JPS62181403A - Permanent magnet - Google Patents
Permanent magnetInfo
- Publication number
- JPS62181403A JPS62181403A JP61023228A JP2322886A JPS62181403A JP S62181403 A JPS62181403 A JP S62181403A JP 61023228 A JP61023228 A JP 61023228A JP 2322886 A JP2322886 A JP 2322886A JP S62181403 A JPS62181403 A JP S62181403A
- Authority
- JP
- Japan
- Prior art keywords
- amount
- powder
- coercive force
- magnet
- permanent magnet
- 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
- 229910052772 Samarium Inorganic materials 0.000 claims abstract description 5
- 229910052735 hafnium Inorganic materials 0.000 claims abstract description 5
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 5
- 229910052684 Cerium Inorganic materials 0.000 claims abstract description 4
- 229910052691 Erbium Inorganic materials 0.000 claims abstract description 4
- 229910052796 boron Inorganic materials 0.000 claims abstract description 4
- 229910052727 yttrium Inorganic materials 0.000 claims abstract description 4
- 229910052692 Dysprosium Inorganic materials 0.000 claims abstract description 3
- 229910052688 Gadolinium Inorganic materials 0.000 claims abstract description 3
- 229910052779 Neodymium Inorganic materials 0.000 claims abstract description 3
- 229910052777 Praseodymium Inorganic materials 0.000 claims abstract description 3
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 229910052746 lanthanum Inorganic materials 0.000 claims abstract description 3
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 3
- 229910052758 niobium Inorganic materials 0.000 claims abstract 2
- 239000000654 additive Substances 0.000 claims 1
- 230000000996 additive effect Effects 0.000 claims 1
- 239000000843 powder Substances 0.000 abstract description 16
- 238000000465 moulding Methods 0.000 abstract description 6
- 230000000694 effects Effects 0.000 abstract description 5
- 238000000034 method Methods 0.000 abstract description 5
- 239000000203 mixture Substances 0.000 abstract description 5
- 238000005266 casting Methods 0.000 abstract description 3
- 229910052689 Holmium Inorganic materials 0.000 abstract description 2
- 229910052771 Terbium Inorganic materials 0.000 abstract description 2
- 238000007596 consolidation process Methods 0.000 abstract description 2
- 238000004090 dissolution Methods 0.000 abstract 1
- 239000000463 material Substances 0.000 abstract 1
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 10
- 238000005245 sintering Methods 0.000 description 8
- 229910045601 alloy Inorganic materials 0.000 description 7
- 239000000956 alloy Substances 0.000 description 7
- 238000010438 heat treatment Methods 0.000 description 7
- 229910052761 rare earth metal Inorganic materials 0.000 description 5
- 230000032683 aging Effects 0.000 description 4
- 230000007423 decrease Effects 0.000 description 4
- 238000002844 melting Methods 0.000 description 4
- 230000008018 melting Effects 0.000 description 4
- 230000001590 oxidative effect Effects 0.000 description 4
- 238000011282 treatment Methods 0.000 description 4
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 3
- 238000001816 cooling Methods 0.000 description 3
- 230000004907 flux Effects 0.000 description 3
- 239000007789 gas Substances 0.000 description 3
- 239000011261 inert gas Substances 0.000 description 3
- 150000001247 metal acetylides Chemical class 0.000 description 3
- 239000002994 raw material Substances 0.000 description 3
- 229910052723 transition metal Inorganic materials 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 239000000314 lubricant Substances 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 239000011812 mixed powder Substances 0.000 description 2
- 150000002910 rare earth metals Chemical class 0.000 description 2
- 150000003624 transition metals Chemical group 0.000 description 2
- VWQVUPCCIRVNHF-UHFFFAOYSA-N yttrium atom Chemical compound [Y] VWQVUPCCIRVNHF-UHFFFAOYSA-N 0.000 description 2
- 229910000640 Fe alloy Inorganic materials 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- GWXLDORMOJMVQZ-UHFFFAOYSA-N cerium Chemical compound [Ce] GWXLDORMOJMVQZ-UHFFFAOYSA-N 0.000 description 1
- 238000005056 compaction Methods 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 238000007872 degassing Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- KBQHZAAAGSGFKK-UHFFFAOYSA-N dysprosium atom Chemical compound [Dy] KBQHZAAAGSGFKK-UHFFFAOYSA-N 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- UYAHIZSMUZPPFV-UHFFFAOYSA-N erbium Chemical compound [Er] UYAHIZSMUZPPFV-UHFFFAOYSA-N 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- KJZYNXUDTRRSPN-UHFFFAOYSA-N holmium atom Chemical compound [Ho] KJZYNXUDTRRSPN-UHFFFAOYSA-N 0.000 description 1
- FZLIPJUXYLNCLC-UHFFFAOYSA-N lanthanum atom Chemical compound [La] FZLIPJUXYLNCLC-UHFFFAOYSA-N 0.000 description 1
- QEFYFXOXNSNQGX-UHFFFAOYSA-N neodymium atom Chemical group [Nd] QEFYFXOXNSNQGX-UHFFFAOYSA-N 0.000 description 1
- QIQXTHQIDYTFRH-UHFFFAOYSA-N octadecanoic acid Chemical compound CCCCCCCCCCCCCCCCCC(O)=O QIQXTHQIDYTFRH-UHFFFAOYSA-N 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
- PUDIUYLPXJFUGB-UHFFFAOYSA-N praseodymium atom Chemical compound [Pr] PUDIUYLPXJFUGB-UHFFFAOYSA-N 0.000 description 1
- 229910001404 rare earth metal oxide Inorganic materials 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- KZUNJOHGWZRPMI-UHFFFAOYSA-N samarium atom Chemical compound [Sm] KZUNJOHGWZRPMI-UHFFFAOYSA-N 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 239000007858 starting material Substances 0.000 description 1
- GZCRRIHWUXGPOV-UHFFFAOYSA-N terbium atom Chemical compound [Tb] GZCRRIHWUXGPOV-UHFFFAOYSA-N 0.000 description 1
Classifications
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/032—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials
- H01F1/04—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials metals or alloys
- H01F1/047—Alloys characterised by their composition
- H01F1/053—Alloys characterised by their composition containing rare earth metals
- H01F1/055—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5
- H01F1/057—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
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Ｒ−Ｂ−Ｆｅ系焼結磁石において炭化物を形成
することにより保磁力（ｉＨｃ）を改善したものである
。DETAILED DESCRIPTION OF THE INVENTION [Industrial Application Field] The present invention improves coercive force (iHc) by forming carbides in an R-B-Fe sintered magnet.
近年、従来のＳｍ −Ｃｏ系磁石に比較し、より高磁気
特性を有しかつ資源的にも高価なＳｍやＣｏを、必らず
しも含まないＮｄ −Ｂ −Ｆｅ系永久磁石が、発明さ
れた。（佐用ほか、Ｊ、Ａｐｐｌ、Ｐｈｙｓ、５５（６
）、１５Ｍａｒｃｈ １９８４ 、 ｐ２０８３〜２０
８７．および特開昭５９−４７５００８号公報、同５９
−２０４２０９号公報参照）それらＫよれば、製造方法
として溶解、鋳造し得られた合金インゴットを粉砕し、
必要に応じて磁界を印加しながらプレス成形し、さらに
焼結することが開示されている。In recent years, Nd-B-Fe-based permanent magnets have been invented that have higher magnetic properties than conventional Sm-Co-based magnets and do not necessarily contain Sm or Co, which are expensive in terms of resources. It was done. (Sayo et al., J. Appl. Phys., 55 (6
), 15March 1984, p2083-20
87. and Japanese Unexamined Patent Publication No. 59-475008, 59
(Refer to Publication No. 204209) According to those K, as a manufacturing method, an alloy ingot obtained by melting and casting is crushed,
It is disclosed that press molding is performed while applying a magnetic field as necessary, and further sintering is performed.
しかし、これら従来の方法による製造方法では磁気特性
の点で、十分満足のできる保磁力（ｉＨｃ）が得られる
には、至ってない。However, with these conventional manufacturing methods, it has not been possible to obtain a sufficiently satisfactory coercive force (iHc) in terms of magnetic properties.
本発明は上述した従来技術の問題点を解消し、保磁力（
ｉＨｃ）が大きく、磁気特性の優れたＲ−Ｂ−Ｆｅ系永
久磁石を得ることを目的とするものである０
すなわち、従来方法の場合、原料およびその他の要因で
Ｃ（炭素）が、混入−存在すると、保磁力（ｉＨｃ ）
が低下するという問題を有］−ていた。たとえば、Ｎｄ
酸化物を精製する場合、電極からＣがＮｄメタルへ混入
する。そのようなＣ量の多Ｎｄメタルを使用すると、磁
気特性の低下が生じる。The present invention solves the above-mentioned problems of the prior art and has a coercive force (
The purpose of this method is to obtain an R-B-Fe permanent magnet with a large iHc) and excellent magnetic properties. If present, the coercive force (iHc)
There was a problem that the For example, Nd
When refining an oxide, C is mixed into the Nd metal from the electrode. If such a Nd-rich metal with a high C content is used, the magnetic properties will deteriorate.
また、成形時にＣを含む滑剤などを用いると、前記と同
様な持性低下が生じる。Furthermore, if a lubricant containing C is used during molding, the same deterioration in durability as described above occurs.
上記問題点に対し、撞々検訂した結果、ＣがＭ（Ｎｂ
、 Ｔｉ 、 Ｚｒ 、 Ｈｆの内少くとも１８Ｉ）と
炭化物を形成しやすい性質を利用し本発明を見出すに至
ったのである。As a result of thorough examination of the above problems, we found that C is M(Nb
The present invention was discovered by taking advantage of the property of easily forming carbides with at least 18I of Ti, Zr, and Hf.
本発明を詳述すると原子チで８〜３０％のＮｄ 。To explain the present invention in detail, Nd is 8 to 30% in terms of atoms.
Ｐｒ ｒ Ｄｙ ＋ Ｈｏ ＋ Ｔｂの内、少くとも１
種と、Ｌａ ＋Ｃｅ 、 Ｓｍ ｒ Ｇｄ 、 Ｅｒ
ｒ Ｙの内少くとも１種、２〜２８チのＢ 、０．０２
〜２％のＣおよび残部Ｆｅと不純物から成る焼結磁石に
おいて、Ｍ（Ｎｂ 、 ’ｌ’ｉ 。At least 1 of Pr r Dy + Ho + Tb
Seeds, La + Ce, Sm r Gd, Er
r At least one type of Y, 2 to 28 B, 0.02
In a sintered magnet consisting of ~2% C and balance Fe and impurities, M(Nb,'l'i).
Ｚｒ 、 Ｈｆの内少くとも１種）のｔ （ｙ）がＣの
ＪＪＩ：（Ｘ）に対し
Ｘ≦ｙ≦（ｘ＋４） の範囲であることを、特徴とす
るものである。It is characterized in that t (y) of at least one of Zr and Hf is in the range of X≦y≦(x+4) with respect to JJI: (X) of C.
本発明を詳述すると先ず公知の手段にて所定成分を有す
るＲ−Ｂ−Ｆｅ系合金粉末またはそれと同組成となり得
る混合粉末が準備される。例えば、溶解、鋳造しインゴ
ットを粉末にする方法または溶解しアトマイズする方法
または希土類酸化物を出発原料とする還元拡散法で合金
粉は作成される。To explain the present invention in detail, first, an R-B-Fe alloy powder having a predetermined component or a mixed powder that can have the same composition is prepared by known means. For example, the alloy powder is prepared by a method of melting and casting an ingot into powder, a method of melting and atomizing, or a reduction diffusion method using a rare earth oxide as a starting material.
上記合金粉の少くとも一部をＦｅを代表する遷移金属粉
、ボロン粉、希土類金属粉、Ｂ−遷移金属合金粉、Ｒ−
遷移金属合金粉などの１種または２種以上で代替とした
混合粉末を使用しても本発明の効果は失なわれない。At least a part of the above alloy powder is a transition metal powder representing Fe, boron powder, rare earth metal powder, B-transition metal alloy powder, R-
The effects of the present invention will not be lost even if a mixed powder made of one or more of transition metal alloy powders is used instead.
上記粉末は、Ｃｉ （ｘ ＝ ０．０２〜２原子％）に
対応するＭ （Ｎ′ｂ＋ Ｔｌ ＋ Ｚｒ 、Ｈｆの内
少くとも１種）を含む。Ｍのｉｋ （ｙ）はＸ≦ｙ≦（
ｘ＋４）を満足せねばならない。The above powder contains M (at least one of N'b+Tl+Zr and Hf) corresponding to Ci (x = 0.02 to 2 atomic %). ik (y) of M is X≦y≦(
x+4) must be satisfied.
ｙの値が、Ｘ未満では十分な効果が得られないこと、（
ｘ＋４）を越えると、磁気特性が低下する理由による。If the value of y is less than X, sufficient effect cannot be obtained (
This is because when the value exceeds x+4), the magnetic properties deteriorate.
上記方法にて得られた粉末を圧縮プレスなどにて成形−
圧密化を行う。The powder obtained by the above method is molded using a compression press, etc.
Consolidate.
なお、上記成形−圧密化は、０．５〜１０ ｔ／ｄの成
形圧力が良く、必要に応じ成形時において、磁界（５Ｋ
Ｏｅ以上）を印加することによシ、磁気特性は向上する
。一連の成形−圧密化は湿式あるいは乾式でよく、常温
以外の高温度にて行っても良い。雰囲気は非酸化性雰囲
気が望ましく、例えば真空中、不活性ガス中あるいは還
元性ガス中にて行っても良い。得られた成形体を９００
〜１２００℃の温度にて焼結する。９００℃未満では、
密度があがらないためＢｒが十分でな（１２００℃を越
えるとＢｒおよび角形性が低下する理由による。The above molding-consolidation is preferably performed at a molding pressure of 0.5 to 10 t/d, and if necessary, a magnetic field (5K
Magnetic properties are improved by applying a magnetic field (Oe or more). The series of molding and compaction may be performed wet or dry, and may be performed at a high temperature other than room temperature. The atmosphere is preferably a non-oxidizing atmosphere, and may be carried out, for example, in a vacuum, an inert gas, or a reducing gas. The obtained molded body was heated to 900
Sinter at a temperature of ~1200°C. Below 900℃,
Br is not sufficient because the density does not increase (this is because Br and squareness decrease when the temperature exceeds 1200°C).
焼結は、Ｒ元素の酸化防止のための非酸化性雰囲気中に
て行なうことが望ましい。すなわち、真空、不活性ガス
、または還元性ガスの雰囲気が良い。なお、焼結時室温
からの昇温速度は特に規定しないが、昇温途中２００〜
８００℃の温度範囲で少くとも０．５時間保持すること
により、被加熱部の温度均一性を改善したり、真空中に
おいて脱ガス処理を行うことも可能となる。あるいは潤
滑剤として用いるステアリン酸塩などのクランキング（
水素化熱分解法）も、水素ガス雰囲気中で行い得る。従
って、焼結における雰囲気としては、真空あるいは不活
性ガス（例えばＡｒ ）あるいは還元性ガス（例えばＨ
２）などの非酸化性雰囲気が良い０加熱保持後の冷却速
度は、特に規定しないが、０．５〜１００ツ分が良く、
一般的には１〜１０℃２今が良い０遅くすることによシ
、その後の熱処理による磁気特性のバラツキが少なくな
るためである。また冷却は一度常温まで冷却することも
良くあるいは、５００℃迄行い、次の熱処理のため再度
昇温するように、焼結と熱処理を連続的に行っても良い
。Sintering is preferably performed in a non-oxidizing atmosphere to prevent oxidation of the R element. That is, a vacuum, an inert gas, or a reducing gas atmosphere is preferable. Note that the rate of temperature increase from room temperature during sintering is not particularly specified, but
By maintaining the temperature in the 800° C. range for at least 0.5 hours, it becomes possible to improve the temperature uniformity of the heated portion and to perform degassing treatment in a vacuum. or cranking (such as stearate) used as a lubricant.
Hydropyrolysis) can also be carried out in a hydrogen gas atmosphere. Therefore, the atmosphere for sintering should be vacuum, inert gas (e.g. Ar), or reducing gas (e.g. H2).
2) A non-oxidizing atmosphere such as
Generally speaking, by slowing down the heat treatment by 1 to 10°C, variations in magnetic properties due to subsequent heat treatment will be reduced. Further, cooling may be performed once to room temperature, or sintering and heat treatment may be performed continuously, such as cooling to 500° C. and raising the temperature again for the next heat treatment.
以上の焼結後、さらに磁気特性を向上せしめるため、５
００〜７００℃で時効処理を行うが、必要に応じ時効処
理前に８００〜１０００℃で保持−徐冷という中間熱処
理を行うことにより一層磁気特性が向上する。時効処理
、中間熱処理などの熱処理は前記焼結と同じく、非酸化
性雰囲気が望ましい。After the above sintering, in order to further improve the magnetic properties,
Aging treatment is performed at 00 to 700°C, but if necessary, an intermediate heat treatment of holding and slow cooling at 800 to 1000°C is performed before aging to further improve the magnetic properties. Heat treatments such as aging treatment and intermediate heat treatment are preferably performed in a non-oxidizing atmosphere, as in the case of sintering.
なお時効処理は５００〜７００℃で少くとも０．５時間
保持し、急冷することで良い。５００℃未満では効果が
少なく７００℃を越えると磁気特性の低下が生じるから
である。The aging treatment may be carried out by holding at 500 to 700°C for at least 0.5 hours and then rapidly cooling. This is because if the temperature is less than 500°C, the effect will be small, and if it exceeds 700°C, the magnetic properties will deteriorate.
次に本発明を適用する希土類・ボロン・鉄系永久磁石の
成分限定理由について説明すると、本発明の磁石は希土
類元素Ｒ（但しＲはＹを含む希土類元素の少くとも１種
）、ボロンおよび鉄を必須元素とする。さらに詳述する
と、Ｒとしてはネオジム（Ｎｄ） 、プラセオジム（Ｐ
ｒ ）またはそれらの混合物（ジジム）が好ましく、他
にランタン（Ｌａ）。Next, to explain the reason for limiting the components of the rare earth/boron/iron permanent magnet to which the present invention is applied, the magnet of the present invention contains the rare earth element R (where R is at least one rare earth element including Y), boron, and iron. is an essential element. To explain in more detail, R is neodymium (Nd), praseodymium (P
r) or mixtures thereof (didim), and also lanthanum (La).
セリウム（Ｃｅ） 、テルビウム（Ｔｂ） 、ジスプロ
シウム（Ｄｙ） 、ホルミウム（Ｈｏ）、エルビウム（
Ｅｒ）、サマリウム（Ｓｍ） 、カドリニウム（Ｇｄ）
及びイツトリウム（Ｙ）などの希土類元素を含Ｘ７で良
く、総量で８〜３０原子チとされる。８原子チ未満では
十分な保磁力が得られず、３０原子チを越えると、残留
磁束密度が低下するためである□ボロンＢは２〜２８原
子チとされる。２原子チ未満では十分な保磁力が得られ
ず、２８原子チを越えると残留磁束密度が低下し優れた
磁気特性が得られないためである。上記ＲおよびＢ以外
の元素としてＦｅは必須であり４０〜９０原子チ含有さ
れる。Cerium (Ce), Terbium (Tb), Dysprosium (Dy), Holmium (Ho), Erbium (
Er), samarium (Sm), cadrinium (Gd)
It may contain rare earth elements such as yttrium (Y) and yttrium (Y), and the total amount is 8 to 30 atoms. If it is less than 8 atoms, a sufficient coercive force cannot be obtained, and if it exceeds 30 atoms, the residual magnetic flux density will decrease. This is because if it is less than 2 atoms, a sufficient coercive force cannot be obtained, and if it exceeds 28 atoms, the residual magnetic flux density decreases and excellent magnetic properties cannot be obtained. Fe is essential as an element other than R and B, and is contained in an amount of 40 to 90 atoms.
４０原子チ未満では残留磁束密度（Ｂｒ）が低下し、９
０原子チを越えると高い保磁力（ｉＨｃ ）が得られな
いためである。Below 40 atoms, the residual magnetic flux density (Br) decreases, and 9
This is because if it exceeds 0 atoms, a high coercive force (iHc) cannot be obtained.
次に本発明の実施例について説明するが、本発明はこれ
ら実施例に限定されるものではない０〔実施例〕
実施例１
第１表の組成となるよう溶解し、合金インゴットを得た
。合金インゴットをショークラッシャー。Next, examples of the present invention will be described, but the present invention is not limited to these examples.0 [Example] Example 1 An alloy ingot was obtained by melting so as to have the composition shown in Table 1. Show crusher for alloy ingots.
ブラウンミル、ジェット・ミルを用いて平均粒径３．５
μｍの微粉とし、原料粉とした０得られた原料粉を、成
形圧２ 、７ Ｖｄで磁揚中（１０ＫＯｅ）成形し、得
られた成形体を真空中（１０−”Ｔｏｒｒ ）で、１０
８０℃×２時間の焼結後炉冷し、再度６３０℃×１時間
の熱処理後、急冷し磁気特性の評価に供した。結果を第
２表に示す０第１表に見る如＜ Ｎｂ無添加（ＡＩ 、
５ 、 ｉｏ ）に比較し、冷を添加することにより
、著しく保磁力（ｉＨｃ）が向上することが分る。また
、金相学的には隅とＣの共存の場合、ＮｂＣの形成と存
在が、認められた。Average particle size 3.5 using brown mill, jet mill
The obtained raw material powder was made into a fine powder of μm and used as raw material powder. The obtained raw material powder was molded during magnetic lifting (10 KOe) at a molding pressure of 2.7 Vd, and the obtained molded body was molded in a vacuum (10-" Torr) for 10
After sintering at 80° C. for 2 hours, it was cooled in a furnace, heat treated again at 630° C. for 1 hour, and then rapidly cooled to evaluate magnetic properties. The results are shown in Table 2.0 As shown in Table 1, Nb-free (AI,
5, io), it can be seen that the coercive force (iHc) is significantly improved by adding cold. Moreover, metallographically, in the case of coexistence of corner and C, the formation and existence of NbC was recognized.
第 １ 表
実施例２
第３表に示す組成となるように溶解し、実施例１と同様
に成形、焼結、熱処理を行い、磁気特性の評価に供し丸
。結果を、第４表に示す。Table 1 Example 2 A circle was melted to have the composition shown in Table 3, molded, sintered, and heat treated in the same manner as in Example 1, and subjected to evaluation of magnetic properties. The results are shown in Table 4.
Ｔｉ＊ Ｚｒ ｒ Ｈｆの場合にても、それらの炭化物
の形成が認められた。The formation of these carbides was also observed in the case of Ti*Zr r Hf.
第２表
第 ６ 表
第 ４ 表
〔発明の効果〕
以上述べた如く、本発明は、ＣとＮｂ ｒ Ｔｉ、Ｚｒ
。Table 2, Table 6, Table 4 [Effects of the invention] As stated above, the present invention provides the following advantages:
.
Claims (1)
の内少くとも１種とＬａ、Ｃｅ、Ｓｍ、Ｇｄ、Ｅｒ、Ｙ
の内少くとも１種、２〜２８％のＢ、０．０２〜２％の
Ｃおよび残部Ｆｅと不純物から成る焼結磁石において添
加元素Ｍ（Ｎｂ、Ｔｉ、Ｚｒ、Ｈｆの内少くとも１種）
の量（ｙ）が、Ｃの量（ｘ）に対し、 ｘ≦ｙ≦（ｘ＋４）の範囲であることを、特徴とする永
久磁石。[Claims] 8 to 30% Nd, Pr, Dy, Ho, Tb in atomic %
At least one of the following and La, Ce, Sm, Gd, Er, Y
Additive element M (at least one of Nb, Ti, Zr, Hf) in a sintered magnet consisting of at least one of the following, 2 to 28% B, 0.02 to 2% C, and the balance Fe and impurities. )
A permanent magnet characterized in that the amount (y) of C is in the range of x≦y≦(x+4) with respect to the amount (x) of C.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61023228A JPS62181403A (en) | 1986-02-05 | 1986-02-05 | Permanent magnet |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61023228A JPS62181403A (en) | 1986-02-05 | 1986-02-05 | Permanent magnet |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS62181403A true JPS62181403A (en) | 1987-08-08 |
Family
ID=12104767
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP61023228A Pending JPS62181403A (en) | 1986-02-05 | 1986-02-05 | Permanent magnet |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS62181403A (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0260105A (en) * | 1988-08-26 | 1990-02-28 | Shin Etsu Chem Co Ltd | Rare-earth permanent magnet |
| US5085716A (en) * | 1990-02-20 | 1992-02-04 | General Motors Corporation | Hot worked rare earth-iron-carbon magnets |
| EP0571002A2 (en) † | 1989-08-25 | 1993-11-24 | Dowa Mining Co., Ltd. | Permanent magnet alloy having improved resistance to oxidation and process for production thereof |
| US5376291A (en) * | 1993-01-29 | 1994-12-27 | Ici Japan Limited | Bonded magnet molding composition and bonded magnet |
| CN102304663A (en) * | 2011-09-20 | 2012-01-04 | 浙江大学 | Permanent magnetic alloy block and preparation method thereof |
-
1986
- 1986-02-05 JP JP61023228A patent/JPS62181403A/en active Pending
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0260105A (en) * | 1988-08-26 | 1990-02-28 | Shin Etsu Chem Co Ltd | Rare-earth permanent magnet |
| EP0571002A2 (en) † | 1989-08-25 | 1993-11-24 | Dowa Mining Co., Ltd. | Permanent magnet alloy having improved resistance to oxidation and process for production thereof |
| EP0571002B2 (en) † | 1989-08-25 | 2003-01-02 | Dowa Mining Co., Ltd. | Permanent magnet alloy having improved resistance to oxidation and process for production thereof |
| US5085716A (en) * | 1990-02-20 | 1992-02-04 | General Motors Corporation | Hot worked rare earth-iron-carbon magnets |
| US5376291A (en) * | 1993-01-29 | 1994-12-27 | Ici Japan Limited | Bonded magnet molding composition and bonded magnet |
| CN102304663A (en) * | 2011-09-20 | 2012-01-04 | 浙江大学 | Permanent magnetic alloy block and preparation method thereof |
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