JPS6031208A - Permanent magnet - Google Patents
Permanent magnetInfo
- Publication number
- JPS6031208A JPS6031208A JP58139678A JP13967883A JPS6031208A JP S6031208 A JPS6031208 A JP S6031208A JP 58139678 A JP58139678 A JP 58139678A JP 13967883 A JP13967883 A JP 13967883A JP S6031208 A JPS6031208 A JP S6031208A
- Authority
- JP
- Japan
- Prior art keywords
- permanent magnet
- atomic
- less
- rare earth
- temperature characteristics
- 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.)
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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
- H01F1/047—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
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- Chemical & Material Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Inorganic Chemistry (AREA)
- Engineering & Computer Science (AREA)
- Power Engineering (AREA)
- Hard Magnetic Materials (AREA)
Abstract
Description
【発明の詳細な説明】
この発明は、Ｒ（ＲはＹを含む希土類元素のうち少なく
とも１種＞、Ｂ、Ｆｅ、ＧＯを主成分とする永久磁石に
係り、主成分たるＦｅまたはＢの一部をＳｉで置換し、
温度特性及び耐酸化性を改善した希土類・鉄・ボロン・
コバル１〜系永久磁石合に関する。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a permanent magnet whose main components are R (R is at least one rare earth element including Y), B, Fe, and GO, and where one of the main components is Fe or B. is replaced with Si,
Rare earth, iron, boron, etc. with improved temperature characteristics and oxidation resistance.
Regarding Kobal 1~ system permanent magnet combination.
永久磁石材料は、一般家庭の各種電気製品から、大型コ
ンピュータの周辺端末機器まで、幅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。近年の電
気・電子機器の小形化、高効率化の要求にともない、永
久磁石材料は益々高性能化がめられるようになった。Permanent magnetic materials are one of the extremely important electrical and electronic materials used in a wide range of fields, from various household appliances to peripheral terminal equipment for large computers. In recent years, with the demand for smaller size and higher efficiency of electrical and electronic equipment, permanent magnet materials are increasingly required to have higher performance.
現在の代表的な永久磁石材料は、アルニコ、ハードフェ
ライトおよび希土類コバル１〜磁石である。Current representative permanent magnet materials are alnico, hard ferrite and rare earth Kobal 1~ magnets.
近年のコバルトの原料事情の不安定化に伴ない、コバル
１〜を２０〜３０ｗｔ％含むアルニ」磁石の需要は減り
、鉄の酸化物を主成分とする安価なハードフェライトが
磁石材料の主流を占めるにうになった。As the raw material situation for cobalt has become unstable in recent years, the demand for aluminum magnets containing 20 to 30 wt% of cobal 1 has decreased, and cheap hard ferrite, which is mainly composed of iron oxides, has become the mainstream magnet material. It became more common.
一方、希土類コバル１−磁石はコバル［へを５０〜ｅｏ
ｗｔ％も含むうえ、希土類鉱石中にあまり含まれていな
いＳｍを使用するため大変高価であるが、他の磁石に比
べて、磁気特性が格段に高いため、主として小型で付加
価値の高い磁気回路に多用されるにうになった。On the other hand, the rare earth Kobal 1 magnet is Kobal [to 50~eo
Although it is very expensive because it uses Sm, which is not included in rare earth ores, it has much higher magnetic properties than other magnets, so it is mainly used in small and high value-added magnetic circuits. Now it is often used in
そこで、本発明者は先に、高価’ｃ’ｊ ＳｍやωをＣ
右しない新しい高性能永久磁石どしてＦｅ−ＢＲ系（Ｒ
はＹを含む希土類元素のうち少なくとも１種）永久磁石
を提案した（特願昭５７−１４５０７２号）。この永久
磁石は、Ｒとして陶やＰｒを中心どする資源的に豊富な
軽希土類を用い、Ｆｅを主成分として２５Ｍ Ｇ Ｏｅ
以上の極めて高いエネルギー積を示すすぐれた永久磁石
である。Therefore, the inventor first changed the expensive 'c'j Sm and ω to C
Fe-BR series (R
proposed a permanent magnet containing at least one rare earth element containing Y (Japanese Patent Application No. 57-145072). This permanent magnet uses light rare earths, which are rich in resources, mainly ceramics and Pr, as R, and has Fe as the main component, and is 25M G Oe.
This is an excellent permanent magnet that exhibits an extremely high energy product.
また、さらに、上記のすぐれた磁気特性を有するＦｅ−
ＢＲ元系磁気異方焼結体からなる永久磁石の温度特性を
改善するため、Ｆｅの一部を６で置換することにＪこり
、生成台金のキュリ一点を上昇させて温度特性を改善し
たＦｅ−ＢＣｏＲ系異方性焼結体からなる永久磁石を提
案したく 特願昭５７−１６６６６３号）。この永久磁
石により、高温度の環境下での使用が可能となった。Furthermore, Fe-
In order to improve the temperature characteristics of a permanent magnet made of a BR element-based magnetic anisotropic sintered body, we decided to replace a part of Fe with 6, and raised the Curie point of the generated base metal by one point to improve the temperature characteristics. We would like to propose a permanent magnet made of an anisotropic sintered body of Fe-BCoR system (Japanese Patent Application No. 166663/1982). This permanent magnet allows use in high-temperature environments.
しかし、今日、磁石の用途は拡がる一方であり、苛酷な
環境下での使用に耐え得る永久磁石が強く要望されてい
る。また、この苛酷な環境どは、高温多湿の環境であり
、すぐれた温度特性と共に高い耐食性を有する永久磁石
材料が必要となる。However, today, the uses of magnets are expanding, and there is a strong demand for permanent magnets that can withstand use in harsh environments. Moreover, this harsh environment is a high temperature and humid environment, and a permanent magnet material that has excellent temperature characteristics and high corrosion resistance is required.
この発明は、希土類・ボロン・鉄を主成分とする新規な
永久磁石の温度特性と共に耐酸化性を改善した希土類・
ボロン・鉄を主成分とする永久磁石を目的としている。This invention is a new permanent magnet mainly composed of rare earth elements, boron, and iron, which has improved temperature characteristics and oxidation resistance.
It is aimed at permanent magnets whose main components are boron and iron.
すなわち、この発明は、Ｒ（但しＲはＹを含む希土類元
素のうち少なくとも１種） ８原子％〜３０原子％、Ｂ
２原子％〜２８原子％、ＣＯ５０原子％以下、５ｉ１
５原子％以下、残部Ｆｅ及び不可避的不純物からなり、
主相が正方品とする焼結体であることを特徴りる永久磁
石である。That is, this invention provides R (where R is at least one kind of rare earth elements including Y) 8 at % to 30 at %, B
2 atomic% to 28 atomic%, CO50 atomic% or less, 5i1
5 at % or less, the remainder consisting of Fe and unavoidable impurities,
A permanent magnet characterized by being a sintered body whose main phase is a square one.
永久磁石材料におけるキュリ一点の増大は、磁気特性の
温度変化の減少のための最も重要な要因とされており、
上述したＲ−Ｂ−Ｆｅ系永久磁石のキュリ一点は、希土
類含有される希土類元素によって変化し、ちなみに、ｔ
！１−Ｂ−Ｆｅ系で約３１０℃、ω−日日−ｅ系で約３
７０℃であった。この発明では、主成分たるＦｓの一部
を０で置換覆ることにより、生成合金のキュリ一点を上
テｒさけ、残留磁束密度の温度特性を改善し、さらに、
ＦｅまたはＢの一部をＳＬで置換することにより、生成
合金のキュリ一点を上昇させ、残留磁束密度の温度特性
を改善づると共に、さらに、磁気回路に組立だ揚台の永
久磁石の錆発生は磁気回路の出ノＪ低下を招来するため
、永久磁石の耐酸化性の改善をＬ）つたちのであＲＢＣ
ｏ−Ｆｅ系永久ＩｔｉＥｉにおいて、このＳＬの置換間
の増大に伴ない、耐食性が向上し、さらに、生成合金の
キュリ一点が上昇し、残留磁束密度の温度特性が改善さ
れ、かつ、希土類元素９種類を問わず有効である。The increase in the Curie point in permanent magnet materials is considered the most important factor for reducing temperature changes in magnetic properties.
The Curie point of the above-mentioned R-B-Fe permanent magnet changes depending on the rare earth element contained, and by the way, t
! About 310℃ for 1-B-Fe system, about 3 for ω-day day-e system
The temperature was 70°C. In this invention, by substituting and covering a part of Fs, which is the main component, with 0, the Curie point of the produced alloy is avoided, the temperature characteristics of the residual magnetic flux density are improved, and further,
By substituting a part of Fe or B with SL, the Curie point of the resulting alloy is raised by a single point, improving the temperature characteristics of the residual magnetic flux density, and furthermore, rusting of the permanent magnet of the lifting platform assembled in the magnetic circuit is reduced. In order to reduce the output J of the magnetic circuit, it is necessary to improve the oxidation resistance of the permanent magnet.
In the o-Fe-based permanent ItiEi, as the SL substitution period increases, the corrosion resistance improves, the Curie point of the resulting alloy increases, the temperature characteristics of the residual magnetic flux density improves, and the rare earth element 9 Valid regardless of type.
従って、この発明の永久磁石は、Ｒとして陶や円を中心
とする資源的に豊富な軽希土類を主に用い、Ｆｅ 、Ｂ
、 Ｒ，Ｃｏ、 ＳＬを主成分とすることにより、２５
ＭＧＯｅ以上の極めて高いエネルギー積並びに、高残留
磁束密度、高保持力を有し、かつすぐれた残留磁束密度
の温度特性を示Ｊとともに高い耐酸化性を有づる、すぐ
れた永久磁石を安価に得ることができる。Therefore, the permanent magnet of the present invention mainly uses resource-rich light rare earths such as ceramics and circles as R, and Fe, B
, R, Co, and SL as the main components, 25
To obtain an excellent permanent magnet at a low cost, which has an extremely high energy product exceeding MGOe, a high residual magnetic flux density, a high coercive force, and exhibits excellent temperature characteristics of the residual magnetic flux density, and has high oxidation resistance as well as J. be able to.
また、ＳＬは、安価な低１［ｉ度「ｅまたはフェロボロ
ン中に多量に含有されており、これら不純物の多い安価
な原料を使用することにより、不純物としてＳＬが含有
されるが、この原料合金中の５ｉｔｉを調整することに
にす、湿度特性のすぐれた高性能永久磁石が安価に得ら
れる。In addition, SL is contained in a large amount in inexpensive low 1 degree "e" or ferroboron, and by using cheap raw materials with many of these impurities, SL is contained as an impurity, but this raw material alloy By adjusting the 5iti inside, a high-performance permanent magnet with excellent humidity characteristics can be obtained at a low cost.
以下に、この発明による永久磁石の組成限定理由を説明
する。The reasons for limiting the composition of the permanent magnet according to the present invention will be explained below.
この発明の永久磁石に用いる希土類元素Ｒは、イン１−
リウム（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、これらのうち少なくとも１種、好ま
しくはＮｄ、ｐｒ等の軽希土類を主体として、あるいは
Ｎｄ、ｌ）ｒ等との混合物を用いる。すなわち、Ｒとし
ては、
ネオジム（Ｎｄ）、プラセオジム（Ｐｒ）。The rare earth element R used in the permanent magnet of this invention is
Rare earth elements including lithium (Y), light rare earths and heavy rare earths, at least one of these, preferably light rare earths such as Nd and pr, or a mixture with Nd, l)r, etc. Use. That is, R includes neodymium (Nd) and praseodymium (Pr).
ランタン（Ｌａ）、セリウム（Ｃｅ）。Lanthanum (La), cerium (Ce).
テルビウム（Ｔｂ＞、ジスプロシウム（Ｄｙ）。Terbium (Tb>, dysprosium (Dy).
ホルミウム（１１０）、エルビウム（Ｅｒ）。Holmium (110), erbium (Er).
ユウロピウム（ＥＵ）、サマリウム（Ｓｍ）。Europium (EU), samarium (Sm).
カドリニウム（Ｇｄ）、プロメチウム（Ｐｍ）。Cadolinium (Gd), promethium (Pm).
ツリウム（Ｔｍ）、イッテルビウム（Ｙｂ）。Thulium (Tm), Ytterbium (Yb).
ルテチウム（Ｌｕ）、イソ１〜リウム（Ｙ）が包含され
る。Included are lutetium (Lu) and iso1-lium (Y).
又、通例Ｒのうち１種をもって足りるが、実用上は２種
以上の混合物（ミツシュメタル、ジジム等）を入手上の
便宜等の理由により用いることができ、Ｓｍ、Ｙ、Ｌａ
、Ｃｅ、Ｇｄ等は他のＲ１特にＮｄ、ｐｒ等との混合物
として用いることができる。In addition, it is usually sufficient to use one type of R, but in practice, a mixture of two or more types (Mitushmetal, didymium, etc.) can be used for reasons such as convenience of availability, and Sm, Y, La
, Ce, Gd, etc. can be used as a mixture with other R1, especially Nd, pr, etc.
なお、この［では純希土類元索でなくてもよく、工業上
入手可能な範囲で製造上不可避な不純物を含有づ−るも
のでも差支えない。Note that this does not necessarily have to be a pure rare earth element, and may contain impurities that are unavoidable in production within an industrially available range.
Ｒ（Ｙを含む希土類元素のうち少なくとも１種）は、新
規な上記系永久磁石におりる必須元素であって、８原子
％未満では、高磁気特性、特に保磁力１ｋＯｅ以上が冑
られず、３ｏ原子％を越えると、残留磁束密度（Ｂｒ
）が低下して、すぐれた特性の永久磁石が得られず、工
業生産上取扱・製造が困難となる。よっＣ１希土類元素
は、８原子％〜３゜原子％の範囲とする。R (at least one rare earth element including Y) is an essential element in the new above-mentioned permanent magnet, and if it is less than 8 atomic %, high magnetic properties, especially coercive force of 1 kOe or more, will not be improved. When it exceeds 3o at%, the residual magnetic flux density (Br
) decreases, making it impossible to obtain a permanent magnet with excellent characteristics, and making it difficult to handle and manufacture in industrial production. Therefore, the C1 rare earth element should be in the range of 8 atomic % to 3° atomic %.
Ｂは、新規な上記系永久磁石における必須元素であって
、２原子％未満では、保磁力（１ｌ−１Ｇ ）１に０８
以上は得られず、２８原子％を越えるど、残留磁束密度
（Ｂｒ ）が低下し、４ＫＧ未満となるため、Ｊぐれた
永久磁石が得られない。よって、Ｂは、２原子％・−２
８原子％の範囲とづる。B is an essential element in the new above-mentioned permanent magnet, and at less than 2 atomic %, B has a coercive force (1l-1G) of 0.8
However, as the residual magnetic flux density (Br 2 ) exceeds 28 at %, the residual magnetic flux density (Br 2 ) decreases to less than 4 KG, making it impossible to obtain a permanent magnet with J deviation. Therefore, B is 2 atomic %・-2
Spelled out as a range of 8 atomic percent.
ＣＯは、Ｆｅの一部と置換Ｊ°ることにより、生成合金
のキュリ一点を上昇さぜる効果を有するが、保磁力ｉＨ
ｃは６置換により減少づる傾向にあり、ら置換量ととも
に保磁力の低下が箸しく、永久磁石祠料として必要な保
磁力１ｋＯｅ以上を１ｉノるために、Ｃｏ量は５０原子
％以下とする。CO has the effect of raising the Curie point of the produced alloy by substituting a part of Fe, but the coercive force iH
C tends to decrease with 6 substitutions, and the coercive force decreases with the amount of 6 substitutions.In order to maintain the coercive force of 1 kOe or more required as a permanent magnet abrasive, the amount of Co is set to 50 atomic % or less. .
Ｓｌは、水系永久磁石の温度特性を改善Ｊるため、Ｂま
たはＦｅの一部を置換するもので、置換量の増大に伴な
い生成合金のキュリ一点を上昇「しめるが、１５原子％
を越えるど、保磁力がＩＫＯθ未満となり、実用磁石と
して不適であるので、１５１Ｍ子％以下とする。また、
高い磁気特性を有する永久１石を得るには、１０原子％
以下のＳＬが望ましく、好ましい組成範囲の永久磁石の
保磁ツノは４．５ＫＯｅ以上、最大エネルギー積は１９
ＭＧＯｅ以上となる。Sl replaces a part of B or Fe in order to improve the temperature characteristics of water-based permanent magnets, and as the amount of substitution increases, the temperature of the produced alloy increases by one point, but it decreases by 15 atomic %.
If it exceeds IKOθ, the coercive force becomes less than IKOθ, making it unsuitable for use as a practical magnet. Also,
To obtain a permanent stone with high magnetic properties, 10 atom%
The following SL is desirable, and the coercive horn of the permanent magnet in the preferred composition range is 4.5 KOe or more, and the maximum energy product is 19
It will be more than MGOe.
［ｅは、新規な上記系永久磁石にお（プる必須元素であ
り、上記成分を含有した残余を占める。しかし、６５原
子％未満では残留磁束密度（Ｂｒ ）が低下い８２原子
％を越えると、高い保磁力が得られないので、Ｆｅは６
５原子％〜８２原子％が望ましい。[e is an essential element for the new above-mentioned permanent magnet, and occupies the remainder containing the above components.However, if it is less than 65 at%, the residual magnetic flux density (Br) decreases and if it exceeds 82 at%. Since high coercive force cannot be obtained, Fe is 6
5 atomic % to 82 atomic % is desirable.
この発明において、高い残留磁束密度と高い保磁力を共
に有するすぐれた永久磁石を得るためには、［＜１０原
子％〜２５原子％、Ｂ４原子％〜２Ｇ原子％、Ｇｏ ３
原子％〜４５原子％、３ｔ １０原子％以下、Ｆｅ ６
８原子％・−８０原子％が好ましい。In this invention, in order to obtain an excellent permanent magnet having both a high residual magnetic flux density and a high coercive force, [<10 at% to 25 at%, B4 at% to 2G at%, Go3
atomic% to 45 atomic%, 3t 10 atomic% or less, Fe 6
8 atomic % and −80 atomic % are preferable.
また、この発明による永久磁石は、 Ｒ，［３゜Ｆｅの
他、工業的生産上不可避的不純物の存在を許容できるが
、Ｂの 一部を４．０原子％以下のＣ１３，５原子％の
Ｐ、２．５原子％以上のＳ、３．５％以下のＣＯのうら
少なくとも１種、合８１量で４．０原子％以下で置換°
りることにより、永久磁石の製造性改善、低価格化が可
能である。In addition, the permanent magnet according to the present invention can tolerate the presence of unavoidable impurities in industrial production in addition to R and [3°Fe, but a portion of B is replaced with 4.0 at% or less of C13.5 at%. At least one of P, S of 2.5 atomic % or more, and CO of 3.5 atomic % or less, in a total amount of 81% or less, substituted with 4.0 atomic % or less
By doing so, it is possible to improve the manufacturability and reduce the cost of permanent magnets.
ざらに、Ｒ、Ｂ、Ｃｏ 、Ｓｉ 、Ｆｅ系に、９．５原
子％以上のへ交、４．５原子％以下の１−１１９．５原
子％以下のＶ、８．５原子％以下のＱｒ１８．０原子％
以下のＭｎ、５原子％以下のＢ１１１２．５原子％以下
のＮｂ 、 １０．５原子％以下のＴａ、９．５原子％
以下のＭｏ ｓ ９．５原子％以下のＷ、２．５原子％
以下のＳｂ、７原子％以下のＧｅ、３５原子％以下のＳ
ｎ、５．５原子％以上のＺｒ、５．５原子％以下のＨ１
’のうち少なくとも１種を添加含有、但し、２種以上含
有乃る場合は、その最大含有量は当該添加元素のうち最
大値を有するものの原子百分比％以下の含有さμること
により、永久磁石の高保磁力化が可能になる。Roughly, in the R, B, Co, Si, and Fe systems, 9.5 atom% or more of hexagonal, 4.5 atom% or less of 1-119.5 atom% of V, and 8.5 atom% or less of Qr18.0 atomic%
The following Mn, 5 at% or less B11 2.5 at% or less Nb, 10.5 at% or less Ta, 9.5 at%
Mos: 9.5 at% or less W, 2.5 at%
Sb below, Ge below 7 atomic%, S below 35 atomic%
n, 5.5 at% or more Zr, 5.5 at% or less H1
However, if two or more of the following are added, the maximum content is less than the atomic percentage of the one with the maximum value among the added elements, and the permanent magnet is It becomes possible to increase the coercive force of
結晶相は主相が正方晶であることが、微細で均一な合金
粉末より、すぐれた磁気特性を有づる焼結永久磁石を作
製するのに不可欠である。It is essential that the main crystalline phase be tetragonal in order to produce a sintered permanent magnet with superior magnetic properties than a fine and uniform alloy powder.
また、製造に際して、磁場中プレス成型覆ることにより
磁気的異方性磁石が得られ、無磁界中でプレス成型する
ことにより、磁気的等方性磁石を得ることができる。Furthermore, during production, a magnetically anisotropic magnet can be obtained by press-molding in a magnetic field, and a magnetically isotropic magnet can be obtained by press-molding in a non-magnetic field.
この発明による永久磁石は、保磁）Ｊ＋１−１ｃ≧１Ｋ
Ｏｓ、残留磁束密度３ｒ＞４）（Ｑ、を示し、最大エ
ネルギー積（ＢＨ）ｍａｘはハードフェライトど同等以
上となり、最も好ましい組成範囲では、（ＢＨ）ｍａｘ
≧１０ＭＧＯｅを示し、最大値は２５ＭＧＯθ以上に達
する。The permanent magnet according to the present invention has a coercivity J+1-1c≧1K
Os, residual magnetic flux density 3r>4) (Q), the maximum energy product (BH) max is equal to or higher than that of hard ferrite, and in the most preferable composition range, (BH) max
It shows ≧10MGOe, and the maximum value reaches 25MGOθ or more.
また、この発明永久磁石のＲの主成分がその５０％以上
を軽希土類金属が占める場合で、［＜１２原子％〜２０
原子％、Ｂ４４原子〜２４原子％、Ｃｏ３原子％〜４５
原子％、Ｆｅ ６５原子％〜８２原子％、５Ｌ１０原子
％以下含有するとき最もずぐれた磁気特性を示し、特に
軽希土類金属が陶の場合には、（Ｂ ｌ−１）ｍａｘは
その最大値が３３ＭＧＯｓ以上に達する。Further, in the case where the main component of R of the permanent magnet of this invention is light rare earth metal for 50% or more, [<12 atomic % to 20
atomic%, B44 atomic% to 24 atomic%, Co3 atomic% to 45 atomic%
%, Fe 65 atomic % to 82 atomic %, 5L exhibits the most outstanding magnetic properties when it contains 10 atomic % or less, and especially when the light rare earth metal is ceramic, (B l-1) max is its maximum value. reaches more than 33 MGOs.
以下に、この発明による実施例を示しその効果を明らか
にする。Examples according to the present invention will be shown below to clarify its effects.
実施例１
出発原料として、純度９９．９％の電解鉄、８１９．４
％を含有し残部はＦｅ及び／Ｖ、ＳＬ、Ｃ等の不純物か
らなるフエ［１ボロン合金、純度９９．７％以上の陶、
純度９９．９％の電解ら、純度９９．９％のＳＬを使用
し、これらを高周波溶解し、その後水冷銅鋳型に鋳造し
た。Example 1 As a starting material, electrolytic iron with a purity of 99.9%, 819.4
%, with the remainder consisting of Fe and impurities such as /V, SL, and C.
Electrolysis with a purity of 99.9% and SL with a purity of 99.9% were used, which were subjected to high frequency melting, and then cast into a water-cooled copper mold.
その後インゴットを、スタンプミルにより３５メツシユ
スルーまでに粗粉砕し、次にボールミルにより３時間粉
砕し、粒度３〜１０加の微粉末を得た。Thereafter, the ingot was coarsely ground with a stamp mill to a throughput of 35 meshes, and then ground with a ball mill for 3 hours to obtain a fine powder with a particle size of 3 to 10 mm.
この微粉末を金型に挿入し、１０ＫＯｅの磁界中で配向
し、２ ｔＪの圧力で成形した。This fine powder was inserted into a mold, oriented in a magnetic field of 10 KOe, and molded at a pressure of 2 tJ.
得られた成形体を、１０００℃〜１２００℃、１〜４時
間、 Ａｒ中、の条件で焼結し、その後放冷し、この発
明による永久磁石を作製した。The obtained molded body was sintered under the conditions of 1000° C. to 1200° C. for 1 to 4 hours in Ar, and then allowed to cool to produce a permanent magnet according to the present invention.
このとき、基本成分組成を、１５Ｋ −８Ｅｌ −１０
Ｃ。At this time, the basic component composition is 15K -8El -10
C.
−５７Ｆｅとし、Ｆｅの一部をＳＬで置換し、５Ｌｆｆ
ｌを種々変化させた各種永久磁石〔１５Ｍ−８１３−１
０Ｃｏ−（５７−Ｘ ） Ｆｅ Ｘ Ｓｖ）のキュリ一
温度を調べた。-57Fe, part of Fe is replaced with SL, 5Lff
Various permanent magnets with various changes in l [15M-813-1
The Curie temperature of 0Co-(57-X)FeXSv) was investigated.
結果は第１図に示す。The results are shown in Figure 1.
キュリ一温度の測定は、焼結体から ３．５＋ｎ＋ｎＸ
３ 、５ ｍｍ Ｘ １ ｍｍ寸法に切り出し、１０
Ｋ Ｏｅの磁場を印加し、２５℃〜５００℃の温度範囲
で、１７ｒｌの温度変化を測定し、４πＩがほぼＯとな
る湿度とした。The Curie temperature is measured from a sintered body at 3.5+n+nX
3.Cut out to 5 mm x 1 mm dimensions, 10
A magnetic field of K Oe was applied, and a temperature change of 17 rl was measured in a temperature range of 25° C. to 500° C., and the humidity was set such that 4πI was approximately O.
第１図の結果から明らかなように、ＳＬ量の増加に伴な
って、キュリ一点が上昇して磁気特性の温度変化の改善
に有効なことがわかる。As is clear from the results in FIG. 1, as the SL amount increases, the Curie point increases, indicating that it is effective in improving temperature changes in magnetic properties.
実施例２
出発原料として、純度９９．９％の電解鉄、Ｅ１１９．
４％を含有し残部はＦｅ及びＡ３５５Ｃ等の不純物から
なるフェロボロン合金、純度！１９．７％以上のＭ１純
度９９．９％の電解Ｇ１純度９９．９％のＳＬを使用し
、これらを高周波溶解し、その後水冷銅鋳型に鋳造した
。Example 2 As a starting material, electrolytic iron with a purity of 99.9%, E119.
Ferroboron alloy containing 4% and the remainder consisting of impurities such as Fe and A355C, purity! Electrolysis with M1 purity of 99.9% and SL with G1 purity of 99.9% over 19.7% were used, which were high frequency melted and then cast into water-cooled copper molds.
その後インボッ１−を、スタンプミルにより３５メツシ
ユスルーまでに粗粉砕し、次にボールミルにより３時間
粉砕し、粒度３〜１０庫の微Ｖ）末を得た。Thereafter, the Inboru 1- was coarsely pulverized with a stamp mill to 35 mesh throughput, and then pulverized with a ball mill for 3 hours to obtain a fine V) powder with a particle size of 3 to 10.
この微粉末を金型に挿入し、１０ＫＯｅの磁界中で配向
し、２ ｔＪの圧力で成形した。This fine powder was inserted into a mold, oriented in a magnetic field of 10 KOe, and molded at a pressure of 2 tJ.
得られた成形体を、１０００℃・〜１２００℃、１〜４
時間、 Ａｒ中、の条件で焼結し、その後放冷し、この
発明による永久磁石を作製した。The obtained molded body was heated at 1000°C to 1200°C for 1 to 4
A permanent magnet according to the present invention was produced by sintering the magnet in Ar for 2 hours, and then allowing it to cool.
上記の製造に際して、基本成分組成を、１７！Ｎ−９Ｅ
ｔ −５Ｃｏ ６９Ｆｅとし、「θの一部をＳ＝で置換
し、５ｉｊｆｉヲ種々変化させた各種永久！！石（１７
Ｎｄ−９Ｂ−５Ｃｏ −（６９−Ｘ ） Ｆｅ−Ｘ Ｓ
Ｌ）の耐酸化性並びにキュリ一温度を調べた。キュリ一
温度の測定は実施例１と同方法で測定し、ｋ４酸化性の
試験は、１法１０ ｍｍ Ｘ １０ ｍｍ Ｘ １５
ｍｍの直方体試料を用い、湿度８０％含有人気中で６０
℃で２４時間保持した後、各試料の単位面積当りの重量
増加で評価した。結果は第１表に示すように、ＳＬ量の
増加にともない耐酸化性が著しく改善されており、また
、＝１コリ一点も上昇していることが明らかである。When producing the above, the basic component composition is 17! N-9E
t-5Co 69Fe, various permanent stones (17
Nd-9B-5Co-(69-X)Fe-XS
The oxidation resistance and Curie temperature of L) were investigated. The Curie temperature was measured in the same manner as in Example 1, and the k4 oxidation test was conducted using one method: 10 mm x 10 mm x 15
Using a rectangular parallelepiped sample with a diameter of 60 mm, the humidity was 80%.
After being maintained at ℃ for 24 hours, each sample was evaluated by weight increase per unit area. The results are shown in Table 1, and it is clear that as the SL amount increases, the oxidation resistance is significantly improved, and also increases by 1 point.
実施例３
出発原料として、純度９９．９％の電解鉄、Ｅ１１９．
４％を含有し残部はＦｅ及び＃、ＳＬ、Ｃ等の不純物か
らなるフェロボロン合金、純度９９．７％以上の陶、純
度９９．９％の電解ら、純度９９．９％のＳしを使用し
、第２表の成分組成となるように配合し、これらを高周
波溶解し、その後水冷銅鋳型に鋳造した。Example 3 As a starting material, electrolytic iron with a purity of 99.9%, E119.
A ferroboron alloy containing 4% and the remainder is Fe and impurities such as #, SL, and C, ceramic with a purity of 99.7% or more, electrolytic material with a purity of 99.9%, and sulfur with a purity of 99.9% are used. They were blended to have the composition shown in Table 2, subjected to high frequency melting, and then cast into a water-cooled copper mold.
その後インゴットを、スタンプミルににす３５メツシユ
スルーまでに粗粉砕し、次にボールミルにより３時間粉
砕し、粒度３・〜１０ＡＩＩ１１の微’Ｆｔ）末を得た
。Thereafter, the ingot was coarsely ground in a stamp mill to a throughput of 35 meshes, and then ground in a ball mill for 3 hours to obtain a fine 'Ft) powder with a particle size of 3.about.10 AII11.
この微粉末を金型に挿入し、１０ Ｋ Ｏｓの磁界中で
配向し、２ ｔ、７の圧力で成形した。This fine powder was inserted into a mold, oriented in a magnetic field of 10 K Os, and molded at a pressure of 2 t and 7 t.
得られた成形体を、１０００℃〜１２００’Ｃ，１〜４
詩閤、 Ａｒ中、の条件で焼結し、その後放冷し、この
発明による永久磁石を作製した３゜
また、比較のため、Ｓ（を添加しないＲ−Ｂ−Ｃ。The obtained molded body was heated at 1000°C to 1200'C, 1 to 4
Permanent magnets according to the present invention were produced by sintering under the following conditions in Ar and then allowed to cool.Also, for comparison, R-B-C without S(S) was added.
−Ｆｅ系永久磁石も同製法で作製した。-Fe-based permanent magnets were also produced using the same manufacturing method.
得られた永久磁石の磁気時ｆ！ｌ並びにキュリー温度を
測定した。測定結果を第３表に示ず。The magnetic time of the obtained permanent magnet is f! l as well as the Curie temperature were measured. Measurement results are not shown in Table 3.
第２表から明らかなように、高い最大エネルギー積を有
し、キュリ一点が改善され温度特性のりぐれた永久磁石
が得られたことがわかる。As is clear from Table 2, a permanent magnet with a high maximum energy product, an improved Curie point, and excellent temperature characteristics was obtained.
以下余白 第１表 第２表 以下余白Below margin Table 1 Table 2 Below margin
第１図は５Ｌｆ７ｉとキュリ一温度との関係を示すグラ
フである。
出願人 住友特殊金属株式会社FIG. 1 is a graph showing the relationship between 5Lf7i and Curie temperature. Applicant: Sumitomo Special Metals Co., Ltd.
Claims (1)
種）８原子％〜３０原子％、Ｂ ２原子％・−２８原子
％、Ｃ０５０原子％以下、３ｉ１５原子％以下、残部［
ｅ及び不可避的不純物からなり、主相が正方晶どづる焼
結体であることを特徴する永久磁石。1R (where R is at least one rare earth element including Y)
Species) 8 at% to 30 at%, B 2 at% -28 at%, C050 at% or less, 3i15 at% or less, balance [
1. A permanent magnet characterized in that the main phase is a sintered body of tetragonal crystals.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP58139678A JP2610798B2 (en) | 1983-07-29 | 1983-07-29 | Permanent magnet material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP58139678A JP2610798B2 (en) | 1983-07-29 | 1983-07-29 | Permanent magnet material |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS6031208A true JPS6031208A (en) | 1985-02-18 |
| JP2610798B2 JP2610798B2 (en) | 1997-05-14 |
Family
ID=15250870
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP58139678A Expired - Lifetime JP2610798B2 (en) | 1983-07-29 | 1983-07-29 | Permanent magnet material |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2610798B2 (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS62174905A (en) * | 1985-10-25 | 1987-07-31 | Toshiba Corp | Permanent magnet |
| US5110377A (en) * | 1984-02-28 | 1992-05-05 | Sumitomo Special Metals Co., Ltd. | Process for producing permanent magnets and products thereof |
| US5135584A (en) * | 1990-09-20 | 1992-08-04 | Mitsubishi Steel Mfg. Co., Ltd. | Permanent magnet powders |
| CN1058579C (en) * | 1989-03-22 | 2000-11-15 | 住友特殊金属株式会社 | Method of manufacturing permanent magnet |
| CN106992051A (en) * | 2017-03-09 | 2017-07-28 | 京磁材料科技股份有限公司 | The preparation method of Sintered NdFeB magnet |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP3997413B2 (en) | 2002-11-14 | 2007-10-24 | 信越化学工業株式会社 | R-Fe-B sintered magnet and method for producing the same |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS57141901A (en) * | 1981-02-26 | 1982-09-02 | Mitsubishi Steel Mfg Co Ltd | Permanent magnet powder |
| JPS59222564A (en) * | 1983-05-31 | 1984-12-14 | Sumitomo Special Metals Co Ltd | Rare earth-ferrous magnetic material and permanent magnet |
| JPH0617200A (en) * | 1992-10-19 | 1994-01-25 | Sumitomo Special Metals Co Ltd | Tetragonal rare earth element-iron-boron type compound |
-
1983
- 1983-07-29 JP JP58139678A patent/JP2610798B2/en not_active Expired - Lifetime
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS57141901A (en) * | 1981-02-26 | 1982-09-02 | Mitsubishi Steel Mfg Co Ltd | Permanent magnet powder |
| JPS59222564A (en) * | 1983-05-31 | 1984-12-14 | Sumitomo Special Metals Co Ltd | Rare earth-ferrous magnetic material and permanent magnet |
| JPH0617200A (en) * | 1992-10-19 | 1994-01-25 | Sumitomo Special Metals Co Ltd | Tetragonal rare earth element-iron-boron type compound |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5110377A (en) * | 1984-02-28 | 1992-05-05 | Sumitomo Special Metals Co., Ltd. | Process for producing permanent magnets and products thereof |
| JPS62174905A (en) * | 1985-10-25 | 1987-07-31 | Toshiba Corp | Permanent magnet |
| CN1058579C (en) * | 1989-03-22 | 2000-11-15 | 住友特殊金属株式会社 | Method of manufacturing permanent magnet |
| US5135584A (en) * | 1990-09-20 | 1992-08-04 | Mitsubishi Steel Mfg. Co., Ltd. | Permanent magnet powders |
| CN106992051A (en) * | 2017-03-09 | 2017-07-28 | 京磁材料科技股份有限公司 | The preparation method of Sintered NdFeB magnet |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2610798B2 (en) | 1997-05-14 |
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