JPH0467322B2 - - Google Patents

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Publication number
JPH0467322B2
JPH0467322B2 JP58079096A JP7909683A JPH0467322B2 JP H0467322 B2 JPH0467322 B2 JP H0467322B2 JP 58079096 A JP58079096 A JP 58079096A JP 7909683 A JP7909683 A JP 7909683A JP H0467322 B2 JPH0467322 B2 JP H0467322B2
Authority
JP
Japan
Prior art keywords
permanent magnet
isotropic
magnet material
present
materials
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.)
Expired - Lifetime
Application number
JP58079096A
Other languages
Japanese (ja)
Other versions
JPS59204209A (en
Inventor
Setsuo Fujimura
Masato Sagawa
Yutaka Matsura
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Proterial Ltd
Original Assignee
Sumitomo Special Metals Co Ltd
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Sumitomo Special Metals Co Ltd filed Critical Sumitomo Special Metals Co Ltd
Priority to JP58079096A priority Critical patent/JPS59204209A/en
Priority to CA000444488A priority patent/CA1277159C/en
Priority to DE8383113252T priority patent/DE3380612D1/en
Priority to EP19830113252 priority patent/EP0124655B1/en
Priority to US06/567,640 priority patent/US4840684A/en
Publication of JPS59204209A publication Critical patent/JPS59204209A/en
Priority to SG49090A priority patent/SG49090G/en
Priority to HK68390A priority patent/HK68390A/en
Priority to US07/717,002 priority patent/US5192372A/en
Publication of JPH0467322B2 publication Critical patent/JPH0467322B2/ja
Granted legal-status Critical Current

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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
    • H01F1/06—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 in the form of particles, e.g. powder
    • H01F1/08—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 in the form of particles, e.g. powder pressed, sintered, or bound together
    • H01F1/086—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 in the form of particles, e.g. powder pressed, sintered, or bound together sintered

Landscapes

  • Engineering & Computer Science (AREA)
  • Power Engineering (AREA)
  • Powder Metallurgy (AREA)
  • Hard Magnetic Materials (AREA)

Description

【発明の詳細な説明】[Detailed description of the invention]

本発明は等方性永久磁石材料に関する。本発明
においてＲは希土類元素を示す記号として用い
る。 永久磁石材料は一般家庭で使用される各種電気
製品から産業用大型コンピユーターの周辺末端機
まで巾広い分野で使用される極めて重要な電気、
電子材料の一つである。 また、近年の電気、電子機器の小型化高効率化
の要求に伴ない永久磁石材料はますます高性能化
が求められるようになつた。永久磁石の中でも等
方性磁石は性能的に異方性磁石にかなわない点も
あるが形状や磁化方向に制約を受けないため重用
されてきた。 等方性永久磁石は従来磁石材料として用いられ
る殆んど全てのものから作られている。しかし、
フエライト、アルニコ、MnA，FeCrCo磁石で
はエネルギー積（BH）maxが高々2MGOeであ
りSmCo磁石の場合で４〜5MGOeと異方性磁石
の場合の1/4〜1/6である。SmCo磁石材料は、
Sm，Co共資源が希少なため高価であり、磁石を
大量生産するための材料としては好ましくない。 そこでSmに代り資源的に豊富な軽希土類例え
ばCe，Nd，Pr等を用い、Coに代りFeを用いる
ことが望まれている。しかし、軽希土類とFeは
均質に相互溶融し、冷却して結晶化した場合でも
磁石材料として適した金属間化合物を形成しない
ことがよく知られている。さらに、このような軽
希土類−Fe合金の磁力を粉末治金法によつて強
化する試みも成功しなかつた（特開昭57−
210934、明細書６頁参照）。これに対し、特開昭
57−210934において、Fe−Ｒ系非晶質合金が溶
融急冷により得られることが開示され、Fe−Ｒ
（ＲとしてCe，Pr，Nd，Sm，Eu等）、特にFe−
Ndの二元系合金を液体急冷法により非晶質リボ
ンとしこれを磁化して磁石とすることが提案され
ている。この方法では（BH）maxが４〜
5MGOeのものが得られるが数μm〜数10μmの厚
さのリボンであるため実用的なバルクにするには
積層か粉末化後プレスが必要となりいずれの方法
でも理論密度化が60〜80％位に低下し磁石特性は
さらに低下して実用的なものでなくなつてしま
う。 このFe−Ｒ二元系組成を本発明者等は粉末治
金法による焼結体として得ることを試みたが、本
明細書第１表のNo.C1に示す如く、Hc，（BH）
max共殆んど零であり、FeR二元系焼結体は、実
用的な磁石材料とはならない。 従つて本発明は、上述の従来の等方性永久磁石
材料に代わる新規な等方性永久磁石材料を提供す
ることを基本目的とし、特に、資源的に豊富な材
料から成るFe及びＲを用い実用上十分高い磁気
特性を有する等方性永久磁石材料を提供せんとす
るものである。 すなわち本発明の等方性永久磁石材料は原子百
分率で10〜25％のＲ、３〜23％のＢ、および残部
実質的にFeからなり磁気的に等方性でありかつ
Ｒ−Fe−Ｂ三元化合物に基づく実質的に完全な
結晶質であり、但し、ＲはNd，Pr，Dy，Ho，
Tbの少なくとも一種特にＲの50％以上がNdとPr
の一種又は二種（第１の発明）、又はこれらと
La，Ce，Pm，Sm，Eu，Gd，Er，Tm，Yb，
Lu，Ｙの少なくとも一種であつてＲの50％以上
がNdとPrの一種又は二種（第２の発明）であ
る。 本発明者等は先にSm，Coを必ずしも用いる必
要のないFeBR系永久磁石材料を発明した（特開
昭57−145072）。このFeBR系永久磁石材料は、
従来知られているRCo5やR2Co17化合物とは異な
る新しい化合物を基礎とし、特にボロン（Ｂ）
は、従来の、たとえば非晶質合金作成時の非晶質
促進元素又は粉末治金法における焼結促進元素と
して添加されるものではなく、このFeBR系永久
磁石材料の実態的内容を構成する磁気的に安定で
高い磁気異方性定数を有するＲ−Fe−Ｂ化合物
の必須構成元素であることを明らかにした。（な
お、上記FeBR系永久磁石材料に基づき、適当な
ミクロ組織を形成することによつて磁気異方性焼
結永久磁石が得られることも明らかにした。 本発明者等は前記目的を達成するためにさらに
等方性永久磁石材料についても鋭意研究の結果、
FeBRを用いて良好な等方性永久磁石材料が得ら
れる知見を得て本発明に至つた。本発明で得られ
るFeBR系等方性永久磁石材料はSmCo系等方性
磁石材料の特性と同等以上でしかも希少かつ高価
なSmを必ずしも用いる必要がなく、Coを使用す
る必要がないので安価であり、極めて実用的なも
のである。 本発明において、「等方性」とは、実質的に等
方性であることをもつて足り、例えば磁場を印加
しないで成形することにより得られる。 本発明においてＲ及びＢの量は、本永久磁石材
料の典型的最終製品たる等方性焼結体永久磁石と
する場合を考慮して限定したものであり、その限
定は以下の理由による（以下％は特に指定なき場
合原子百分率比を示す）。Ｒは、７〜８％あたり
で保磁力（iHc）が出現して急峻に立上り、以後
Ｒ量が増加するに従つてiHcは増加するが、Brは
iHcよりやや早く立上がるが、10％当りで最大値
を経た後減少する（第１図参照）。かくて等方性
焼結磁石として（BH）max2MGOe以上を満足
するＲ量は10％以上でかつ25％以下である。また
Ｒは多量になると燃え易く取扱いが危険、困難に
なる。 Ｂは、第２図に示すごとく、少量の含有で保磁
力（iHc）が出現し、含有量の増加とともに増加
する。一方、残留磁束密度Brは、含有量の増加
とともに一旦増加し最大値に達したのち減少す
る。そのため、等方性焼結磁石として保磁力
1kOe、最大エネルギー積2MGOe以上を得るため
の範囲として、３〜23％とする。 好ましくはNd，Prの１種又は２種をＲの主成
分（全Ｒ中Nd，Prが50原子％以上）とし12〜20
％のＲ，５〜18％のＢ、残部Feの組成では
（BH）max4MGOe以上の高い磁気特性を示す。
最も好ましい範囲としてNd，Prの１種又は２種
をＲの主成分とし12〜16％のＲ，６〜18％のＢ、
残部Feの組成で（BH）maxが7MGOe以上で等
方性永久磁石材料ではかつて無い高い特性が得ら
れる。 Ｒとしては資源的に豊富な軽希土類を用いるこ
とができ、必ずしもSmを必要とせず或いはSmを
主体とする必要もないので原料が安価でありきわ
めて有用である。 本発明の永久磁石材料に用いる希土類元素Ｒは
Ｙを包含し軽希土類及び重希土類を包含する希土
類元素でありそのうち所定の一種以上を用いる。
即ちこのＲとしてはNd，Pr，La，Ce，Tb，
Dy，Ho，Er，Eu，Sm，Gd，Pm，Tm，Yb，
Lu及びＹが包含される。Ｒとしては軽希土類を
もつて足り特にNd，Prが好ましい。また通例Ｒ
のうち一種をもつて足りるが実用上は二種以上の
混合物（ミツシユメタル、ジジム等）を入手上の
便宜等の理由により用いることが出来、Sm，Ｙ，
La，Ce等は他のNd，Pr等の軽希土類と混合して
用いることができる。なお、このＲは純希土類元
素でなくともよく、工業上入手可能な範囲で製造
上不可避な不純物を含有するもので差支えない。
Ｂ（ホウ素）としては純ボロン又はフエロボロン
を用いることが出来、不可避的に混入してくる不
純物たとえばＡ，Si，Ｃ等を含むものも用いる
ことができる。 本発明の永久磁石材料は磁気的に等方性であ
り、また前記先願（特願昭57−145072）と同様に
Ｒ−Fe−Ｂ三元化合物に基づく結晶質材料であ
る。本発明では、それに基づき焼結体が得られ
る。なお、等方性焼結体は、典型的には溶解鋳造
して成る鋳造合金を粉末化した後成形し焼結する
ことにより得られる。（なお、上記先願において
は、磁界中で配向成形焼結することにより、磁気
異方性焼結体が得られている。） 溶解は真空または不活性ガス雰囲気下で行な
い、鋳造は銅その他金属製等の鋳型を用い、この
場合インゴツト合金の成分偏析を防ぐために水冷
タイプの鋳型などを用いて、冷却速度を早くする
ことが望ましい。十分冷却したのち、スタンプミ
ル等で粗粉砕し、さらにアトライター、ボールミ
ルなどで微粉砕して約400μm以下、好ましくは１
〜100μmとする。 FeBR系合金の微粉砕粉を得る方法としては、
上述した方法の外に、噴霧法などの機械的粉砕法
や還元法、電解法などの物理化学的製粉法なども
用いることができる。 この微粉末合金を、加圧成形し、成形物を約
900〜1200℃、好ましくは1050〜1150℃の温度に
て所定時間焼結する。焼結後の平均結晶粒径が所
定範囲になるように焼結条件（特に温度、時間）
を選択することにより、磁気特性の高い等方性焼
結磁石体を得る。例えば出発原料として100μm以
下の合金粉末を成形し、温度1050〜1150℃におい
て30分〜８時間焼結することにより、好ましい結
晶粒径の焼結体が得られる。 なお、焼結は好ましくは真空又は不活性ガス雰
囲気で行う。また、成形に際しては、カンフア、
パラフイン、レジン、塩化アンモニウム等の結合
剤、ステアリン酸亜鉛、ステアリン酸カルシウ
ム、パラフイン、レジン等の滑剤ないし成形助剤
を用いることができる。 以下本発明を実施例に従つて説明する。但しこ
の実施例は本発明をこれらに限定するものではな
い。 試料として所定組成の永久磁石材料をつぎの工
程により作製した。 (1) Feとして純度99.9％の電解鉄、B19.4％を含
有し残部がFeとＡ，Si，Ｃの不純物からな
るフエロボロン合金、Ｒとして純度99.7％以上
（不純物は主として他の希土類金属）を使用し
所定の原子比になるように配合した後溶解し水
冷銅鋳型にて鋳造。 (2) 粉砕スタンプミルにより35メツシユスルまで
に粗粉砕し次いでボールミルにより３時間微粉
砕（３〜10μm）、 (3) これを成形（1.5t／cm2で加圧）、 (4) 焼結を1000〜1200℃１時間Ar中で結晶粒径
が凡そ５〜30μmの範囲内になるよう行ないそ
の后放冷して試料を得た。 第１表の永久磁石試料は上記の工程により作製
し夫々の磁気特性iHc，Br，（BH）maxを測定
した。第１表には各試料の室温下の磁気特性を記
した。 所定の各成分の範囲内において保磁力iHcは
1kOe以上を示しBrは3kG以上を示した。又
（BH）maxは、2.0MGOeを示して夫々高い磁気
特性を示している。 Ｒとしては２種以上の希土類元素も有用である
ことが判る。さらに、Ｒ量、Ｂ量と磁気特性との
関係を調べるためxNd−8B−Fe系（ｘ＝０〜35
％），15Nd−xB−Fe系（ｘ＝０〜30％）におい
て上記と同様の工程により試料を作製しiHc，Br
を測定し第１図、第２図にその結果を示す。 The present invention relates to isotropic permanent magnet materials. In the present invention, R is used as a symbol representing a rare earth element. Permanent magnet materials are extremely important electrical components used in a wide range of fields, from various household appliances to peripheral equipment for large industrial computers.
It is one of the electronic materials. In addition, with the recent demand for smaller size and higher efficiency of electric and electronic equipment, permanent magnet materials are required to have increasingly higher performance. Among permanent magnets, isotropic magnets are not as good as anisotropic magnets in terms of performance, but they have been widely used because they are not restricted by shape or direction of magnetization. Isotropic permanent magnets are made from almost all conventional magnetic materials. but,
For ferrite, alnico, MnA, and FeCrCo magnets, the energy product (BH) max is at most 2 MGOe, and for SmCo magnets it is 4 to 5 MGOe, which is 1/4 to 1/6 of that for anisotropic magnets. SmCo magnet material is
Sm and Co resources are rare and expensive, making them undesirable as materials for mass-producing magnets. Therefore, it is desired to use resource-rich light rare earths such as Ce, Nd, Pr, etc. in place of Sm, and to use Fe in place of Co. However, it is well known that light rare earths and Fe do not homogeneously melt together and form intermetallic compounds suitable as magnet materials even when cooled and crystallized. Furthermore, attempts to strengthen the magnetic force of such light rare earth-Fe alloys using powder metallurgy were not successful (Japanese Patent Application Laid-Open No. 1983-1999).
210934, see page 6 of the specification). On the other hand, Tokukai Sho
No. 57-210934, it is disclosed that an Fe-R amorphous alloy can be obtained by melt quenching, and
(R as Ce, Pr, Nd, Sm, Eu, etc.), especially Fe-
It has been proposed that a binary Nd alloy be made into an amorphous ribbon by a liquid quenching method, and then magnetized to form a magnet. In this method, (BH)max is 4~
5MGOe can be obtained, but since it is a ribbon with a thickness of several μm to several tens of μm, lamination or pressing after powdering is required to make it into a practical bulk, and either method has a theoretical density of about 60 to 80%. The magnetic properties of the magnet deteriorate further, making it impractical. The present inventors attempted to obtain this Fe-R binary system composition as a sintered body by powder metallurgy, but as shown in No. C1 of Table 1 of this specification, Hc, (BH)
max is almost zero, and the FeR binary sintered body cannot be used as a practical magnetic material. Therefore, the basic object of the present invention is to provide a new isotropic permanent magnet material to replace the above-mentioned conventional isotropic permanent magnet materials, and in particular, it uses Fe and R, which are resource-rich materials. The object of the present invention is to provide an isotropic permanent magnet material having magnetic properties sufficiently high for practical use. That is, the isotropic permanent magnet material of the present invention is magnetically isotropic, consisting of 10 to 25% R, 3 to 23% B, and the remainder substantially Fe in terms of atomic percentage, and is magnetically isotropic and R-Fe-B. Substantially completely crystalline based on ternary compounds, where R is Nd, Pr, Dy, Ho,
At least one type of Tb, especially 50% or more of R is Nd and Pr
one or two types (first invention), or together with these
La, Ce, Pm, Sm, Eu, Gd, Er, Tm, Yb,
At least one of Lu and Y, and 50% or more of R is one or both of Nd and Pr (second invention). The present inventors previously invented a FeBR-based permanent magnet material that does not necessarily require the use of Sm and Co (Japanese Patent Application Laid-Open No. 57-145072). This FeBR-based permanent magnet material is
Based on a new compound different from the conventionally known RCo 5 and R 2 Co 17 compounds, especially boron (B)
is not added as a conventional amorphous promoting element when creating an amorphous alloy or a sintering promoting element in powder metallurgy, but is a magnetic component that constitutes the actual content of this FeBR-based permanent magnet material. It was revealed that it is an essential constituent element of the R-Fe-B compound, which is physically stable and has a high magnetic anisotropy constant. (It has also been revealed that a magnetically anisotropic sintered permanent magnet can be obtained by forming an appropriate microstructure based on the above FeBR-based permanent magnet material.) The present inventors have achieved the above object. As a result of intensive research into isotropic permanent magnet materials,
The present invention was achieved by obtaining the knowledge that a good isotropic permanent magnet material can be obtained using FeBR. The FeBR-based isotropic permanent magnet material obtained by the present invention has properties equal to or better than those of the SmCo-based isotropic magnet material, and is inexpensive because it does not necessarily require the use of rare and expensive Sm or Co. Yes, it is extremely practical. In the present invention, "isotropic" means that it is substantially isotropic, and can be obtained, for example, by molding without applying a magnetic field. In the present invention, the amounts of R and B are limited in consideration of the case of producing an isotropic sintered permanent magnet, which is a typical final product of the permanent magnet material, and this limitation is due to the following reasons (see below). (% indicates atomic percentage ratio unless otherwise specified). Coercive force (iHc) appears at around 7 to 8% and R rises steeply. From then on, as the R amount increases, iHc increases, but Br...
It rises slightly earlier than iHc, but after reaching a maximum value around 10%, it decreases (see Figure 1). Thus, as an isotropic sintered magnet, the R amount that satisfies (BH)max2MGOe or more is 10% or more and 25% or less. Moreover, when R is used in large amounts, it becomes easily flammable and becomes dangerous and difficult to handle. As shown in FIG. 2, coercive force (iHc) appears when a small amount of B is contained, and increases as the content increases. On the other hand, the residual magnetic flux density Br increases once as the content increases, reaches a maximum value, and then decreases. Therefore, as an isotropic sintered magnet, the coercive force
The range for obtaining a maximum energy product of 2 MGOe or more is 3 to 23%. Preferably, one or both of Nd and Pr are the main components of R (Nd and Pr are 50 at% or more in the total R) and 12 to 20
% R, 5 to 18% B, and the balance Fe shows high magnetic properties of (BH)max4MGOe or higher.
The most preferable range is 12 to 16% R, 6 to 18% B, with one or two of Nd and Pr as the main components of R.
With a composition of balance Fe, (BH)max is 7MGOe or more, and high properties never seen before in an isotropic permanent magnet material can be obtained. As R, a light rare earth element which is abundant in resources can be used, and since Sm is not necessarily required or Sm does not need to be the main component, the raw material is inexpensive and extremely useful. The rare earth element R used in the permanent magnet material of the present invention is a rare earth element that includes Y, light rare earth elements, and heavy rare earth elements, and one or more of them is used.
That is, this R includes Nd, Pr, La, Ce, Tb,
Dy, Ho, Er, Eu, Sm, Gd, Pm, Tm, Yb,
Lu and Y are included. As R, a light rare earth element is sufficient, and Nd and Pr are particularly preferable. Also usually R
It is sufficient to have one type of these, but in practice, a mixture of two or more types (mitsushimetal, dididim, etc.) can be used for reasons such as convenience of availability, and Sm, Y,
La, Ce, etc. can be used in combination with other light rare earths such as Nd, Pr, etc. Note that this R does not have to be a pure rare earth element, and may contain impurities that are unavoidable in production within an industrially available range.
As B (boron), pure boron or ferroboron can be used, and those containing unavoidably mixed impurities such as A, Si, C, etc. can also be used. The permanent magnet material of the present invention is magnetically isotropic and is a crystalline material based on the R--Fe--B ternary compound as in the previous application (Japanese Patent Application No. 57-145072). In the present invention, a sintered body is obtained based on this. Note that the isotropic sintered body is typically obtained by pulverizing a cast alloy obtained by melting and casting, followed by shaping and sintering. (In the above-mentioned prior application, a magnetically anisotropic sintered body is obtained by oriented forming and sintering in a magnetic field.) Melting is performed in a vacuum or an inert gas atmosphere, and casting is performed using copper or other materials. It is desirable to use a mold made of metal or the like, and in this case, to speed up the cooling rate, use a water-cooled mold or the like to prevent segregation of the components of the ingot alloy. After cooling sufficiently, coarsely pulverize with a stamp mill, etc., and then finely pulverize with an attritor, ball mill, etc. to about 400 μm or less, preferably 1.
~100μm. The method for obtaining finely pulverized FeBR alloy powder is as follows:
In addition to the above-mentioned methods, mechanical pulverization methods such as a spraying method, physicochemical pulverization methods such as a reduction method, and an electrolytic method can also be used. This fine powder alloy is press-molded to give a molded product of approx.
Sintering is performed at a temperature of 900 to 1200°C, preferably 1050 to 1150°C for a predetermined period of time. Sintering conditions (especially temperature and time) so that the average grain size after sintering is within a specified range
By selecting , an isotropic sintered magnet body with high magnetic properties can be obtained. For example, by molding alloy powder of 100 μm or less as a starting material and sintering it at a temperature of 1050 to 1150° C. for 30 minutes to 8 hours, a sintered body with a preferred crystal grain size can be obtained. Note that sintering is preferably performed in vacuum or in an inert gas atmosphere. In addition, during molding, camphor,
Binders such as paraffin, resin, and ammonium chloride, lubricants and molding aids such as zinc stearate, calcium stearate, paraffin, and resin can be used. The present invention will be explained below based on examples. However, the present invention is not limited to these examples. A permanent magnet material having a predetermined composition was prepared as a sample through the following steps. (1) Electrolytic iron with a purity of 99.9% as Fe, feroboron alloy containing 19.4% of B with the balance being Fe and impurities of A, Si, and C, and a purity of 99.7% or more as R (impurities are mainly other rare earth metals) After blending to the specified atomic ratio, it is melted and cast in a water-cooled copper mold. (2) Coarsely pulverize to 35 mesh using a crushing stamp mill, then finely pulverize (3 to 10 μm) using a ball mill for 3 hours, (3) Form this (pressure at 1.5 t/cm 2 ), (4) Sinter. A sample was obtained by heating at 1000 to 1200° C. for 1 hour in Ar so that the crystal grain size was within the range of approximately 5 to 30 μm, and then cooling the sample. The permanent magnet samples shown in Table 1 were produced by the above steps, and their respective magnetic properties iHc, Br, and (BH)max were measured. Table 1 shows the magnetic properties of each sample at room temperature. Within the range of each predetermined component, the coercive force iHc is
It showed more than 1kOe and Br showed more than 3kG. Furthermore, (BH)max was 2.0MGOe, indicating high magnetic properties. It turns out that two or more kinds of rare earth elements are also useful as R. Furthermore, in order to investigate the relationship between the amount of R, the amount of B, and the magnetic properties, we investigated the xNd-8B-Fe system (x = 0 to 35
%), 15Nd-xB-Fe system (x = 0 to 30%), samples were prepared using the same process as above, and iHc, Br
were measured and the results are shown in Figures 1 and 2.

【表】 本発明のFeBR系等方性永久磁石材料を最も有
効に用いてなる焼結体永久磁石はフエライトや
Ｒ・Co磁石に同様な例が見られる如く、単磁区
とほぼ同等の大きさの粒子からなる磁石であり一
旦粉末にして加圧成形後焼結を経て良好な磁石特
性が得られる。 そこで本発明者等は本発明によるFeBR系等方
性永久磁石材料の焼結後の結晶粒径の大きさと磁
石特性、特にiHcの関係について、一例としてFe
−8B−15Nd系について検討した。その結果を第
３図に示す。 保磁力iHc（kOe）が1kOe以上では平均結晶粒
径は１〜160μm、2kOe以上では１〜110μmであ
り、さらに好ましくは１〜80μm、最も好ましく
は３〜10μmであり、永久磁石とする上で参考と
なる。 本発明の磁石材料を製造するに際し結合剤、滑
剤を加えた造粒粉（数十〜数百μm）として用い
ることも出来る。結合剤、滑剤（一般には数十〜
数百μm）は、異方性磁石材料成形の際には、配
向を妨げるため一般には用いられないが、本発明
では等方性磁石材料のため、結合剤、滑剤等を含
むことによりプレス効率の改善、成形体の強度増
大等が可能である。 本発明によつて得られる等方性永久磁石材料は
好ましい態様において従来の等方性永久磁石材料
のどれよりも高い磁石特性を有ししかもSm，Co
などの希少かつ高価な成分を特に必要としないも
のである。又提案されている非晶質リボンでは得
られない実用的に十分なバルクの永久磁石材料が
得られる上、さらにバルクの等方性永久磁石が粉
末治金法により製造可能である点において、本発
明磁石材料はきわめて有用であり高価値を有する
ものである。 以上詳述の通り本発明のFeBR系等方性永久磁
石材料はＲとして軽希土類（特にNd，Pr等）、
特に各種の軽希土類、重希土類の混合物等の安価
なＲ原料を用いて高い磁気特性の等方性永久磁石
を提供できる。 本発明永久磁石材料は工業的製造上不可避な不
純物の存在を許容できるがさらに以下の展開も可
能であり一層実用性を高めることができる。即ち
Ｒ，Ｂ，Feの他に所定範囲内でＣ，Ｐ，Ｓ，Cu
が含有されることもでき製造上の便宜、低価格化
に資する。Ｃは有機結合剤から、Ｓ，Ｐ，Cu等
は原料、製造工程からも含有されることがある。
C4.0％以下、P3.3％以下、S2.5％以下、Cu3.3％
以下、但しこれらの合計は、各成分のうち最大値
以下では実用可能である。 さらに本発明の磁石材料にＡ，Ti，Ｖ，Cr，
Mn，Ni，Zn，Zr，Nb，Mo，Ta，Ｗ，Sn，
Bi，Sbの一種以上を添加することにより高保磁
力化が可能となりまたNi添加により耐食性改善
も可能となる。いずれも限られた範囲内で使用が
可能である。 以上本発明はFeBR系等方性永久磁石材料であ
り、高残留磁化、高保磁力、高エネルギー積を有
するすぐれた等方性焼結体永久磁石を提供するこ
とを可能としたのもので工業的にきわめて高い価
値をもつものである。[Table] The sintered permanent magnet made by most effectively using the FeBR-based isotropic permanent magnet material of the present invention has a size almost equivalent to that of a single magnetic domain, as seen in similar examples of ferrite and R/Co magnets. It is a magnet made of particles, and good magnetic properties can be obtained by turning it into a powder, press-molding it, and then sintering it. Therefore, the present inventors investigated the relationship between the crystal grain size after sintering of the FeBR-based isotropic permanent magnet material according to the present invention and the magnetic properties, especially iHc.
-8B-15Nd system was investigated. The results are shown in FIG. When the coercive force iHc (kOe) is 1 kOe or more, the average crystal grain size is 1 to 160 μm, and when it is 2 kOe or more, it is 1 to 110 μm, more preferably 1 to 80 μm, and most preferably 3 to 10 μm. Useful for reference. When producing the magnet material of the present invention, it can also be used as granulated powder (several tens to hundreds of micrometers) to which a binder and a lubricant are added. Binder, lubricant (generally several dozen to
(several hundred μm) is generally not used when molding anisotropic magnet materials because it hinders orientation, but in the present invention, since it is an isotropic magnet material, it contains binders, lubricants, etc. to improve press efficiency. It is possible to improve the properties of the molded product and increase the strength of the molded product. In a preferred embodiment, the isotropic permanent magnet material obtained by the present invention has higher magnetic properties than any of the conventional isotropic permanent magnet materials, and
It does not particularly require rare and expensive ingredients such as. Furthermore, the present invention has the advantage that it is possible to obtain a practically sufficient bulk permanent magnet material that cannot be obtained with the proposed amorphous ribbon, and furthermore, a bulk isotropic permanent magnet can be manufactured by powder metallurgy. The invented magnet material is extremely useful and of high value. As detailed above, in the FeBR-based isotropic permanent magnet material of the present invention, R is a light rare earth (particularly Nd, Pr, etc.),
In particular, isotropic permanent magnets with high magnetic properties can be provided using inexpensive R raw materials such as mixtures of various light rare earths and heavy rare earths. Although the permanent magnet material of the present invention can tolerate the presence of impurities that are inevitable in industrial production, the following developments are also possible and the practicality can be further improved. That is, in addition to R, B, and Fe, C, P, S, and Cu are added within a specified range.
can also be included, which contributes to manufacturing convenience and cost reduction. C may be contained from an organic binder, and S, P, Cu, etc. may be contained from raw materials and manufacturing processes.
C4.0% or less, P3.3% or less, S2.5% or less, Cu3.3%
Below, however, these totals are practical if they are less than the maximum value of each component. Furthermore, the magnet material of the present invention includes A, Ti, V, Cr,
Mn, Ni, Zn, Zr, Nb, Mo, Ta, W, Sn,
By adding one or more of Bi and Sb, it is possible to increase the coercive force, and by adding Ni, it is also possible to improve corrosion resistance. Both can be used within a limited range. As described above, the present invention is an isotropic permanent magnet material based on FeBR, which makes it possible to provide an excellent isotropic sintered permanent magnet having high residual magnetization, high coercive force, and high energy product. It has extremely high value.

【図面の簡単な説明】[Brief explanation of drawings]

第１図は、Ｒ（Nd）量とiHc，Brの関係を示す
グラフ、第２図は、Ｂ量とiHc，Brの関係を示す
グラフ、第３図は本発明の一実施例についての平
均結晶粒径分布と保磁力の関係を示すグラフ、第
４図はＡ元素含有量とBrの関係を示すグラフ、
を夫々示す。 Fig. 1 is a graph showing the relationship between the amount of R (Nd) and iHc, Br, Fig. 2 is a graph showing the relationship between the amount of B and iHc, Br, and Fig. 3 is the average for one example of the present invention. A graph showing the relationship between crystal grain size distribution and coercive force, Figure 4 is a graph showing the relationship between A element content and Br,
are shown respectively.

Claims (1)

【特許請求の範囲】 １ 原子百分率で10〜25％のＲ（但しＲはNd，
Pr，Dy，Ho，Tbの少くとも一種）、３〜23％の
Ｂ、及び残部実質的にFeから成り、磁気等方性
であり、かつＲ−Fe−Ｂ三元化合物に基づく実
質的に完全な結晶質であることを特徴とする永久
磁石材料。 ２ Ｒの50％以上がNdとPrの一種又は二種であ
る特許請求の範囲第１項に記載の永久磁石材料。 ３ 原子百分率で10〜25％のＲ（但しＲはNd，
Pr，Dy，Ho，Tbの少くとも一種とLa，Ce，
Pm，Sm，Eu，Gd，Er，Tm，Yb，Lu，Ｙの
少なくとも一種であつて、かつＲの50％以上が
NdとPrの一種又は二種）、３〜23％のＢ、及び
残部実質的にFeから成り、磁気等方性であり、
かつＲ−Fe−Ｂ三元化合物に基づく実質的に完
全な結晶質であることを特徴とする永久磁石材
料。[Scope of Claims] 1 10 to 25% R in atomic percentage (R is Nd,
Pr, Dy, Ho, Tb), 3 to 23% B, and the balance substantially Fe, is magnetically isotropic, and is substantially based on an R-Fe-B ternary compound. A permanent magnetic material characterized by being completely crystalline. 2. The permanent magnet material according to claim 1, wherein 50% or more of R is one or both of Nd and Pr. 3 10 to 25% R in atomic percentage (however, R is Nd,
At least one of Pr, Dy, Ho, Tb and La, Ce,
At least one of Pm, Sm, Eu, Gd, Er, Tm, Yb, Lu, Y, and 50% or more of R
consisting of one or two of Nd and Pr), 3 to 23% B, and the remainder substantially Fe, and is magnetically isotropic;
and a substantially completely crystalline permanent magnetic material based on an R-Fe-B ternary compound.
JP58079096A 1983-05-06 1983-05-06 Isotropic permanent magnet and manufacture thereof Granted JPS59204209A (en)

Priority Applications (8)

Application Number Priority Date Filing Date Title
JP58079096A JPS59204209A (en) 1983-05-06 1983-05-06 Isotropic permanent magnet and manufacture thereof
CA000444488A CA1277159C (en) 1983-05-06 1983-12-30 Isotropic permanent magnets and process for producing same
DE8383113252T DE3380612D1 (en) 1983-05-06 1983-12-30 Isotropic permanent magnets and process for producing same
EP19830113252 EP0124655B1 (en) 1983-05-06 1983-12-30 Isotropic permanent magnets and process for producing same
US06/567,640 US4840684A (en) 1983-05-06 1983-12-30 Isotropic permanent magnets and process for producing same
SG49090A SG49090G (en) 1983-05-06 1990-07-04 Isotropic permanent magnets and process for producing same
HK68390A HK68390A (en) 1983-05-06 1990-08-30 Isotropic permanent magnets and process for producing same
US07/717,002 US5192372A (en) 1983-05-06 1991-06-18 Process for producing isotropic permanent magnets and materials

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
JP58079096A JPS59204209A (en) 1983-05-06 1983-05-06 Isotropic permanent magnet and manufacture thereof

Publications (2)

Publication Number Publication Date
JPS59204209A JPS59204209A (en) 1984-11-19
JPH0467322B2 true JPH0467322B2 (en) 1992-10-28

Family

ID=13680342

Family Applications (1)

Application Number Title Priority Date Filing Date
JP58079096A Granted JPS59204209A (en) 1983-05-06 1983-05-06 Isotropic permanent magnet and manufacture thereof

Country Status (1)

Country Link
JP (1) JPS59204209A (en)

Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS61147503A (en) * 1984-11-30 1986-07-05 Tohoku Metal Ind Ltd Rare earth magnet
CA1273231A (en) * 1984-12-10 1990-08-28 Kalathur S.V.L. Narasimhan Permanent magnet alloy
JPS6338217A (en) * 1986-08-04 1988-02-18 Tohoku Metal Ind Ltd Manufacture of sintered rare earth element magnet
US4829277A (en) * 1986-11-20 1989-05-09 General Motors Corporation Isotropic rare earth-iron field magnets for magnetic resonance imaging
JPS63140605U (en) * 1987-03-05 1988-09-16

Family Cites Families (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS57141901A (en) * 1981-02-26 1982-09-02 Mitsubishi Steel Mfg Co Ltd Permanent magnet powder
US4851058A (en) * 1982-09-03 1989-07-25 General Motors Corporation High energy product rare earth-iron magnet alloys

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Publication number Publication date
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