃ〜 ９８００〜
工ＨＣ〜１４２０００ａ
（Ｂ Ｈ） ｍａＸ 〜３５．６Ｍ Ｇ Ｏｅなお、焼
結後の磁石に６００℃Ｘ１１１ｒの時効を施し急冷した
場合味、以下の磁気特性を示した。Br-12150G BHc ~ 9800 ~ Engineering HC ~ 142000a (B H) maX ~ 35.6M G Oe Note that when the sintered magnet was aged at 600°C x 111r and rapidly cooled, it exhibited the following magnetic properties.
Ｂｒ 〜 １２１００Ｇ
ＢＨｃ 〜９１０００ｅ
ｊｌ：１」Ｃ〜１１９０００ｅ
（ＢＨ）Ｉｌａｘ〜３４．８ＭＧＯｅ
６００℃×柚ｒの時効と比較して多段時効の方が高いｐ
ＨＣを得るために効果があり、角型も改良され、高（Ｂ
Ｈ） ｗａｘが得られる。Br ~ 12100G BHc ~ 91000e jl: 1'' C ~ 119000e (BH) Ilax ~ 34.8MGOe Multi-stage aging has higher p than aging at 600℃ x Yuzuri
It is effective for obtaining HC, the square shape is also improved, and high (B
H) Wax is obtained.
実施例２
Ｐｒ （Ｆｅ０．９Ｂ、、）５ なる組成を有する合金
を実施例１と同様の方法で溶解、粉砕、磁界中成形。Example 2 An alloy having the composition Pr (Fe0.9B,,)5 was melted, pulverized, and molded in a magnetic field in the same manner as in Example 1.
焼結した。本磁石に種々の時効を加えた結果を第１表に
示す。第１表中の時効の内容は第２表に示す。Sintered. Table 1 shows the results of applying various types of aging to this magnet. The contents of the statute of limitations in Table 1 are shown in Table 2.
実施例３
Ｎ ｄｏ、１） Ｐ ｒ ｈ４ （Ｆ ｅｏ、Ｉ Ｂｏ
、０ｉａＳ ｉｏ、□Ｊ ）５ なる組成を右する合金
を実施例１と同様に溶解、粉砕、磁場中成形し゛た。焼
結は１１００℃Ｘ ｉｈｒ ＋ １１２０℃Ｘ１ｈの２
段焼結を行い、Ａｒ気流中に急冷した。急冷後ＧＯＯ℃
×柚ｒの時効を施したところ、以下の磁気特性を得た。Example 3 N do, 1) P r h4 (F eo, I Bo
, 0iaS io, □J)5 was melted, crushed, and molded in a magnetic field in the same manner as in Example 1. Sintering is 1100℃ x ihr + 1120℃ x 1h 2
Stage sintering was performed and quenching was performed in an Ar stream. GOO℃ after quenching
When subjected to the aging of ×Yuzu, the following magnetic properties were obtained.
Ｂｒ 〜 １１７００Ｇ
ｐＨＣ〜９３０００ｅ
シ１−ＩＣ〜 １３３０００ｅ
（［３’ ＠ ） １ｌａＸ 〜３３．５Ｍ Ｇ Ｏｓ
であった。Br ~ 11700G pHC ~ 93000e Si1-IC ~ 133000e ([3' @ ) 1laX ~33.5M G Os
Met.
さらに１０００℃Ｘ１ｂｒ保持後１．３℃／１ｎで６０
０℃まで連続冷却し、１時間保持後Ａｒ気流中に急冷し
た。得られた磁気特性は、
Ｂｒ 〜１１７２０Ｇ
ＢＨＣ〜９５０００ｅ
工ＨＣ〜１７２００ｏ１１
（３１−１） ｗａｘ ”−３３，８ＭＧＯｅであった
。Further, after holding at 1000℃X1br, 60 at 1.3℃/1n
It was continuously cooled to 0° C., kept for 1 hour, and then rapidly cooled in an Ar gas flow. The obtained magnetic properties were: Br~11720G BHC~95000e Engineering HC~17200o11 (31-1) wax''-33,8MGOe.
実施例４
Ｎ ｄ （Ｆ ｅ（１，６ＣＯｏ、ｔ Ｂ６．１）６４
なる合金を実施例１と同様の方法で溶解、粉砕、磁場中
成形、焼結した。焼結後６００℃ｘｌｈｒの時効を加え
た結果、以下の磁気特性を得た。Example 4 N d (F e (1,6 COo, t B6.1) 64
The alloy was melted, crushed, formed in a magnetic field, and sintered in the same manner as in Example 1. As a result of aging at 600°C x lhr after sintering, the following magnetic properties were obtained.
Ｂ「〜１０７５０Ｇ
βＨａ〜 ８７００へ
＞ＨＣ〜９９０００ｅ
（Ｂ ｌ−１） ｅ＋ａｘ 〜２７．ＩＭ Ｇ Ｏｓさ
らに１０００℃から多段時効を行った。すなわち、１０
００℃ｘ１ｈｒ ＋ ９００℃×柚ｒ ＋ ８００℃Ｘ
１ｈｒ＋７００℃ｘ１ｈｒ ＋６００℃ｘｌｈｒ ＋５
００℃ｘ １ｈｒの時効Ｉ支Ａ ｒ中に急冷した。得ら
れた磁気特性は、Ｂｒ 〜１０８２０Ｇ
ｆＪＨＣ〜９３００ｏｅ
工１−ＩＣ〜１３８０００ｅ
（Ｂ Ｈ） ｌａｘ 〜２８．ＩＭ ＧＯｅであった。B'~10750G βHa~ To 8700 > HC~99000e (B l-1) e+ax ~27. IM G Os Further, multi-stage aging was performed from 1000°C. That is, 10
00°C x 1hr + 900°C x Yur + 800°C
1hr+700℃x1hr +600℃xlhr +5
The sample was rapidly cooled during aging at 00° C. for 1 hr. The obtained magnetic properties are: Br ~10820G fJHC ~9300oe Engineering 1-IC ~138000e (B H) lax ~28. It was IM GOe.
Claims (1)
土類元素の１種又は２１！以上の組合せ、０≦Ｘ≦０．
３゜０．０２≦Ｂ≦０．１５．４≦Ａ≦８、ただしＦｅ
の１部をＭｎ、Ｎｉで、又Ｂの１部をＳｉ、Ｇｅで置換
可能である。）なる組成を有する合金を溶解。 粉砕、磁場中成形、焼結、熱処理を施す希土類磁石の製
造法において、熱処理を焼結湿度から５０〜１００℃低
い温度領域から始め、低温側へ順次多段ないし連続冷却
により時効を加え、４００〜６００℃の温度範囲で時効
終了後急冷することを特徴とする永久磁石の製造方法。[Claims] R(Fe, -, Co, By)A (where R: one kind of rare earth element or a combination of 21! or more, 0≦X≦0.
3゜0.02≦B≦0.15.4≦A≦8, but Fe
A part of B can be replaced with Mn or Ni, and a part of B can be replaced with Si or Ge. ) is melted. In the manufacturing method of rare earth magnets, which involves crushing, forming in a magnetic field, sintering, and heat treatment, heat treatment is started at a temperature range of 50 to 100 degrees Celsius lower than the sintering humidity, and then aging is applied by multi-stage or continuous cooling in order to lower temperatures, and the temperature range is 400 to 400 degrees Celsius. A method for producing a permanent magnet, characterized by rapid cooling after aging in a temperature range of 600°C.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP59028338A JPS60171703A (en) | 1984-02-17 | 1984-02-17 | Manufacture of permanent magnet |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP59028338A JPS60171703A (en) | 1984-02-17 | 1984-02-17 | Manufacture of permanent magnet |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS60171703A true JPS60171703A (en) | 1985-09-05 |
Family
ID=12245816
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP59028338A Pending JPS60171703A (en) | 1984-02-17 | 1984-02-17 | Manufacture of permanent magnet |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS60171703A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6293908A (en) * | 1985-10-19 | 1987-04-30 | Tohoku Metal Ind Ltd | Manufacture of rare-earth magnet |
| JPS6342102A (en) * | 1986-08-07 | 1988-02-23 | Tohoku Metal Ind Ltd | Manufacture of sintered rare-earth magnet |
-
1984
- 1984-02-17 JP JP59028338A patent/JPS60171703A/en active Pending
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6293908A (en) * | 1985-10-19 | 1987-04-30 | Tohoku Metal Ind Ltd | Manufacture of rare-earth magnet |
| JPS6342102A (en) * | 1986-08-07 | 1988-02-23 | Tohoku Metal Ind Ltd | Manufacture of sintered rare-earth magnet |
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