JPS63255902A - R-b-fe sintered magnet and manufacture thereof - Google Patents
R-b-fe sintered magnet and manufacture thereofInfo
- Publication number
- JPS63255902A JPS63255902A JP62090355A JP9035587A JPS63255902A JP S63255902 A JPS63255902 A JP S63255902A JP 62090355 A JP62090355 A JP 62090355A JP 9035587 A JP9035587 A JP 9035587A JP S63255902 A JPS63255902 A JP S63255902A
- Authority
- JP
- Japan
- Prior art keywords
- rare earth
- sintered
- sintered magnet
- mixed
- powder
- 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
- 238000004519 manufacturing process Methods 0.000 title claims description 6
- 239000000843 powder Substances 0.000 claims abstract description 14
- 229910052761 rare earth metal Inorganic materials 0.000 claims abstract description 13
- 229910052742 iron Inorganic materials 0.000 claims abstract description 7
- 229910052796 boron Inorganic materials 0.000 claims abstract description 6
- 239000011812 mixed powder Substances 0.000 claims abstract description 6
- 101100274801 Caenorhabditis elegans dyf-3 gene Proteins 0.000 claims abstract description 5
- 229910000640 Fe alloy Inorganic materials 0.000 claims abstract description 4
- PXGOKWXKJXAPGV-UHFFFAOYSA-N Fluorine Chemical compound FF PXGOKWXKJXAPGV-UHFFFAOYSA-N 0.000 claims abstract description 4
- 229910052731 fluorine Inorganic materials 0.000 claims abstract description 4
- 239000011737 fluorine Substances 0.000 claims abstract description 4
- 229910052736 halogen Inorganic materials 0.000 claims abstract description 4
- 150000002367 halogens Chemical class 0.000 claims abstract description 4
- 238000010438 heat treatment Methods 0.000 claims description 9
- 238000005245 sintering Methods 0.000 claims description 9
- 238000000034 method Methods 0.000 claims description 6
- 239000000203 mixture Substances 0.000 claims description 4
- -1 rare earth fluorides Chemical class 0.000 claims description 3
- 230000004907 flux Effects 0.000 abstract description 6
- KRHYYFGTRYWZRS-UHFFFAOYSA-M Fluoride anion Chemical compound [F-] KRHYYFGTRYWZRS-UHFFFAOYSA-M 0.000 abstract description 4
- 229910017557 NdF3 Inorganic materials 0.000 abstract description 4
- 229910016468 DyF3 Inorganic materials 0.000 abstract description 3
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 17
- 230000000694 effects Effects 0.000 description 6
- 229910045601 alloy Inorganic materials 0.000 description 5
- 239000000956 alloy Substances 0.000 description 5
- 238000011282 treatment Methods 0.000 description 5
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 4
- 230000032683 aging Effects 0.000 description 4
- 230000007423 decrease Effects 0.000 description 4
- 230000001590 oxidative effect Effects 0.000 description 4
- 239000011261 inert gas Substances 0.000 description 3
- 150000002910 rare earth metals Chemical class 0.000 description 3
- 239000002994 raw material Substances 0.000 description 3
- 229910052723 transition metal Inorganic materials 0.000 description 3
- 229910052692 Dysprosium Inorganic materials 0.000 description 2
- 229910052779 Neodymium Inorganic materials 0.000 description 2
- 229910052772 Samarium Inorganic materials 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 238000000465 moulding Methods 0.000 description 2
- 239000002245 particle 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
- 229910052689 Holmium Inorganic materials 0.000 description 1
- 229910052765 Lutetium Inorganic materials 0.000 description 1
- 229910052777 Praseodymium Inorganic materials 0.000 description 1
- 229910052773 Promethium 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
- 229910052799 carbon Inorganic materials 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
- 239000002131 composite material Substances 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 238000007596 consolidation process Methods 0.000 description 1
- 230000009089 cytolysis Effects 0.000 description 1
- 238000007872 degassing Methods 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
- OGPBJKLSAFTDLK-UHFFFAOYSA-N europium atom Chemical compound [Eu] OGPBJKLSAFTDLK-UHFFFAOYSA-N 0.000 description 1
- 150000002222 fluorine compounds Chemical class 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- KJZYNXUDTRRSPN-UHFFFAOYSA-N holmium atom Chemical compound [Ho] KJZYNXUDTRRSPN-UHFFFAOYSA-N 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 238000000462 isostatic pressing Methods 0.000 description 1
- 229910052746 lanthanum Inorganic materials 0.000 description 1
- FZLIPJUXYLNCLC-UHFFFAOYSA-N lanthanum atom Chemical compound [La] FZLIPJUXYLNCLC-UHFFFAOYSA-N 0.000 description 1
- OHSVLFRHMCKCQY-UHFFFAOYSA-N lutetium atom Chemical compound [Lu] OHSVLFRHMCKCQY-UHFFFAOYSA-N 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- QEFYFXOXNSNQGX-UHFFFAOYSA-N neodymium atom Chemical group [Nd] QEFYFXOXNSNQGX-UHFFFAOYSA-N 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- PUDIUYLPXJFUGB-UHFFFAOYSA-N praseodymium atom Chemical compound [Pr] PUDIUYLPXJFUGB-UHFFFAOYSA-N 0.000 description 1
- VQMWBBYLQSCNPO-UHFFFAOYSA-N promethium atom Chemical compound [Pm] VQMWBBYLQSCNPO-UHFFFAOYSA-N 0.000 description 1
- 229910001404 rare earth metal oxide Inorganic materials 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
- FRNOGLGSGLTDKL-UHFFFAOYSA-N thulium atom Chemical compound [Tm] FRNOGLGSGLTDKL-UHFFFAOYSA-N 0.000 description 1
- 150000003624 transition metals Chemical class 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- NAWDYIZEMPQZHO-UHFFFAOYSA-N ytterbium Chemical compound [Yb] NAWDYIZEMPQZHO-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
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、弗化物を添
加することにより磁気特性を改善したものである。DETAILED DESCRIPTION OF THE INVENTION [Industrial Application Field] The present invention is an R-B-Fe sintered magnet whose magnetic properties are improved by adding fluoride.
近年、従来のＳｏ −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
。（俵用ほか、Ｊ、Ａｐｐｌ、Ｐｈｙｓ、５５（６１，
１５Ｍａｒｃｈ１９８４、 Ｐ２Ｏ８３〜２０８７、お
よび特開昭５９−４６００８号公報、同６０−１８２１
０４号公報参照）それらによれば、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、さらに焼結および
熱処理することが開示されている。In recent years, Nd-B-Fe permanent magnets have been invented that have higher magnetic properties than conventional So-Co magnets and do not necessarily contain Sm or Co, which are expensive resources. It was done. (Bale use, etc., J, Appl, Phys, 55 (61,
15March1984, P2O83-2087, and JP-A-59-46008, JP-A-60-1821
According to them, as a manufacturing method, an alloy ingot obtained by melting and casting is crushed, press-formed while applying a magnetic field as necessary, and further sintered and heat-treated. There is.
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、十分満足のできる磁気特性が得られるには、至
ってない。However, with these conventional manufacturing methods, it has not been possible to obtain sufficiently satisfactory magnetic properties.
本発明は上述した従来技術の問題点を解消し、磁気特性
の優れたＲ−Ｂ−Ｆｅ系焼結磁石およびその製造方法を
、提供することを目的とするものである。It is an object of the present invention to solve the above-mentioned problems of the prior art and to provide an R-B-Fe sintered magnet with excellent magnetic properties and a method for manufacturing the same.
すなわち本発明はＲ（但しＲはＹを含む希土類元素の内
、少くとも１種）、ＢおよびＦｅを必須成分とするＲ−
Ｂ−Ｆｅ系合金粉またはそれと同組成となる混合粉にさ
らに希土類フッ化物ＮｄＦ、、 ＤＹＦ３の内、少（と
も１種を配合し、混合、成形、焼結および熱処理を行う
ことを特徴とするものである。That is, the present invention provides an R-
B-Fe alloy powder or mixed powder having the same composition is further blended with at least one of the rare earth fluorides NdF, DYF3, and mixed, molded, sintered and heat treated. It is something.
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系合金粉またはそれと同組成となり得る
混合粉が準備される。例えば、溶解。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, lysis.
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。上記合金粉の少くとも一
部をＦｅを代表とする遷移金属粉、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を使用しても本
発明の効果は失なわれない。The alloy powder is produced by a method of 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. At least a part of the above alloy powder was replaced with one or more of transition metal powder represented by Fe, boron powder, rare earth metal powder, B-transition metal alloy powder, R-transition metal alloy powder, etc. Even if a mixed powder is used, the effects of the present invention are not lost.
なお、希土類フッ化物ＮｄＦｉ、 ＤｙＦ３の内掛くと
も１種は焼結および熱処理後の製品に、ハロゲン元素フ
ッ素（Ｆ）が、重■％にて０．００１〜０．８シロ含有
されるように、配合添加される。０．００１％未満およ
び０．８％を越えると、効果が少いことと磁気特性が低
下するため０．００１〜０．８ｗｔ％とされる。In addition, at least one of the rare earth fluorides NdFi and DyF3 contains the halogen element fluorine (F) by weight of 0.001 to 0.8 sigma in the product after sintering and heat treatment. It is mixed and added to. If it is less than 0.001% or more than 0.8%, the effect will be small and the magnetic properties will deteriorate, so it is set at 0.001 to 0.8 wt%.
上記方法にて得られた混合粉を圧縮プレスなどにて成形
−圧密化を行う。）（ＩＰ等の１益間静水圧成形も可能
である。The mixed powder obtained by the above method is molded and compacted using a compression press or the like. ) (Isostatic pressing such as IP is also possible.
なお、上記成形−圧密化は、０．５〜Ｌｏｔ／ｃｔｄの
成形圧力が良く、必要に応じ成形時において、磁界（５
ＫＯｅ以上）を印加することにより、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９０
０〜１２００°Ｃの温度にて焼結する。９００℃未満で
は、宙度があがらないためＢｒが十分でなく１２００’
ｃを越えるとＢｒおよび角形性が低下する理由による。In the above molding-consolidation, a molding pressure of 0.5 to Lot/ctd is good, and if necessary, a magnetic field (5
By applying KOe or more), the magnetic properties are improved. 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 90
Sinter at a temperature of 0 to 1200°C. If the temperature is less than 900°C, the degree of inertia will not increase and Br will not be sufficient, resulting in a temperature of 1200'
This is because if it exceeds c, Br and squareness decrease.
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、真空または不活性
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°Ｃ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。Sintering is preferably performed in a non-oxidizing atmosphere to prevent oxidation of the R element. That is, a vacuum or an inert gas atmosphere is preferable. The rate of temperature increase from room temperature during sintering is not particularly specified, but the temperature uniformity of the heated part can be improved by maintaining the temperature in the range of 200 to 800 °C for at least 0.5 hours during the temperature increase. Alternatively, it becomes possible to perform degassing treatment in a vacuum.
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）などの非酸化性雰囲気が良い。Therefore, the atmosphere for sintering is preferably a non-oxidizing atmosphere such as vacuum or an inert gas (eg Ar).
加熱保持後の冷却速度は、特に規定しないが、０゜１〜
ｂ
は０．２〜ｂ
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、５
００°Ｃ位迄行い、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。The cooling rate after heating and holding is not particularly specified, but it is 0°1~
This is because the variation in magnetic properties due to b being 0.2 to b is reduced. It is also good to cool down to room temperature once, or
Sintering and heat treatment may be performed continuously, such that the temperature is raised to about 00°C and the temperature is raised 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、ａ：要に応じ時効
処理前に８００〜１０００°Ｃで保持−徐冷という中間
熱処理を行うことにより一層ｆｎ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 a: If necessary, an intermediate heat treatment of holding and slow cooling at 800 to 1000°C is performed before the aging treatment to further improve the fn properties. Heat treatments such as aging treatment and intermediate heat treatment are the same as the sintering described above.
A non-oxidizing atmosphere is preferred.
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 ’Ｃを越えると磁気特性の低下が生
じるからである。Note that 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 there is little effect below 500°C, and above 700'C the magnetic properties deteriorate.
次に本発明を適用する希土類・ボロン・鉄系焼結磁石の
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（ただし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どする。さらに詳述す
ると、Ｒとしてはネオジム（Ｎｄ） 、プラセオジム（
Ｐｒ）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）、セリウム（Ｃｅ） 、テルビウム
（Ｔｂ）、 ジスプロシウム（Ｄｙ） 、ホルミウム（
Ｊｉｏ）、エルビウム（Ｅｒ）。Next, to explain the reason for limiting the components of the rare earth/boron/iron sintered 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 of the rare earth elements including Y).
species), boron and iron as essential elements. To explain in more detail, R is neodymium (Nd), praseodymium (
Pr) or a mixture thereof (didim) is preferred; other examples include lanthanum (La), cerium (Ce), terbium (Tb), dysprosium (Dy), and holmium (
Jio), erbium (Er).
ユウロピウム（Ｅｕ） 、サマリウム（Ｓｍ） 、カド
リニウム（Ｇｄ）、プロメチウム（Ｐｍ）、ツリウム（
Ｔｍ）、イッテルビウム（Ｙｂ）、ルテチウム（Ｌｕ）
及びイソトリウム（Ｙ）などの希土類元素を含んで良く
、総量で８〜３０原子％とされる。８原子％未満では十
分な保磁力が得られず、３０原子％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
％とされる。２原子％未満では十分な保磁力が得られず
、２８原子％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は必須元素であり４０〜９０原子％含有
される。Europium (Eu), samarium (Sm), cadrinium (Gd), promethium (Pm), thulium (
Tm), ytterbium (Yb), lutetium (Lu)
and rare earth elements such as isotrium (Y), in a total amount of 8 to 30 at.%. This is because if it is less than 8 atomic %, sufficient coercive force cannot be obtained, and if it exceeds 30 atomic %, the residual magnetic flux density decreases. Boron B is contained in an amount of 2 to 28 atomic %. This is because if it is less than 2 atomic %, a sufficient coercive force cannot be obtained, and if it exceeds 28 atomic %, the residual magnetic flux density decreases and excellent magnetic properties cannot be obtained. Fe is an essential element other than R and B, and is contained in an amount of 40 to 90 atomic %.
４０原子％未満では残留磁束密度（Ｂｒ）が低下、
し、９０原子％を越えると高い保磁力（ｉｌｌｃ）が得
られないためである。If it is less than 40 at%, the residual magnetic flux density (Br) decreases,
However, if it exceeds 90 atomic %, a high coercive force (ILLC) cannot be obtained.
上記Ｒ−ＢおよびＦｅを必須元素とし、希土類・ボロン
・鉄系焼結磁石は作成されるが下記の如く、鉄の一部を
他の元素で置換することや、不純物を含んでも本発明の
効果は失なわれない。Rare earth/boron/iron based sintered magnets can be created using the above R-B and Fe as essential elements, but as described below, even if some of the iron is replaced with other elements or even if impurities are included, the present invention will still work. The effect will not be lost.
すなわち、Ｆｅ０代りに、５０原子％以下のＣｏ。That is, 50 atomic % or less of Co is used instead of Fe0.
８原子％以下のＮｉで代替しても良い。Ｃｏは５０原子
％を越えると高いｉＨｃが得られず、Ｎｉは８％を越え
ると高いＢｒが得られないためである。また上記以外の
元素として下記所定原子％以下のＡ元素の１種以上（た
だし、２種以上含む場合のＡ元素の総量は当該含有Ａ元
素の内最大値を有するものの値以下）をＦｅ元素と置換
しても本発明の効果は失なわれない。Ａ元素を下記する
。It may be replaced with 8 atomic % or less of Ni. This is because if Co exceeds 50 atomic %, high iHc cannot be obtained, and if Ni exceeds 8 atomic %, high Br cannot be obtained. In addition, as elements other than the above, one or more of the A elements below the specified atomic % (however, if two or more types are included, the total amount of A elements is less than or equal to the value of the maximum value of the contained A elements) is considered to be Fe element. Even if substituted, the effects of the present invention will not be lost. Element A is shown below.
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。Next, examples of the present invention will be described, but the present invention is not limited to these examples.
実施例１
第１表の如＜ 、ＮｄＦｚを配合添加し、重量％にて３
３８ｄ １．ＩＢ−（ｘ）Ｆ−残Ｆｅの焼結体が得ら
れるよう原料粉（平均粒径３．１μｍ）を作成した。Example 1 As shown in Table 1, NdFz was mixed and added at a weight percent of 3.
38d 1. Raw material powder (average particle size: 3.1 μm) was prepared so as to obtain a sintered body of IB-(x)F-remaining Fe.
得られた原料粉を２ｔ／ａ１１で磁場中（８ＫＯｅ）で
成形し、得られた成形体を真空中（１０−’Ｔｏｒｒ）
で、１０５０℃×２時間の焼結後、炉冷し、再度６４０
℃×１時間の熱処理後、急冷し磁気特性の測定に供した
。The obtained raw material powder was molded at 2t/a11 in a magnetic field (8KOe), and the resulting molded body was molded in a vacuum (10-'Torr).
After sintering at 1050°C for 2 hours, it was cooled in the furnace and sintered at 640°C again.
After heat treatment at °C for 1 hour, it was rapidly cooled and subjected to measurement of magnetic properties.
得られた製品の磁気特性値を第１表に示す。Table 1 shows the magnetic property values of the obtained product.
第１表に見る如く、Ｆの無添加材（階１）に比較しＦ含
有材（患２〜６）の磁気特性が優れていることが分る。As shown in Table 1, it can be seen that the magnetic properties of the F-containing materials (Cases 2 to 6) are superior to the F-free materials (Scope 1).
しかし、過度の添加量では、阻７の如く磁気特性は低下
する。However, if the amount added is excessive, the magnetic properties will deteriorate as shown in Example 7.
実施例２
第２表の如＜ 、）ｌｄＦ、およびＤｙＦ、を配合添加
し、重量％にて、３ＯＮｄ−１，０Ｂ−３，５Ｄｙ−（
ｘ）Ｆ−残Ｆｅの焼結体が得られるよう原料粉（平均粒
径３，５μｍ）を作成し、以後、実施例１と同様に行っ
た結果を第２表に示す。Example 2 As shown in Table 2, 3ONd-1,0B-3,5Dy-(3ONd-1,0B-3,5Dy-(
x) A raw material powder (average particle size 3.5 μm) was prepared so as to obtain a sintered body of F-residue Fe, and the same procedure as in Example 1 was carried out. The results are shown in Table 2.
ＮｄＦ２およびＤｙｔ’Ｈの複合添加においてもＦ添加
による磁気特性の向上が認められる。Even in the combined addition of NdF2 and Dyt'H, the magnetic properties are improved by the addition of F.
第１表でのＮｄＦ３単独、第２表でのＮｄＦ３． Ｄｙ
Ｆ：＋の複合配合した場合に見る如く、磁気特性（Ｂｒ
、１ｌｌｃおよび（Ｂ１１）ＭＡＸ）を著しく向上させ
ることがわかる。NdF3 alone in Table 1, NdF3 in Table 2. Dy
As seen in the case of F:+ composite blending, the magnetic properties (Br
, 1llc and (B11)MAX).
（発明の効果）
Ｄｙ、 Ｎｄの弗化物の添加により残留磁束密度（Ｂｒ
）。(Effect of the invention) By adding Dy and Nd fluorides, the residual magnetic flux density (Br
).
保磁力（ｉ ｔ（ｃ ） 、最大エネルギー積（ＢＨｎ
＋ａｘ＋ ）などの磁気特性を著しく向上する。従って
、サーボモーター等の減磁界が作用する用途に適するだ
けでなく、Ｖ、Ｃ，Ｍｏ等の高磁束量を要求される用途
にも好適である。coercive force (it(c)), maximum energy product (BHn
+ax+) and other magnetic properties are significantly improved. Therefore, it is suitable not only for applications such as servo motors where a demagnetizing field acts, but also for applications that require a high amount of magnetic flux such as V, C, Mo, etc.
Claims (1)
種）、ＢおよびＦｅを必須成分とするＲ−Ｂ−Ｆｅ系合
金粉または、それと同組成となる混合粉に希土類フッ化
物ＮｄＦ＿３、ＤｙＦ＿３の内、少くとも１種を配合し
、混合、成形、焼結および熱処理することを特徴とする
Ｒ−Ｂ−Ｆｅ系焼結磁石の製造方法。 ２、ハロゲン元素フッ素（Ｆ）が重量％にて０．００１
〜０．８％含有されることを特徴とする特許請求の範囲
第１項記載の製造方法。 ３、ハロゲン元素フッ素（Ｆ）が、重量％にて０．００
１〜０．８％含有することを特徴とするＲ−Ｂ−Ｆｅ系
焼結磁石。[Claims] 1. R (where R is at least one rare earth element including Y)
At least one of the rare earth fluorides NdF_3 and DyF_3 is blended with R-B-Fe alloy powder containing B and Fe as essential components, or a mixed powder with the same composition, mixed, molded, A method for manufacturing an R-B-Fe sintered magnet, which comprises sintering and heat treatment. 2. Halogen element fluorine (F) is 0.001% by weight
The manufacturing method according to claim 1, characterized in that the content is 0.8% to 0.8%. 3. Halogen element fluorine (F) is 0.00% by weight
An R-B-Fe-based sintered magnet characterized by containing 1 to 0.8%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62090355A JPS63255902A (en) | 1987-04-13 | 1987-04-13 | R-b-fe sintered magnet and manufacture thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62090355A JPS63255902A (en) | 1987-04-13 | 1987-04-13 | R-b-fe sintered magnet and manufacture thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS63255902A true JPS63255902A (en) | 1988-10-24 |
Family
ID=13996225
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP62090355A Pending JPS63255902A (en) | 1987-04-13 | 1987-04-13 | R-b-fe sintered magnet and manufacture thereof |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS63255902A (en) |
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1987
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