JPH01168844A - Permanent magnet material - Google Patents
Permanent magnet materialInfo
- Publication number
- JPH01168844A JPH01168844A JP62327821A JP32782187A JPH01168844A JP H01168844 A JPH01168844 A JP H01168844A JP 62327821 A JP62327821 A JP 62327821A JP 32782187 A JP32782187 A JP 32782187A JP H01168844 A JPH01168844 A JP H01168844A
- Authority
- JP
- Japan
- Prior art keywords
- permanent magnet
- magnet material
- rare earth
- earth elements
- composition
- 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
- 239000000463 material Substances 0.000 title claims abstract description 24
- 239000000203 mixture Substances 0.000 claims abstract description 16
- 229910052761 rare earth metal Inorganic materials 0.000 claims abstract description 7
- 229910052733 gallium Inorganic materials 0.000 claims abstract 2
- 230000005291 magnetic effect Effects 0.000 abstract description 12
- 229910045601 alloy Inorganic materials 0.000 abstract description 7
- 239000000956 alloy Substances 0.000 abstract description 7
- 229910052742 iron Inorganic materials 0.000 abstract description 2
- 238000004519 manufacturing process Methods 0.000 description 8
- 230000005294 ferromagnetic effect Effects 0.000 description 6
- 230000005415 magnetization Effects 0.000 description 6
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 5
- 238000000034 method Methods 0.000 description 4
- 239000013078 crystal Substances 0.000 description 3
- 239000010453 quartz Substances 0.000 description 3
- 238000010791 quenching Methods 0.000 description 3
- 230000000171 quenching effect Effects 0.000 description 3
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N silicon dioxide Inorganic materials O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 3
- 238000006467 substitution reaction Methods 0.000 description 3
- 229910052723 transition metal Inorganic materials 0.000 description 3
- 150000003624 transition metals Chemical class 0.000 description 3
- 230000006866 deterioration Effects 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 229910001172 neodymium magnet Inorganic materials 0.000 description 2
- 238000010298 pulverizing process Methods 0.000 description 2
- 238000005245 sintering Methods 0.000 description 2
- 229910001339 C alloy Inorganic materials 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 229910052797 bismuth Inorganic materials 0.000 description 1
- 230000015271 coagulation Effects 0.000 description 1
- 238000005345 coagulation Methods 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- RKTYLMNFRDHKIL-UHFFFAOYSA-N copper;5,10,15,20-tetraphenylporphyrin-22,24-diide Chemical compound [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 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000005347 demagnetization Effects 0.000 description 1
- 238000000280 densification Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 238000010790 dilution Methods 0.000 description 1
- 239000012895 dilution Substances 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000005284 excitation Effects 0.000 description 1
- 230000004907 flux Effects 0.000 description 1
- 229910001751 gemstone Inorganic materials 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 230000001939 inductive effect Effects 0.000 description 1
- 239000012770 industrial material Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 239000012768 molten material Substances 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 150000002910 rare earth metals Chemical class 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 230000000087 stabilizing effect Effects 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
- H01F1/058—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IVa elements, e.g. Gd2Fe14C
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Ｎｄ−Ｆｅ系永久磁石材料の合金組成に関する
ものである。DETAILED DESCRIPTION OF THE INVENTION [Field of Industrial Application] The present invention relates to an alloy composition of a Nd-Fe permanent magnet material.
［従来の技術］
Ｈｄ−Ｆｅ−Ｂ系材料を基本成分とする永久磁石が近年
工業化され、従来の５ｓ−Ｃｏ系材料を中心とする永久
磁石材料とともに今後の発展が予想されている。[Prior Art] Permanent magnets whose basic components are Hd-Fe-B-based materials have been industrialized in recent years, and future development is expected along with permanent magnet materials centered on conventional 5s-Co-based materials.
これまでに公開された技術背景は、製法的には５ｓ−Ｃ
ｏ系永久磁石の製造方法をそのまま利用する焼結法と、
ロール急冷等による非晶質物質を再結晶化し、それを原
料粉とする樹脂結合永久磁石またはその原料粉を再びホ
ットプレス。The technical background disclosed so far is that the manufacturing method is 5s-C.
A sintering method that uses the manufacturing method of o-based permanent magnets as is;
The amorphous material is recrystallized by quenching with rolls, etc., and then the resin-bonded permanent magnet or its raw material powder is hot-pressed again.
熱間圧延もしくはダイアップセット法により緻密化、磁
気異方性化する方法等があり、磁気特性的にも最大エネ
ルギー積で５〜４５８ＧＯｅまでカバーできる実用材料
となってきた。There are methods of densification and magnetic anisotropy by hot rolling or die-up setting, and it has become a practical material that can cover a maximum energy product of 5 to 458 GOe in terms of magnetic properties.
［発明が解決しようとする問題点］
従来の上記永久磁石材料は希土類−鉄以外の第三元素と
してＢを添加することにより、正方晶Ｒ２Ｆ８１４Ｂ化
合物を中心とする強磁性相を構成したもので、実際には
Ｒ２Ｆｅ１４Ｂ相よりＲ−リッチ側に組成を調合し、上
記Ｒ２Ｆｅ１４Ｂ相を希土類もしくはＢＦ２度の高い境
界相で分離させることによって、高保磁力を誘起した機
構からなっている。したがってさらに高い飽和磁束密度
材料を得るには、Ｒおよび８１１度の高い境界相を少な
くしなければならないが、これは保磁力の劣化を伴うた
め、結果として強磁性相を希釈することになり、さらに
高いＢｒ＠−得るには限界があった。[Problems to be Solved by the Invention] The above-mentioned conventional permanent magnet material constitutes a ferromagnetic phase centered on a tetragonal R2F814B compound by adding B as a third element other than rare earth-iron. In reality, the composition is more R-rich than the R2Fe14B phase, and the R2Fe14B phase is separated by a rare earth or boundary phase with a high BF2 degree, thereby inducing a high coercive force. Therefore, in order to obtain an even higher saturation magnetic flux density material, the boundary phase with high R and 811 degrees must be reduced, but this is accompanied by a deterioration of the coercive force, resulting in dilution of the ferromagnetic phase. There was a limit to obtaining even higher Br@-.
［問題点を解決するための手段］
本発明は、従来組成よりも高いＢｒを保有する永久磁石
材料を提供せんとするものである。すなわち一般式Ｒ（
Ｆｅ１−ｘ−ｙ ＣｏｘＭｙ） ２において、Ｒは希土
類元素９ＭはＣもしくはＣを主体とするＡ＃、Ｇａ、Ｇ
ｅ、Ｂｉ、ｐ、Ｓｉ、３から選択された１種もしくは２
種以上の元素との混合物からなり、０≦Ｘ≦０．６，０
．０４≦ｙ≦０．１５．６≦Ｚ≦１０の組成範囲で規定
されるとき具現化できる。これまでの公知技術ではＣを
包合する材料はなく、遷移金属と希土類元素の比が従来
のＮｄ−Ｆｅ−Ｂ系ではｚ −５〜６．５の領域に入っ
ていたのに対し、Ｂに置き換えてＣを使用するとき、ｌ
値が６≦Ｚ≦１０の遷移金属の濃度が高い側において実
用に供する保磁力を維持することを見い出した。[Means for Solving the Problems] The present invention aims to provide a permanent magnet material having a higher Br content than conventional compositions. That is, the general formula R (
Fe1-x-y CoxMy) 2, R is a rare earth element 9M is C or C-based A#, Ga, G
One or two selected from e, Bi, p, Si, 3
Consisting of a mixture of more than one species, 0≦X≦0.6,0
．． This can be realized when the composition range is defined as 04≦y≦0.15.6≦Z≦10. Until now, there is no material that encapsulates C in the known technology, and while the ratio of transition metal to rare earth element was in the range of z -5 to 6.5 in the conventional Nd-Fe-B system, B When using C instead of l
It has been found that a practically usable coercive force is maintained on the side where the concentration of transition metal is high, where the value is 6≦Z≦10.
すなわちＣを主体としたＲ−Ｆｅ−Ｃｏ−Ｃ合金におい
ては、非磁性である境界相が相対的に減少しても強磁性
相の磁気モーメントを安定化でき、その結果強磁性相が
増加したために飽和磁化の増加が確認され、その磁気特
性を生かした磁石動作点の高い（Ｂ／Ｈ＞１）応用分野
、たとえば円筒型マイクロモーター、ステッピングモー
ターなどにおいて、新規な工業材料として有望である。In other words, in the R-Fe-Co-C alloy mainly composed of C, the magnetic moment of the ferromagnetic phase can be stabilized even if the non-magnetic boundary phase is relatively reduced, and as a result, the ferromagnetic phase increases. An increase in saturation magnetization has been confirmed, and it is promising as a new industrial material in application fields where the magnet operating point is high (B/H > 1), such as cylindrical micromotors and stepping motors, making use of its magnetic properties.
本発明の成分限定理由はそれぞれ磁気特性および工業生
産性から制限される。ＣＯのＦｅ置換量は広範囲な成分
が可能であるが、永久磁石材料のキュリー温度を高め強
磁性相を室温で安定化させる意味においてＣｏ１Ｊ換は
効果的であるが、合金の飽和磁化を低下させる作用およ
び保磁力劣化作用を示すので、Ｆｅに対する置換量は０
≦Ｘ≦０．６の範囲に規定される。Ｃ量はｙ＜０．０４
では安定な強磁性相が維持できなくなり、実用上要求さ
れる保磁力が発生せず、ｙ＞ ０．１５では飽和磁化の
減少を伴う。次に希土類と遷移金属類との比率２はｚ＜
６においても保磁力は得られるが飽和磁化の劣化を引き
起こし、ｚ〉１０においては保磁性が期待できなくなる
ことにより、６≦２≦１０の組成に限定される。The components of the present invention are limited due to magnetic properties and industrial productivity. Although a wide range of Fe substitution amounts are possible for CO, Co1J substitution is effective in increasing the Curie temperature of the permanent magnet material and stabilizing the ferromagnetic phase at room temperature, but it lowers the saturation magnetization of the alloy. The amount of substitution for Fe is 0 because it shows the effect of coercive force deterioration.
It is defined in the range of ≦X≦0.6. The amount of C is y<0.04
If y>0.15, a stable ferromagnetic phase cannot be maintained and the coercive force required for practical use is not generated, and saturation magnetization decreases when y>0.15. Next, the ratio 2 of rare earths and transition metals is z<
Although a coercive force can be obtained even with Z6, the saturation magnetization deteriorates, and coercivity cannot be expected at Z>10, so the composition is limited to 6≦2≦10.
［実施例］ 〜
第１表は本発明の実施例を示す永久磁石材料の組成式で
あり、試料ｌ１ｃＬ１〜１１の各組成に秤吊第１表
し、Ａｒ中でアーク溶解しインゴットを得た。次にイン
ゴットを小片（３０ｏ）とり、第２図に示すように、底
部に１φのキャピラリのある石英坩堝中に入れ、真空に
排気後Ａｒ気流を送り、高周波溶解用の励起コイル内に
石英坩堝を挿入し十分高温に溶融した後、坩堝上部から
ｉ、ｓａｔ＋ｉの圧力でＡ「を導入し、溶融体を底部キ
ャピラリから噴射させて、石英坩堝下部の回転ロールに
て急冷することにより、１１種類の非晶質リボンを作成
した。次にそれぞれのリボンを第２表の熱処理条件によ
り再結晶化させ、その磁気特性を振動磁力計によって計
測した。[Example] - Table 1 shows the composition formulas of permanent magnet materials showing examples of the present invention. Each composition of samples 11cL1 to 11 was weighed and arc melted in Ar to obtain ingots. Next, take a small piece (30o) of the ingot and place it in a quartz crucible with a 1φ capillary at the bottom as shown in Figure 2. After evacuation to a vacuum, Ar airflow is sent to the quartz crucible in an excitation coil for high frequency melting. was inserted and melted at a sufficiently high temperature, A' was introduced from the top of the crucible at a pressure of i, sat + i, the molten material was injected from the bottom capillary, and quenched by the rotating rolls at the bottom of the quartz crucible, 11 types were produced. Next, each ribbon was recrystallized under the heat treatment conditions shown in Table 2, and its magnetic properties were measured using a vibrating magnetometer.
第２表に磁気特性データも示す。第２表に示されるよう
に、本発明による組成合金が高い飽和磁化（２０にＯｅ
の磁場における磁化の強さ）を保有すること、および実
用永久磁石材料として必要なだけの固有保磁力を有して
いることが確認できる。Table 2 also shows magnetic property data. As shown in Table 2, the composition alloy according to the present invention has a high saturation magnetization (20 Oe
It can be confirmed that the material has a strong magnetization strength in a magnetic field of
本発明の組成永久磁石材料の製造方法は、ロール急冷等
の急冷、凝固、再結晶方法だけではな（多様な方法が可
能であり、最適な条件に調整することにより、＾性能永
久磁石材料を製造することは容易にできる。たとえば第
３図に示すように”０．８０Ｖ０．２ ［Ｆ２Ｏ，５６
Ｃ００，３８Ｃ０１０５Ｍ０．０２Ｂ ］ 組成合
金を高周波溶融後、底面側０．０１ ６．５
から凝固するように水冷銅鋳型中にＡ＃ ２０３製リン
グ（１０φＸ２０φ、高さ１５履）を置き、その内側空
間に溶湯を流し込み鋳造すると、底面から上部へ成長す
る一方向性柱状晶凝固体が得られる。この凝固体を８０
０℃、７２時間熱処理を施すと、柱状晶の成長方向に対
して直角面内に放射状の異方性を有し、第１図に示すよ
うに固有保磁力３〜５にＯｅの鋳造磁石が得られた。The method for producing the composition permanent magnet material of the present invention is not limited to quenching, solidification, and recrystallization methods such as roll quenching (various methods are possible, and by adjusting the optimum conditions, the performance permanent magnet material can be obtained. It is easy to manufacture. For example, as shown in Figure 3, "0.80V0.2 [F2O,56
C00,38C0105M0.02B] After high-frequency melting of the composition alloy, a ring made of A# 203 (10 φ x 20 φ, height 15 shoes) was placed in a water-cooled copper mold so that it solidified from the bottom side, and the inner space was When a molten metal is poured into and cast, a unidirectional columnar solidified body that grows from the bottom to the top is obtained. 80% of this coagulation
When heat treated at 0°C for 72 hours, the cast magnet has radial anisotropy in a plane perpendicular to the growth direction of the columnar crystals, and has an intrinsic coercive force of 3 to 5 Oe, as shown in Figure 1. Obtained.
さらにこうして得られた鋳造体を砕いて樹脂結合型永久
磁石材料とすることも容易である。Furthermore, it is easy to crush the cast body thus obtained to obtain a resin-bonded permanent magnet material.
また鋳造体を従来の５ｌ−Ｃｏ系永久磁石と同様な方法
によって粗粉砕、微粉砕、磁場配向、圧縮成長、焼結１
時効工程を経て永久磁石を製造することも可能である。In addition, the cast body was subjected to coarse pulverization, fine pulverization, magnetic field orientation, compression growth, and sintering in the same manner as conventional 5L-Co permanent magnets.
It is also possible to manufacture permanent magnets through an aging process.
［発明の効果］
以上本発明の組成合金は軽希土類を中心とし、Ｆｅ、
Ｃｏを主成分とする比較的豊富な元素から構成され、か
つ最近の８を中心とするＮｄ−Ｆｅ−Ｂ系磁石に対して
、ＢをＣに置換した新規な組成合金からなる永久磁石材
料を提供するものであり、電子部品、産業機器分野にお
いて多様な応用分野に利用できる。[Effects of the Invention] As described above, the composition alloy of the present invention mainly contains light rare earth elements, Fe,
In contrast to the recent Nd-Fe-B magnets, which are composed of relatively abundant elements with Co as the main component, and which mainly consist of 8, we have developed a permanent magnet material made of a new compositional alloy in which B is replaced with C. It can be used in a variety of application fields in the fields of electronic components and industrial equipment.
第１図は本発明の永久磁石材料の減磁曲線。
Ａ：柱状晶の成長方向に対して直角方向Ｂ：柱状晶の成
長方向に対して平行方向第２図は本発明の材料を作るた
めの製造装置の概略図。
第３図は本発明の材料を作るための製造装置の概略図。
特許出願人 並木精密宝石株式会社
第 １ 図FIG. 1 shows a demagnetization curve of the permanent magnet material of the present invention. A: Direction perpendicular to the growth direction of columnar crystals B: Parallel to the growth direction of columnar crystals FIG. 2 is a schematic diagram of a manufacturing apparatus for producing the material of the present invention. FIG. 3 is a schematic diagram of a manufacturing apparatus for manufacturing the material of the present invention. Patent applicant Namiki Precision Jewel Co., Ltd. Figure 1
Claims (1)
）＿ｚにおいて、Ｒは希土類元素、ＭはＣもしくはＣを
主体とするＡｌ，Ｇａ，Ｇｅ，Ｂｉ，Ｐ，Ｓｉ，Ｂから
選択された１種もしくは２種以上の元素との混合物から
なり、０≦ｘ≦０．６ ０．０４≦ｙ≦０．１５ ６≦ｚ≦１０ なる組成範囲に限定される永久磁石材料。[Claims] General formula R(Fe_1_-_x_-_yCo_xM_y
)_z, R is a rare earth element, M is C or a mixture of C with one or more elements selected from Al, Ga, Ge, Bi, P, Si, and B, and 0 A permanent magnet material whose composition is limited to the following composition ranges: ≦x≦0.6, 0.04≦y≦0.15, 6≦z≦10.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62327821A JPH01168844A (en) | 1987-12-24 | 1987-12-24 | Permanent magnet material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62327821A JPH01168844A (en) | 1987-12-24 | 1987-12-24 | Permanent magnet material |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH01168844A true JPH01168844A (en) | 1989-07-04 |
Family
ID=18203354
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP62327821A Pending JPH01168844A (en) | 1987-12-24 | 1987-12-24 | Permanent magnet material |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH01168844A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0339222A (en) * | 1989-07-06 | 1991-02-20 | Ricoh Co Ltd | Injection molding device |
| JPH0382744A (en) * | 1989-08-25 | 1991-04-08 | Dowa Mining Co Ltd | Permanent magnet alloy excellent in oxidation resistance |
| JPH04268052A (en) * | 1991-02-22 | 1992-09-24 | Dowa Mining Co Ltd | R-fe-b-c permanent magnet alloy reduced in irreversible demagnetization and excellent in heat stability |
| 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 |
-
1987
- 1987-12-24 JP JP62327821A patent/JPH01168844A/en active Pending
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0339222A (en) * | 1989-07-06 | 1991-02-20 | Ricoh Co Ltd | Injection molding device |
| JPH0382744A (en) * | 1989-08-25 | 1991-04-08 | Dowa Mining Co Ltd | Permanent magnet alloy excellent in oxidation resistance |
| 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 |
| EP0414645B2 (en) † | 1989-08-25 | 2003-01-02 | 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 |
| JPH04268052A (en) * | 1991-02-22 | 1992-09-24 | Dowa Mining Co Ltd | R-fe-b-c permanent magnet alloy reduced in irreversible demagnetization and excellent in heat stability |
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