JPS63248102A - Rare earth permanent magnet - Google Patents
Rare earth permanent magnetInfo
- Publication number
- JPS63248102A JPS63248102A JP62082398A JP8239887A JPS63248102A JP S63248102 A JPS63248102 A JP S63248102A JP 62082398 A JP62082398 A JP 62082398A JP 8239887 A JP8239887 A JP 8239887A JP S63248102 A JPS63248102 A JP S63248102A
- Authority
- JP
- Japan
- Prior art keywords
- magnet
- rare earth
- compound
- permanent magnet
- tetragonal
- 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 18
- 150000002910 rare earth metals Chemical class 0.000 title claims description 10
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 8
- 229910052735 hafnium Inorganic materials 0.000 claims abstract description 6
- 150000001875 compounds Chemical class 0.000 abstract description 13
- 230000005415 magnetization Effects 0.000 abstract description 10
- 238000000034 method Methods 0.000 abstract description 7
- 239000000203 mixture Substances 0.000 abstract description 7
- RKTYLMNFRDHKIL-UHFFFAOYSA-N copper;5,10,15,20-tetraphenylporphyrin-22,24-diide Chemical group [Cu+2].C1=CC(C(=C2C=CC([N-]2)=C(C=2C=CC=CC=2)C=2C=CC(N=2)=C(C=2C=CC=CC=2)C2=CC=C3[N-]2)C=2C=CC=CC=2)=NC1=C3C1=CC=CC=C1 RKTYLMNFRDHKIL-UHFFFAOYSA-N 0.000 abstract description 6
- -1 tetragonal compound Chemical class 0.000 abstract description 3
- 229910052719 titanium Inorganic materials 0.000 abstract description 3
- 229910045601 alloy Inorganic materials 0.000 abstract description 2
- 239000000956 alloy Substances 0.000 abstract description 2
- 239000011248 coating agent Substances 0.000 description 5
- 238000000576 coating method Methods 0.000 description 5
- 229910001172 neodymium magnet Inorganic materials 0.000 description 5
- 239000004575 stone Substances 0.000 description 5
- 229910052772 Samarium Inorganic materials 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- 239000000843 powder Substances 0.000 description 4
- 238000005245 sintering Methods 0.000 description 4
- 229910052779 Neodymium Inorganic materials 0.000 description 3
- 239000013078 crystal Substances 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 229910052742 iron Inorganic materials 0.000 description 3
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 238000004544 sputter deposition Methods 0.000 description 3
- 229910052727 yttrium Inorganic materials 0.000 description 3
- 240000008067 Cucumis sativus Species 0.000 description 2
- 235000010799 Cucumis sativus var sativus Nutrition 0.000 description 2
- 229910052692 Dysprosium Inorganic materials 0.000 description 2
- 229910002056 binary alloy Inorganic materials 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 238000004663 powder metallurgy Methods 0.000 description 2
- 241000894007 species Species 0.000 description 2
- 238000006467 substitution reaction Methods 0.000 description 2
- 239000010409 thin film Substances 0.000 description 2
- 229910052684 Cerium Inorganic materials 0.000 description 1
- 229910052691 Erbium Inorganic materials 0.000 description 1
- 229910052693 Europium Inorganic materials 0.000 description 1
- 229910017061 Fe Co Inorganic materials 0.000 description 1
- 229910052688 Gadolinium Inorganic materials 0.000 description 1
- 229910052689 Holmium Inorganic materials 0.000 description 1
- 229910052765 Lutetium Inorganic materials 0.000 description 1
- 229910052777 Praseodymium Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 229910052771 Terbium Inorganic materials 0.000 description 1
- 229910052775 Thulium Inorganic materials 0.000 description 1
- 229910052769 Ytterbium Inorganic materials 0.000 description 1
- 239000004927 clay Substances 0.000 description 1
- 235000021438 curry Nutrition 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000004070 electrodeposition Methods 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 239000012770 industrial material Substances 0.000 description 1
- 150000002500 ions Chemical class 0.000 description 1
- 229910052746 lanthanum Inorganic materials 0.000 description 1
- 230000005389 magnetism Effects 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 238000009740 moulding (composite fabrication) Methods 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000005240 physical vapour deposition Methods 0.000 description 1
- 238000007747 plating Methods 0.000 description 1
- 238000010298 pulverizing process Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 239000011347 resin Substances 0.000 description 1
- 229920005989 resin Polymers 0.000 description 1
- 230000002441 reversible effect Effects 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000011105 stabilization Methods 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 229910002058 ternary alloy Inorganic materials 0.000 description 1
- 238000007740 vapor deposition Methods 0.000 description 1
- 238000005303 weighing 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
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
【発明の詳細な説明】
（産業上の利用分野）
本発明は各種電機・電子機器材料として有用な磁気特性
に優れた希土類永久磁石に関する。DETAILED DESCRIPTION OF THE INVENTION (Field of Industrial Application) The present invention relates to a rare earth permanent magnet with excellent magnetic properties useful as a material for various electrical and electronic devices.
（従来技術とその問題点）
従来良く知られ量産化されている希土類永久磁石には、
Ｓｍ−Ｃｏ系磁石があり、これにはＣｕを含まない１１
５磁石とＣｕを含む２相分離型２／１７磁石がある。後
者の２／１７磁石は最大エネルギー積、（ＢＨ）、、、
Ｘが３０Ｍ−Ｇｏｅに達し高特性磁石として、スピーカ
ー、モーター、計測器等に使用されている。Ｓｍ−Ｃｏ
系磁石は高価なＳｍ、Ｃｏ金属を使用しているためコス
トの点からＣＯをＦｅで置換する割合をなるべく高める
ことが中心的な開発課題である。しかし現在量産化され
ている２７１７Ｅｎ石でもＣＯの２０ａｔ％置換がせい
ぜいであり、１１５磁石にはＦｅが固溶しないため、量
産の主流は２／１７１ａ石に移りつつある。(Prior art and its problems) Rare earth permanent magnets that are well-known and mass-produced include:
There are Sm-Co magnets, which do not contain Cu11
5 magnet and a two-phase separated type 2/17 magnet containing Cu. The latter 2/17 magnet has the maximum energy product, (BH),...
With X reaching 30M-Goe, it is used as a high-performance magnet in speakers, motors, measuring instruments, etc. Sm-Co
Since the system magnet uses expensive Sm and Co metals, the main development issue is to increase the ratio of replacing CO with Fe as much as possible from the viewpoint of cost. However, even with the 2717En stone currently being mass-produced, CO replacement is at most 20 at%, and since Fe is not dissolved in solid solution in the 115 magnet, the mainstream of mass production is shifting to the 2/171a stone.
最近開発されたＮｄ−Ｆｅ−Ｂの三元系磁石はＳｍ−Ｃ
ｏ系磁石よりさらに高特性であり、しかも資源的に豊富
なＮｄ、Ｆｅを主たる原料にしているので大変注目され
ている。しかしこのＮｄ６ｎ石は大変錆び易く何等かの
コーティングが必要となるが、未だに量産に適した方法
が見つかって居らず、この点がネックとなって広く用い
られるまでに至っていない。またＮｄ−Ｆｅ−Ｂ系磁石
はキュリ一点（Ｔｃ）が３１０℃と低いため、残留磁化
の温度変化ｔＪ（−０，１２％／℃と大きく、モーター
や計測器のように温度に対する安定性が要求される分野
では使用困難であった。The recently developed Nd-Fe-B ternary magnet is Sm-C
It is attracting a lot of attention because it has higher characteristics than O-based magnets and uses Nd and Fe, which are rich in resources, as the main raw materials. However, this Nd6n stone is very susceptible to rust and requires some kind of coating, but a method suitable for mass production has not yet been found, and this point has been a bottleneck that has prevented it from being widely used. In addition, Nd-Fe-B magnets have a low Curie point (Tc) of 310°C, so the temperature change in residual magnetization tJ (-0.12%/°C) is large, making them less stable against temperature like motors and measuring instruments. It was difficult to use in the field where it was required.
他方、Ｒ−Ｆｅ系の二元化合物としてＲＦｅ２゜ＲＦｅ
５． Ｒ２Ｆｅ１ｙ化合物が良く知られているが、こ
れらはキュリ一点（Ｔｃ）、飽和磁化（４πＭｓ）、６
２２気異方性常数（Ｋｕ）の何れかが低いため磁石素材
としては適していない。On the other hand, as a binary compound of R-Fe system, RFe2゜RFe
5. R2Fely compounds are well known, and these have a single Curie point (Tc), saturation magnetization (4πMs), and 6
It is not suitable as a magnet material because any one of the 22 gas anisotropy constants (Ku) is low.
Ｃｒｏａｔらはこの様な事情があるにも関わらすＲ−Ｆ
ｅの二元系を急冷薄帯法で急冷し、準安定相をクエンチ
して磁石化した（＾１１１）ｌ Ｐｈｙｓ、 Ｌｅｔｔ
。Despite these circumstances, Croat et al.
The binary system of e was quenched by the quenched ribbon method, the metastable phase was quenched, and it became a magnet (＾111)l Phys, Lett
.
３７．１０９６．１９８１） 、また、 （：ａｄｉｅ
ｕ等はスパッター法によりＳｍＦｅ３および（ＳｍＴｉ
）Ｆｅ、の薄膜が作成できることを示した（Ｊ、 Ａｐ
ｐｌ、 Ｐｈｙｓ。37.1096.1981), also (:adie
u etc. are SmFe3 and (SmTi) by sputtering method.
) showed that it is possible to create a thin film of Fe (J, Ap
pl, Phys.
Ｖｏｌ 、５５．２８１１．１９８４）。Vol. 55.2811.1984).
しかし、これもスパッター法による準安定相で、バルク
には存在しないものと考えられていた。そして彼等はこ
れらの薄膜は六方晶であると報告している。この様な磁
石は等方性で特性も低く、準安定相を基本としているた
めその安定性にも疑問がもたれ、より高特性で錆び難く
、安価なＦｎ石の開発が望まれていた。However, this is also a metastable phase created by sputtering and was thought to not exist in the bulk. They report that these thin films are hexagonal. Such magnets are isotropic, have low properties, and are based on a metastable phase, which raises questions about their stability.Therefore, there has been a desire to develop Fn stones with higher properties, rust resistance, and low cost.
上述したようにＲ−Ｆｅ二元系ではキューり点なと磁石
素材としての必要条件を満たすバルクの化合物は知られ
ていなかった。ところがＮｄ−Ｆｅ−Ｂ三元化合物のバ
ルクを主体とする磁石が佐用らによって開発されたため
、本発明者らはそれ以外のＲ−Ｆｅ−Ｍ（但しＭは希土
類元素以外の第３元素）よりなる磁石化可能な三元また
は四元の化合物について種種探索した結果、今までに知
られていない結晶構造をもつ一連の化合物を見いだし、
このような化合物の１つを磁石として提案した（特願６
ｌ−８４７２３）。しかしこれはキューリ温度が最高で
約３１０℃であり、前記Ｎｄ系磁石同様磁化の温度変化
に問題があった。そこでこの点を改良するため鋭意検討
を重ね、Ｆｅの一部をＣｏで置換することによりキュー
リ点が大幅に向上し磁化の温度変化が改善されることを
見いだし本発明に到達１ノたのである。As mentioned above, in the R-Fe binary system, no bulk compound having a cue point and satisfying the requirements as a magnet material has been known. However, since Sayo et al. developed a magnet based on the bulk of the Nd-Fe-B ternary compound, the present inventors developed a magnet based on the bulk of the Nd-Fe-B ternary compound. As a result of searching for various ternary or quaternary compounds that can be magnetized, we discovered a series of compounds with previously unknown crystal structures.
proposed one of these compounds as a magnet (patent application 6).
l-84723). However, this has a maximum Curie temperature of about 310° C., and like the Nd-based magnets described above, there is a problem with temperature changes in magnetization. Therefore, in order to improve this point, we conducted extensive studies and found that by replacing a portion of Fe with Co, the Curie point was significantly improved and the temperature change in magnetization was improved, and we were able to arrive at the present invention. .
（発明の構成）
本発明は前記高価なＣＯ金金属使用を極力抑えＳｍ−Ｃ
ｏ系磁石と同等あるいはそれ以上の６ｎ気特性をもつ、
特にキュリ一点の高い希土類磁石の提供を目的としてお
り、
式Ｒｙ Ｔ ｓ ｙ Ｍｚ Ｆ ｅａ ＣＯｂ（式中Ｒ
はＹを含む希土類元素、ＭはＺｒまたはＨｆであり、重
量百分率でＸは１２〜３０％、ｙは１〜８％、Ｚは０．
１〜８％、ａは５５〜８５％、ｂは３４％以下である）
で示される希土類永久ｒＩ１１石を要旨とするものであ
る。(Structure of the Invention) The present invention minimizes the use of the expensive CO gold metal, and the Sm-C
It has 6N characteristics that are equal to or better than O-type magnets.
In particular, we aim to provide rare earth magnets with a unique level of Curie.
is a rare earth element containing Y, M is Zr or Hf, and in weight percentage, X is 12 to 30%, y is 1 to 8%, and Z is 0.
1-8%, a is 55-85%, b is 34% or less)
This article focuses on rare earth permanent rI11 stones shown in .
以下これについて詳しく説明すると、本発明の永久磁石
はＲ−Ｔ ｉ −Ｍ−Ｆｅ−Ｃｏの三元系合金からなる
もので、前記のようにＲはｙを含む希土類元素の１種ま
たは２種以上、ＭはＺｒまたはＨｆあるいはＺｒとＨｆ
との混合物でもよい。それらの組成範囲は重量百分率で
ｘ＝１２〜３０％、ｙ＝１〜８％、ｚ＝ｏ、１〜８％、
ａ＝５５〜８５％モしてｂは３４％以下である。To explain this in detail below, the permanent magnet of the present invention is made of a ternary alloy of R-Ti-M-Fe-Co, and as mentioned above, R is one or two rare earth elements including y. Above, M is Zr or Hf or Zr and Hf
It may also be a mixture with Their composition range in weight percentage is x=12-30%, y=1-8%, z=o, 1-8%,
a=55 to 85%, and b is 34% or less.
上記合金組成を決定するに当り、本発明者らは例えばＲ
としてＳｍを選びＳ ｍＴ ｆ Ｏ，９Ｚ ｒ ｏ、
＋（Ｆｅ、−ウＣ０Ｘ）１０の二元化合物を作成し、そ
のＸ線回折を行フたところ正方晶構造であることを確認
し指数すけ出来ることが明らかになった。In determining the above alloy composition, the present inventors, for example, R
Select Sm as S mT f O,9Z r o,
A binary compound of + (Fe, -UCO
そして磁化の温度変化もほぼ単−相に近いこと、Ｔｉ、
Ｚｒの導入により正方晶の化合物が安定化されることが
わかった。さらに研究を進めた結果このことはＳｍ以外
全ての希土類元素およびＹについても適用しうることを
見いだした。Also, the temperature change in magnetization is almost single-phase.
It was found that the tetragonal compound was stabilized by the introduction of Zr. As a result of further research, it was found that this can be applied to all rare earth elements other than Sm and Y.
キュリ一点について熱磁気カーブを測定したところ第１
図に示すような結果を得た。これによって例えば１０％
の置換で６０℃以上の上昇を示し磁化の温度変化は顕著
に改善されることがわかった。When the thermomagnetic curve was measured for one point of Currie, the first result was
The results shown in the figure were obtained. For example, 10%
It was found that the temperature change in magnetization was significantly improved, showing an increase of 60° C. or more with the substitution of .
前記Ｒとしては、Ｌａ、Ｃｅ、Ｐｒ、Ｎｄ、Ｓｍ。The above R includes La, Ce, Pr, Nd, and Sm.
Ｅｕ、Ｇｄ、Ｔｂ、Ｄｙ、Ｈｏ、Ｅｒ、Ｔｍ。Eu, Gd, Tb, Dy, Ho, Er, Tm.
Ｙｂ、Ｌｕの希土類元素及びＹが挙げられ、これらの１
種または２種以上の混合物が使用される。Rare earth elements such as Yb and Lu and Y are mentioned, and these 1
Species or mixtures of two or more species are used.
磁石としてより好ましいのは軽希土類元素である。この
理由として重希土類元素を使用した場合には飽和磁化が
低下するためである。Light rare earth elements are more preferred as magnets. The reason for this is that when heavy rare earth elements are used, the saturation magnetization decreases.
Ｒが前記範囲以外のとぎは正方晶構造が安定せず、しか
も１２％以下では保磁力（ｉＨｃ）が、また３０％以上
では飽和磁化（４πＭｓ）がそれぞれ大きく低下するた
め前記範囲内であることが必要である。さらにＴｉ、Ｍ
が前記範囲以外のときは正方晶構造が安定せず、特に８
％以上のときは正方晶の割合が少なくなるため前記範囲
が必要である。また好ましくはＴｉとＭの和が２〜１５
％の間であるのがよい。これは磁性を担っているＦｅ原
子間の距離を適当な範囲に保つために必要である。If R is outside the above range, the tetragonal structure will not be stable, and if it is less than 12%, the coercive force (iHc) will be greatly reduced, and if it is more than 30%, the saturation magnetization (4πMs) will be greatly reduced, so it must be within the above range. is necessary. Furthermore, Ti, M
is outside the above range, the tetragonal structure will not be stable, especially when 8
% or more, the proportion of tetragonal crystals decreases, so the above range is necessary. Preferably, the sum of Ti and M is 2 to 15.
It is better to be between %. This is necessary to maintain the distance between Fe atoms, which are responsible for magnetism, within an appropriate range.
Ｃｏの置換量についてはＦｅの量の４０％以下が適当で
ある。これは、第１図に示すようにＦｅをＣｏで置換す
ることによりキュリ一点は大幅に上昇するが、磁気異方
性常数が低下するため、また高価なＣＯの爾用量をなる
べく抑えるためにもこれ以上置換し過ぎることは好まし
くない。The appropriate amount of Co to be substituted is 40% or less of the amount of Fe. This is because, as shown in Figure 1, replacing Fe with Co greatly increases the Curie point, but the magnetic anisotropy constant decreases, and also because it is necessary to suppress the amount of expensive CO as much as possible. It is not preferable to substitute too much.
本発明に係わる希土類永久磁石は、前記の元素よりなる
組成物を粉末冶金法により、溶解、鋳造、粉砕、磁場中
成形、焼結熱処理することにより得ることが出来る。The rare earth permanent magnet according to the present invention can be obtained by melting, casting, pulverizing, forming in a magnetic field, and heat-sintering a composition made of the above-mentioned elements using a powder metallurgy method.
本発明による希土類永久磁石は前述のようにＴｉ、Ｍに
より正方晶の安定な結晶構造を持つ化合物相を主体とす
る磁石であるので、二元系の化合物に比べてキュリ一点
も高く、飽和磁化も同様に大幅な上昇を示し高い磁気特
性が得られる。または粉末焼結法により異方性磁石とす
ることが出来るので、Ｓｍ−Ｃｏ系磁石と同等以上の磁
石が得られ、しかもよりすくないＣＯ量の磁石であるた
め工業材料としては極めて有利である。As mentioned above, the rare earth permanent magnet according to the present invention is a magnet mainly composed of a compound phase with a stable tetragonal crystal structure made of Ti and M, so it has a saturation magnetization that is one Curie point higher than that of binary compounds. Similarly, the magnetic properties show a significant increase and high magnetic properties can be obtained. Alternatively, since it can be made into an anisotropic magnet by a powder sintering method, a magnet that is equivalent to or better than Sm--Co magnets can be obtained, and since it is a magnet with a lower amount of CO, it is extremely advantageous as an industrial material.
Ｎｄ−Ｆｅ−Ｂ系の磁石では粉末冶金法により磁石を製
造する場合微粉末の急激な酸化により磁気特性の大幅な
劣化が起きる。さらに焼結体の表面も非常に錆び易く、
適切なコーティングをしない限り耐えない。然るに本発
明の粘土磁石はＦｅを主体とする磁石でありながら、高
い耐食性を有しており特にコーティングをしなくても使
用可能である。当然、樹脂塗装（スプレー、電着塗装）
、メッキ（電解、無電解）やＰＶＤ （蒸着、スパッタ
ー、イオンブレーティング）によりコーティングするこ
とにより、さらに耐食性を向上させることが出来る。When manufacturing Nd-Fe-B magnets by powder metallurgy, rapid oxidation of fine powder causes significant deterioration of magnetic properties. Furthermore, the surface of the sintered body is also very susceptible to rust.
Will not withstand unless properly coated. However, although the clay magnet of the present invention is a magnet mainly composed of Fe, it has high corrosion resistance and can be used without any particular coating. Naturally, resin coating (spray, electrodeposition coating)
Corrosion resistance can be further improved by coating by plating (electrolytic, electroless) or PVD (vapor deposition, sputtering, ion blating).
また、急冷薄帯法によフても高い保磁力を有する薄帯が
得られるので、これを粉砕して等方性のプラスチックマ
グネットにしたり、異方性焼結体を粉砕し、異方性プラ
スチックマグネットとすることが出来る。In addition, since the quenched ribbon method produces a ribbon with a high coercive force, it can be crushed to make an isotropic plastic magnet, or an anisotropic sintered body can be crushed to create an anisotropic It can be a plastic magnet.
（発明の効果）
本発明によればＲ−Ｆｅ系にＴｉ−Ｍを所定量加えるこ
とにより、これまで知られていなかった正方晶化合物の
安定化を達成し、高価なＣｏを使用するＳｍ−Ｃｏ系磁
石に代るキューリ点の高い希土類永久磁石が得られる。(Effects of the Invention) According to the present invention, by adding a predetermined amount of Ti-M to the R-Fe system, stabilization of tetragonal compounds, which was unknown until now, can be achieved, and Sm- A rare earth permanent magnet with a high Curie point can be obtained in place of a Co-based magnet.
（実施例１） 各々純度９９．９％のＳｍ、Ｔｉ、Ｚｒ、Ｆｅ。(Example 1) Sm, Ti, Zr, and Fe, each with a purity of 99.9%.
ＣＯメタルを第１表に示す割合で秤量後、高周波溶解炉
で溶解し鋼鋳造に溶湯を傾注してインゴットを作成した
。このインゴットをＮ２ガス中でシェドミルにより平均
粒径２〜１０μｍの大きさに粉砕した。得られた微粉を
粉末焼結法により、１５ｋＯｅの磁場中で配向後、油圧
プレスにて１．５ｔ／ｃｍ’の圧力でプレス成形した。After weighing CO metal in the proportions shown in Table 1, it was melted in a high frequency melting furnace and the molten metal was poured into a steel casting to create an ingot. This ingot was ground to an average particle size of 2 to 10 μm using a shed mill in N2 gas. The obtained fine powder was oriented in a magnetic field of 15 kOe by a powder sintering method, and then press-molded using a hydraulic press at a pressure of 1.5 t/cm'.
この成形体（Ｎｏ、１〜４）をＡｒガス中で、１０００
〜１２００℃で１時間焼結を行った後、４００〜９００
℃でさらに１時間処理した後急冷した。The molded bodies (No. 1 to 4) were heated to 1000°C in Ar gas.
After sintering at ~1200°C for 1 hour, the
After further treatment at ℃ for 1 hour, it was rapidly cooled.
熱処理後の異方性焼結体の磁気特性を測定したところ、
第１表に示す結果が得られた。各々のキューリ一点も同
時に示すがＳｍＴｉＦｅ、。のキューリ一点３１０℃と
比較すると大幅に上昇している。When we measured the magnetic properties of the anisotropic sintered body after heat treatment, we found that
The results shown in Table 1 were obtained. One point of each cucumber is also shown at the same time, SmTiFe. This is a significant increase compared to 310 degrees Celsius for a single cucumber.
（実施例２） 各々純度９９，９％のＮｄ、Ｓｍ、Ｄｙ、ＹとＴｉ。(Example 2) Nd, Sm, Dy, Y and Ti, each with a purity of 99.9%.
Ｚｒ、Ｈｆ、Ｆｅ、（Ｎｏ、５〜８）Ｃｏを第２表に示
す割合で秤量し、実施例１と同一条件で製造して異方性
焼結体（Ｎｏ、 ５〜８）を作成した。各々の異方性焼
結体の磁気特性を測定したところ第２表に示す結果が得
られた。実用上十分な保磁力が得られることが分かる。Zr, Hf, Fe, and (No. 5 to 8) Co were weighed in the proportions shown in Table 2 and produced under the same conditions as Example 1 to create anisotropic sintered bodies (No. 5 to 8). did. When the magnetic properties of each anisotropic sintered body were measured, the results shown in Table 2 were obtained. It can be seen that a practically sufficient coercive force can be obtained.
室温から１００℃の間での可逆温度係数も示す。ＳｍＴ
ｉＦｅ係の−０，１２％／Ｃに比べると大幅に改善され
ている。The reversible temperature coefficient between room temperature and 100°C is also shown. SmT
This is a significant improvement compared to -0.12%/C for iFe.
第１図は
Ｓｍ （Ｔｉａ、ｏ Ｚｒｏ、＋ ）（Ｆｅ、−８ＣＯ
ｘ）１０の磁石組成においてＣＯの置換量とキュリ一温
度の変化を示すグラフである。Figure 1 shows Sm (Tia, o Zro, +) (Fe, -8CO
x) It is a graph showing the change in the amount of CO substitution and the Curie temperature in a magnet composition of 10.
Claims (1)
はＹを含む希土類元素、ＭはＺｒまたはＨｆであり、重
量百分率でｘは１２〜３０％、ｙは１〜８％、ｚは０．
１〜８％、ａは５５〜８５％、ｂは３４％以下である）
で示される希土類永久磁石。 ２、前記ＴｉとＭの和が重量百分率で２〜１５％である
特許請求の範囲第１項記載の希土類永久磁石。[Claims] 1. Formula R_xTi_yM_zFe_aCo_b (wherein R
is a rare earth element containing Y, M is Zr or Hf, x is 12 to 30%, y is 1 to 8%, and z is 0.
1-8%, a is 55-85%, b is 34% or less)
A rare earth permanent magnet shown in 2. The rare earth permanent magnet according to claim 1, wherein the sum of Ti and M is 2 to 15% by weight.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62082398A JPS63248102A (en) | 1987-04-03 | 1987-04-03 | Rare earth permanent magnet |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62082398A JPS63248102A (en) | 1987-04-03 | 1987-04-03 | Rare earth permanent magnet |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS63248102A true JPS63248102A (en) | 1988-10-14 |
Family
ID=13773485
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP62082398A Pending JPS63248102A (en) | 1987-04-03 | 1987-04-03 | Rare earth permanent magnet |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS63248102A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5482573A (en) * | 1991-10-16 | 1996-01-09 | Kabushiki Kaisha Toshiba | Magnetic material |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS56150153A (en) * | 1980-04-18 | 1981-11-20 | Namiki Precision Jewel Co Ltd | Permanent magnet alloy |
| JPS6110209A (en) * | 1984-06-26 | 1986-01-17 | Toshiba Corp | Permanent magnet |
| JPS6151901A (en) * | 1984-08-22 | 1986-03-14 | Daido Steel Co Ltd | Manufacture of permanent magnet |
| JPS6178102A (en) * | 1984-09-25 | 1986-04-21 | Daido Steel Co Ltd | Permanent magnet material |
-
1987
- 1987-04-03 JP JP62082398A patent/JPS63248102A/en active Pending
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS56150153A (en) * | 1980-04-18 | 1981-11-20 | Namiki Precision Jewel Co Ltd | Permanent magnet alloy |
| JPS6110209A (en) * | 1984-06-26 | 1986-01-17 | Toshiba Corp | Permanent magnet |
| JPS6151901A (en) * | 1984-08-22 | 1986-03-14 | Daido Steel Co Ltd | Manufacture of permanent magnet |
| JPS6178102A (en) * | 1984-09-25 | 1986-04-21 | Daido Steel Co Ltd | Permanent magnet material |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5482573A (en) * | 1991-10-16 | 1996-01-09 | Kabushiki Kaisha Toshiba | Magnetic material |
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