JPH0580121B2 - - Google Patents
Info
- Publication number
- JPH0580121B2 JPH0580121B2 JP59262268A JP26226884A JPH0580121B2 JP H0580121 B2 JPH0580121 B2 JP H0580121B2 JP 59262268 A JP59262268 A JP 59262268A JP 26226884 A JP26226884 A JP 26226884A JP H0580121 B2 JPH0580121 B2 JP H0580121B2
- Authority
- JP
- Japan
- Prior art keywords
- processing
- sintering
- aging
- magnetic properties
- 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.)
- Expired - Lifetime
Links
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)
- Manufacturing Of Steel Electrode Plates (AREA)
- Hard Magnetic Materials (AREA)
Description
（産業上の利用分野）
本発明はNd−Fe−Ｂ組成の希土類永久磁石の
製造方法に関するものである。
（従来の技術）
希土類遷移金属合金において希土類金属と遷移
金属の比が２：17である金属間化合物が理論的に
極めて高い磁気特性［（BH）max〜50MGOe］
を有することが発見されて以来、同系化合物を主
体とする永久磁石実用合金を得る試みが種々実験
されてきた。その一例としてSm−Co−Cu−Fe
系金属間化合物で（BH）max〜30MGOeが達成
され、さらにNd−Fe系金属間化合物で（BH）
max〜40MGOeの高磁気特性が得られている。
この組成合金は粉砕、磁場中配向圧縮成形あるい
は非磁場中圧縮成形、焼結、溶体化、時効するこ
とによりバルク化し、研削、研磨加工して所望の
実用形状を有する永久磁石を得る製造方法が一般
的であつた。
（発明が解決しようとする課題）
しかしながらこのような焼結、溶体化、時効す
ることにより最終的な磁気特性を得てから、実用
形状を得るために研削、研磨加工を行なうと、加
工された表面層に加工歪が発生し、その表面層の
磁気特性が加工劣化することにより、全体の磁気
特性に影響をおよぼし、その減磁曲線が第１図−
Ａに示すように変形することが判明した。この現
象は、特に体積が小であり表面積の大なる永久磁
石に顕著に現われ、歩留低下の一因となつてい
た。
本発明は、この点を鑑みて加工歪による表面層
の磁気特性の劣化を改善することを目的とする。
（問題点を解決するための手段）
本発明は、Nd−Fe−Ｂ組成の希土類永久磁石
の磁気特性において特に表面層の保磁力が加工歪
により劣化し、また保磁性は時効工程に大きく依
存することを考慮して、最終的な磁気特性が得ら
れる以前の工程、すなわち焼結後において、研
削、研磨加工を行なうことにより、その加工歪を
その後の時効工程において除去するものである。
本発明の主旨を実現する方法は、基本的には
NdFeB系合金において、圧縮成形された生材を
焼結後、実用に供する形状に加工し、加工後に
500〜1200℃の温度で加熱処理することによつて
加工歪を除去する工程から構成される。本発明の
最も効果的な製造手順は下記〜に示す工程か
ら実施される。
焼結→加工→500〜900℃時効
焼結→加工→900〜1150℃溶体化→500〜900
℃時効
焼結→加工→1000〜1200℃再焼結。
〜のいずれの手順においても十分な効果が
得られるが、角型性、保磁力とも最大限に発揮さ
せるには、の手順が最も有効であり、、が
それに準ずる。温度の限定理由は、いずれも加工
歪層の除去と保磁力の成長促進度合から決定され
る。すなわち焼結、溶体化、時効の各処理の適性
温度範囲として、それぞれ1000〜1200℃、900〜
1150℃、500〜900℃の領域が制限され、各々領域
外では磁気特性の劣化、加工歪層の不完全除去を
生じ本発明の効果を逸脱する。
以下、実施例を示し、さらに詳しく本発明につ
いて説明する。
（実施例）
Nd（Fe0.92B0.08）5.4の組成合金を溶解鋳造し、そ
のインゴツトを振動ミルにて５〜20μｍに微粉砕
した。この粉末を磁場中で圧縮した後、成形体を
真空雰囲気において1120℃、１時間焼結し炉冷し
た。得られた焼結体をＡ，Ｂに分けた。次いでＡ
は従来の製造方法により、1100℃、１時間溶体化
処理して、600℃、１時間で時効した後、研削加
工により１×１×５mmの寸法に成形した。Ｂは本
発明の製造方法により、焼結体を研削加工により
同一の寸法に成形した後、1100℃、１時間溶体化
処理して、600℃、１時間で時効した。Ａおよび
Ｂのそれぞれの永久磁石の磁気特性を測定したと
ころ、第１図に示す減磁曲線を得、Ａは湾曲した
曲線となり、Ｂは肩部のある角型性の良好な減磁
曲線となつた。主な磁気特性を第１表に示す。
(Industrial Application Field) The present invention relates to a method for producing a rare earth permanent magnet having a Nd-Fe-B composition. (Prior art) In a rare earth transition metal alloy, an intermetallic compound with a ratio of rare earth metal to transition metal of 2:17 has theoretically extremely high magnetic properties [(BH)max ~ 50 MGOe]
Since its discovery, various experiments have been conducted in an attempt to obtain a practical permanent magnet alloy mainly composed of similar compounds. For example, Sm−Co−Cu−Fe
(BH) max ~ 30 MGOe was achieved with intermetallic compounds based on Nd-Fe, and (BH) with intermetallic compounds based on Nd-Fe.
High magnetic properties of max~40MGOe have been obtained.
This compositional alloy is made into a bulk by crushing, oriented compression molding in a magnetic field or compression molding in a non-magnetic field, sintering, solution treatment, and aging, and then is ground and polished to obtain a permanent magnet with a desired practical shape. It was common. (Problem to be solved by the invention) However, if the final magnetic properties are obtained through such sintering, solution treatment, and aging, then grinding and polishing are performed to obtain a practical shape. Processing strain occurs in the surface layer, and the magnetic properties of the surface layer deteriorate due to processing, which affects the overall magnetic properties, and the demagnetization curve is shown in Figure 1.
It was found that the material was deformed as shown in A. This phenomenon is particularly noticeable in permanent magnets that have a small volume and a large surface area, and has been a cause of a decrease in yield. In view of this point, the present invention aims to improve the deterioration of the magnetic properties of the surface layer due to processing strain. (Means for Solving the Problems) The present invention solves the problem that in the magnetic properties of rare earth permanent magnets with a Nd-Fe-B composition, the coercive force of the surface layer in particular deteriorates due to processing strain, and that the coercive force greatly depends on the aging process. In consideration of this, grinding and polishing are performed before the final magnetic properties are obtained, that is, after sintering, so that the processing strain is removed in the subsequent aging step. The method of realizing the gist of the present invention is basically
For NdFeB alloys, compression molded green material is sintered and then processed into a shape that can be used for practical purposes.
It consists of a process of removing processing distortion by heat treatment at a temperature of 500 to 1200°C. The most effective manufacturing procedure of the present invention is carried out from the steps shown below. Sintering → processing → aging at 500-900℃ Sintering → processing → solution treatment at 900-1150℃ → 500-900
°C aging Sintering → Processing → Re-sintering at 1000-1200 °C. Sufficient effects can be obtained with any of the procedures in . . . , but in order to maximize both squareness and coercive force, the procedure in . . . is the most effective, and . The reasons for limiting the temperature are determined from the removal of the strained layer and the degree of promotion of coercive force growth. In other words, the appropriate temperature range for each treatment of sintering, solution treatment, and aging is 1000-1200℃ and 900-1200℃, respectively.
The regions of 1150° C. and 500 to 900° C. are restricted, and outside these regions, the magnetic properties deteriorate and the processed strain layer is incompletely removed, which deviates from the effects of the present invention. EXAMPLES Hereinafter, the present invention will be explained in more detail by showing examples. (Example) An alloy having a composition of Nd(Fe 0.92 B 0.08 ) 5.4 was melted and cast, and the ingot was pulverized to 5 to 20 μm using a vibration mill. After compressing this powder in a magnetic field, the compact was sintered at 1120° C. for 1 hour in a vacuum atmosphere and cooled in a furnace. The obtained sintered body was divided into A and B. Then A
was solution-treated at 1100°C for 1 hour, aged at 600°C for 1 hour, and then molded into a size of 1 x 1 x 5 mm by grinding using a conventional manufacturing method. B was formed by grinding a sintered body into the same size according to the manufacturing method of the present invention, and then solution-treated at 1100°C for 1 hour and aged at 600°C for 1 hour. When we measured the magnetic properties of each of the permanent magnets A and B, we obtained the demagnetization curves shown in Figure 1, where A was a curved curve and B was a demagnetization curve with a shoulder and good squareness. Summer. The main magnetic properties are shown in Table 1.
【表】
強度）
（発明の効果）
以上のように、本発明によりBr11KG以上、
iHc10〜20KOeのNd−Fe−Ｂ組成永久磁石につ
いて、研削、研磨加工による表面層の加工歪を時
効処理することにより、保磁性を向上させると共
に、加工歪を加熱することにより除去し、加工劣
化層の正常組織への回復を達成できる。[Table] Strength)
(Effect of the invention) As described above, according to the present invention, Br11KG or more,
For Nd-Fe-B composition permanent magnets with an iHc of 10 to 20 KOe, the coercivity is improved by aging the processing strain on the surface layer due to grinding and polishing, and the processing strain is removed by heating, resulting in processing deterioration. Restoration of the layer to normal tissue can be achieved.
第１図は、本発明の永久磁石の減磁曲線を従来
方法によるものと対比として示したものである。
Ａ：従来の製造方法による、焼結、溶体化、時
効、加工後の永久磁石。Ｂ：本発明の製造方法に
よる、焼結、加工、溶体化、時効後の永久磁石。
FIG. 1 shows the demagnetization curve of the permanent magnet of the present invention in comparison with that of a conventional method. A: Permanent magnet after sintering, solution treatment, aging, and processing by conventional manufacturing methods. B: Permanent magnet after sintering, processing, solution treatment, and aging according to the manufacturing method of the present invention.
Claims (1)
焼結後、実用形状に加工し、500〜900℃で時効処
理することを特徴とする永久磁石の製造方法。 ２ NdFeB組成合金において、1000〜1200℃で
焼結後、実用形状に加工し、900〜1150℃で溶体
化後、500〜900℃で時効処理することを特徴とす
る永久磁石の製造方法。 ３ NdFeB組成合金において、1000〜1200℃で
焼結後、実用形状に加工し、1000〜1200℃で再焼
結処理することを特徴とする永久磁石の製造方
法。[Claims] 1. A method for producing a permanent magnet, which comprises sintering an NdFeB composition alloy at 1000 to 1200°C, processing it into a practical shape, and subjecting it to aging treatment at 500 to 900°C. 2. A method for producing a permanent magnet using an NdFeB composition alloy, which comprises sintering it at 1000 to 1200°C, processing it into a practical shape, solutionizing it at 900 to 1150°C, and aging it at 500 to 900°C. 3. A method for producing a permanent magnet using an NdFeB composition alloy, which comprises sintering it at 1000 to 1200°C, processing it into a practical shape, and re-sintering it at 1000 to 1200°C.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP59262268A JPS61140108A (en) | 1984-12-12 | 1984-12-12 | Manufacture of permanent magnet |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP59262268A JPS61140108A (en) | 1984-12-12 | 1984-12-12 | Manufacture of permanent magnet |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS61140108A JPS61140108A (en) | 1986-06-27 |
| JPH0580121B2 true JPH0580121B2 (en) | 1993-11-08 |
Family
ID=17373427
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP59262268A Granted JPS61140108A (en) | 1984-12-12 | 1984-12-12 | Manufacture of permanent magnet |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS61140108A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP7804266B1 (en) * | 2024-10-17 | 2026-01-22 | マグネデザイン株式会社 | Thin ring magnet and method of manufacturing thin ring magnet |
Families Citing this family (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6356624A (en) * | 1986-08-27 | 1988-03-11 | Hoya Corp | Faraday rotator and optical isolator |
| JP6079643B2 (en) * | 2012-02-03 | 2017-02-15 | 日産自動車株式会社 | Method and apparatus for manufacturing sintered magnet |
| JP6372088B2 (en) | 2013-03-29 | 2018-08-15 | 大同特殊鋼株式会社 | Method for producing RFeB magnet |
| CN109604618B (en) * | 2018-12-18 | 2022-06-10 | 宁波中杭磁材有限公司 | Preparation method of neodymium iron boron magnet with wear-resistant coating attached to surface |
| CN109692963B (en) * | 2018-12-18 | 2022-06-10 | 宁波中杭磁材有限公司 | Preparation method of neodymium iron boron magnet with corrosion-resistant coating attached to surface |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5432415A (en) * | 1977-08-15 | 1979-03-09 | Lion Corp | Preparation of hindered esters |
| JPS59217304A (en) * | 1983-05-25 | 1984-12-07 | Sumitomo Special Metals Co Ltd | Permanent magnet material and manufacture thereof |
-
1984
- 1984-12-12 JP JP59262268A patent/JPS61140108A/en active Granted
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP7804266B1 (en) * | 2024-10-17 | 2026-01-22 | マグネデザイン株式会社 | Thin ring magnet and method of manufacturing thin ring magnet |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS61140108A (en) | 1986-06-27 |
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