JPS6271201A - Bond magnet - Google Patents
Bond magnetInfo
- Publication number
- JPS6271201A JPS6271201A JP60211546A JP21154685A JPS6271201A JP S6271201 A JPS6271201 A JP S6271201A JP 60211546 A JP60211546 A JP 60211546A JP 21154685 A JP21154685 A JP 21154685A JP S6271201 A JPS6271201 A JP S6271201A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- magnetic flux
- flux density
- thermal stability
- coercive force
- 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
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
- H01F1/0578—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 bonded together
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は、Ｒ−Ｆｅ−Ｂ系合金（ＲはＹを含む１種また
は２種以上の希土類元素並びにＦｅの一部をＣｏで置換
したＲ−Ｆｅ−Ｃｏ−Ｂ系合金を含む）のボンド磁石に
関するものである。[Detailed Description of the Invention] [Industrial Application Field] The present invention relates to an R-Fe-B alloy (R is one or more rare earth elements including Y and a portion of Fe is replaced with Co). The present invention relates to bonded magnets (including R-Fe-Co-B alloys).
近年、高エネルギー積を有するＲ−Ｆｅ−Ｂ系合金また
はＦｅの一部をＣｏで置換したＲ−Ｆｅ−Ｃｏ−Ｂ系合
金による永久磁石、特にＮｄＦｅ−Ｂ系永久磁石の研究
が盛んである。これらの永久磁石は、Ｓｍ−Ｃｏ磁石と
略同程度の保磁力とエネルギー積を有するが、Ｓｍ−Ｃ
ｏ磁石より経済的であるため最近注目されている永久磁
石である。而してＮｄ−Ｆｅ−Ｂ系永久磁石の製造プロ
セスは、大別して下記の２種類がある。In recent years, there has been active research into permanent magnets made of R-Fe-B alloys with high energy products or R-Fe-Co-B alloys in which a portion of Fe is replaced with Co, especially NdFe-B permanent magnets. . These permanent magnets have approximately the same coercive force and energy product as Sm-Co magnets, but Sm-C
It is a permanent magnet that has recently attracted attention because it is more economical than o-magnets. The manufacturing process for Nd-Fe-B permanent magnets can be broadly classified into the following two types.
まず第１の製造プロセスは、特開昭５９−４６００８号
公報および同５９−６４７３３号公報に記載されている
ように、Ｎｄ−Ｆｅ−Ｂ系合金を粉砕した後、粉末冶金
プロセスにより成形し、焼結処理を経て焼結磁石とする
方法である。First, the first manufacturing process is as described in Japanese Unexamined Patent Publication Nos. 59-46008 and 59-64733, after crushing the Nd-Fe-B alloy, it is molded by a powder metallurgy process. This is a method of making a sintered magnet through a sintering process.
他の製造プロセスは１例えば特開昭５９−６４７３９号
公報に記載されているように、超急冷法により合金をそ
のまま、あるいは熱処理をすることにより、フレーク状
の永久磁石を作成し、その後特開昭５９−２１１５４９
号公報に記載されるように５樹脂と共に固化成形して等
方性ボンド磁石とするものである。Another manufacturing process is 1, for example, as described in JP-A No. 59-64739, flake-shaped permanent magnets are created by ultra-quenching the alloy as it is or by heat treatment, and then Showa 59-211549
As described in the above publication, it is solidified and molded together with 5 resin to form an isotropic bonded magnet.
前者の方法によれば、磁気異方性化が可能であり、得ら
れる磁気特性は３５〜４５ＭＧＯｅにも到達するのであ
るが、木質的にキューリ一点が低く、熱安定性が悪い。According to the former method, it is possible to create magnetic anisotropy, and the obtained magnetic properties reach 35 to 45 MGOe, but the curie point is low in wood quality and the thermal stability is poor.
従ってモーター用等、高温の環境下で使用されるものに
は適用できない欠点がある。また比較的複雑な形状のも
のまたは薄型の製品を高能率かつ経済的に製造すること
が困難である。また後者の方法によれば、比較的成形が
容易である。しかし単にインゴットを粉砕したのみの粉
末原料を使用するときには、保磁力が低いため、実用に
供し難いという欠点がある。Therefore, it has the disadvantage that it cannot be applied to products used in high-temperature environments such as motors. Furthermore, it is difficult to efficiently and economically manufacture products with relatively complex shapes or thin shapes. Moreover, according to the latter method, molding is relatively easy. However, when a powder raw material obtained by simply pulverizing an ingot is used, the coercive force is low, making it difficult to put it to practical use.
本発明は上記のような従来技術に存する欠点を解消し、
熱安定性良好であり、すなわち不可逆減磁率が小さく、
比較的高温の環境下に適用可能なＲ−Ｆｅ−Ｂ系合金の
ボンド磁石を提供することを目的とするものである。The present invention eliminates the drawbacks existing in the prior art as described above,
Good thermal stability, i.e. low irreversible demagnetization rate,
The object of the present invention is to provide a bonded magnet made of an R-Fe-B alloy that can be used in a relatively high-temperature environment.
本発明は上記目的達成のために、下記のような技術的手
段を採用したのである。In order to achieve the above object, the present invention employs the following technical means.
すなわち、平均粒径を０．０１〜０．５μｍに制御した
Ｒ−Ｆｅ−Ｂ系合金（ＲはＹを含む１種または２種以上
の希土類元素並びにＦｅの一部をＣ。That is, an R-Fe-B alloy with an average grain size controlled to 0.01 to 0.5 μm (R is one or more rare earth elements including Y and a portion of Fe is C).
で置換したＲ−Ｆｅ−Ｃｏ−Ｂ系合金を含む）と。(including R-Fe-Co-B alloys substituted with).
体積構成比で１５〜４０％のバインダーからなるもので
ある。It consists of a binder with a volume composition ratio of 15 to 40%.
而して好ましくは、上ｒａＲ−Ｆｅ−Ｂ系合金が。Preferably, the above raR-Fe-B alloy is used.
原子百分率において、Ｒ：１１〜１８％、Ｂ：４〜１１
％、Ｃｏ：３０％以下、残部Ｆｅおよび不可避不純物か
らなる組成としたものである。In atomic percentage, R: 11-18%, B: 4-11
%, Co: 30% or less, the balance consisting of Fe and unavoidable impurities.
本発明においてＲ−Ｆｅ−Ｂ系合金の平均粒径が０．５
μｍを超えると、１６０℃における不可逆減磁率が１０
％以上となって、著るしく熱安定性を低下させるので不
都合である。また平均粒径が０．０１１！ｍ未満である
と、成形後のボンド磁石の保磁力が低く、所定の永久磁
石特性を得ることができない。従って平均粒径を０．０
１〜０．５μｍと限定した。In the present invention, the average grain size of the R-Fe-B alloy is 0.5
If it exceeds μm, the irreversible demagnetization rate at 160°C is 10
% or more, this is disadvantageous because it significantly reduces thermal stability. Also, the average particle size is 0.011! If it is less than m, the coercive force of the bonded magnet after molding will be low and predetermined permanent magnet characteristics cannot be obtained. Therefore, the average particle size is 0.0
It was limited to 1 to 0.5 μm.
またバインダーは９体積構成比で４０％を超えると、成
形後の永久磁石体が所定の磁気特性を発揮することがで
きず、また１５％未満では、成形体の機械的性質が充分
でなく１割れ、破損等の欠陥を生じ易いため、１５〜４
０％と限定した。In addition, if the binder exceeds 40% in terms of volumetric ratio, the molded permanent magnet will not be able to exhibit the desired magnetic properties, and if it is less than 15%, the mechanical properties of the molded product will be insufficient. 15 to 4 because defects such as cracks and breakage are likely to occur.
It was limited to 0%.
次にＲ−Ｆｅ−Ｂ系合金の好ましい成分範囲について記
述する。第１図および第２図は各々Ｎｄ−Ｆｅ−Ｂ系急
冷薄片磁石の残留磁束密度および保磁力の組成依存性を
示す図である。例えば回転機用永久磁石としては、少な
くとも残留磁束密度Ｂｒは６ｋＧ以上、保磁力ｉＨｃは
１０ｋＯｅ以上が必要である。従って第１図および第２
図からＮｄおよびＢの成分範囲を求め、Ｒ：１１〜１８
％、Ｂ：４〜１１％と定めた。Ｒとしては、飽和磁束密
度の観点から、Ｎｄおよび／またはＰｒを主成分とする
ことが望ましい。また保磁力向上のため、Ｔｂ、 Ｄ
ｙ等の元素を添加したり、資源の有効利用のためＣｅジ
ジム等の原料を使用することも可能である。第３図はＮ
ｄ−Ｆｅ−Ｂ系合金において、Ｆｅの一部をＣｏで置換
した場合（Ｆｅ７＆−ｘｃＯｘ Ｎｄｔ＆Ｂｇ）（Ｄ急
冷薄片磁石）残留磁束密度および保磁力のＣｏ置換量依
存性を示す図である。Ｃｏはキューリ一点を上昇させる
作用があるため置換元素として好ましいが、第３図から
明らかなように、残留磁束密度Ｂｒを６ｋＧ以上確保す
るため、限界置換量を３０ａｔ％と定めた。Next, a preferred range of ingredients for the R-Fe-B alloy will be described. FIG. 1 and FIG. 2 are diagrams showing the composition dependence of the residual magnetic flux density and coercive force of a Nd-Fe-B based rapidly solidified thin piece magnet, respectively. For example, a permanent magnet for a rotating machine must have at least a residual magnetic flux density Br of 6 kG or more and a coercive force iHc of 10 kOe or more. Therefore, Figures 1 and 2
Determine the component range of Nd and B from the diagram, R: 11 to 18
%, B: 4 to 11%. From the viewpoint of saturation magnetic flux density, R preferably contains Nd and/or Pr as a main component. In addition, to improve coercive force, Tb, D
It is also possible to add elements such as y or to use raw materials such as Ce didymium for effective use of resources. Figure 3 is N
FIG. 7 is a diagram showing the dependence of residual magnetic flux density and coercive force on the amount of Co substitution when a part of Fe is replaced with Co (Fe7&-xcOx Ndt&Bg) (D quenched flake magnet) in a d-Fe-B alloy. Co is preferable as a substitution element because it has the effect of raising the Curie point, but as is clear from FIG. 3, in order to ensure a residual magnetic flux density Br of 6 kG or more, the limit substitution amount was set at 30 at%.
なお本発明の合金中には、上記元素の他に、不可避不純
物として、フェロボロン中に含まれるＡＱ。In addition to the above-mentioned elements, the alloy of the present invention contains AQ, which is contained in ferroboron, as an unavoidable impurity.
Ｓｉ、Ｐ、Ｃの他、Ｎｄを還元する際に混入する還元剤
若しくはその酸化物等がある。In addition to Si, P, and C, there are reducing agents or their oxides that are mixed in when reducing Nd.
また前記バインダーとして使用し得る材料として、まず
樹脂では、熱硬化性樹脂および熱可塑性樹脂の何れも適
用できるが、熱的に安定な樹脂が望ましい。例えば、ポ
リアミド、ポリイミド、ポリエステル、フェノール、フ
ッ素、ゲイ素、およびエポキシ等の樹脂を使用できる。As for the material that can be used as the binder, both thermosetting resins and thermoplastic resins can be used, but thermally stable resins are preferable. For example, resins such as polyamide, polyimide, polyester, phenol, fluorine, silicone, and epoxy can be used.
また上記合成樹脂の他に、ＡＱ、Ｓｎ、Ｐｂおよびハン
ダその他の低融点金属または合金を使用することができ
〔実施例 １〕
Ｆ ｅ ６ｏＮ ｄ ＋ａＢｂ合金１００ｇをＡｒ雰囲
気中で単ロール法により薄片化した。薄片は厚さ約３Ｑ
メｔ ｍの不定形であり、Ｘ線回折の結果、薄片は非
結晶質体と結晶質体の混合体であることを確認した。In addition to the above synthetic resins, low melting point metals or alloys such as AQ, Sn, Pb, and solder can be used. [Example 1] 100 g of F e 6oN d +aBb alloy is made into thin pieces by a single roll method in an Ar atmosphere. It became. Thickness of flakes is about 3Q
Met m was amorphous, and X-ray diffraction confirmed that the flakes were a mixture of amorphous and crystalline materials.
この薄片を真空中で６００℃×１時間の熱処理を施した
７＆Ａｒ急冷し、その後３２メツシユ以下に粉砕した。This flake was heat treated in vacuum at 600° C. for 1 hour, rapidly cooled with 7&Ar, and then ground to 32 meshes or less.
この粉末に体積比で２０％のエポキシ樹脂を加えた後に
、多量のアセトンを加えてエポキシ樹脂を溶解し、その
後に真空吸引することにより、前記アセトンを除去し、
粉末表面にエポキシ樹脂のコーティングを行なった。次
にこの粉末を８ｔ ／ ｃｔＡの圧力で成形し、１２０
℃×２時間の硬化処理を施してボンド磁石とした。この
ボンド磁石は、平均結晶粒径０．０６μｍの組織を有し
ており、７０ｋＯｅでパルス着磁することにより。After adding 20% by volume of epoxy resin to this powder, a large amount of acetone is added to dissolve the epoxy resin, and then the acetone is removed by vacuum suction,
The powder surface was coated with epoxy resin. Next, this powder was compacted at a pressure of 8t/ctA, and 120
A bonded magnet was obtained by performing a curing treatment for 2 hours at ℃. This bonded magnet has a structure with an average crystal grain size of 0.06 μm, and is produced by pulse magnetization at 70 kOe.
Ｂｒ＝６．９ｋＧ、１Ｈｃ＝１１．８ｋＯｅ、 （Ｂ
Ｈ）ｍａ ｘ＝１０．３ＭＧＯｅなる磁気特性を示した
。Br=6.9kG, 1Hc=11.8kOe, (B
H) max=10.3MGOe.
不可逆減磁率は、１００℃、１３０℃、１６０℃でそれ
ぞれ、１．４％、２．２％、４．１％であった。The irreversible demagnetization rates were 1.4%, 2.2%, and 4.1% at 100°C, 130°C, and 160°C, respectively.
他の組成のものについても同様の処理を行ない。Similar treatment was performed for other compositions as well.
それらの結果を第１表および第４図に示す。表および図
中における符号Ａ−ＤおよびＥ−Ｇは各々本発明の実施
例における試料および比較例における試料を示す。而し
て符号Ａ−Ｅがボンド磁石。The results are shown in Table 1 and Figure 4. Symbols A-D and E-G in the tables and figures indicate samples in Examples of the present invention and samples in Comparative Examples, respectively. The symbols A-E are bonded magnets.
ＦおよびＧは磁気異方性焼結磁石である。F and G are magnetically anisotropic sintered magnets.
第 １ 表
第１表から明らかなように、試料Ａ−Ｇは何れも保磁力
が１Ｏｋｏｅを超えており、磁気特性は略満足すべき値
を示しているが、第４図に示すように、各温度に対応す
る不可逆減磁率の値には大きな差がある。すなわち本発
明の実施例における試料Ａ−Ｄにおいては、温度１６０
℃においても不可逆減磁率は１０％以下であるのに対し
、比較例のＥ−Ｇは何れも１００〜１３０℃で不可逆減
磁率はすでに１０％を越えている。Table 1 As is clear from Table 1, samples A to G all have coercive forces exceeding 1 Okoe, and their magnetic properties show approximately satisfactory values; however, as shown in Figure 4, There is a large difference in the value of irreversible demagnetization rate corresponding to each temperature. That is, in samples A-D in the examples of the present invention, the temperature was 160
The irreversible demagnetization rate is 10% or less even at 100 DEG C., whereas the irreversible demagnetization rate is already over 10% at 100 to 130 DEG C. in all of the comparative examples E-G.
〔実施例 ２〕
次に薄片の熱処理温度を変えることにより、平均結晶粒
径を制御した結果、不可逆減磁率に及ぼす影響を第２表
に示す。他の条件は何れも実施例１と同様である。[Example 2] Next, the average grain size was controlled by changing the heat treatment temperature of the flakes, and the effects on the irreversible demagnetization rate are shown in Table 2. All other conditions are the same as in Example 1.
第２表
第２表における符号Ｈ−には本発明の実施例であり、符
号りおよびＭは比較例である。第２表から明らかなよう
に、平均結晶粒径の大なるしおよびＭにおいては、不可
逆減磁率は１６０℃において何れも１０％を越えている
のに対し１本発明の実施例を示す符号Ｈ−には、何れも
１０％以下の値を示している。Table 2 In Table 2, the symbol H- indicates an example of the present invention, and the symbol and M indicate a comparative example. As is clear from Table 2, the irreversible demagnetization rate exceeds 10% at 160°C for both large and M grains with large average grain sizes, whereas the symbol H indicating the embodiment of the present invention - indicates a value of 10% or less.
〔実施例 ３〕
本実施例においては２希土類元素の一部を変化させたも
の、およびＦｅの一部をＣｏで置換したものについて、
前記実施例１と同様の条件でボンド磁石を成形したもの
である。[Example 3] In this example, two rare earth elements were partially changed and Fe was partially replaced with Co.
A bonded magnet was molded under the same conditions as in Example 1.
第３表
第３表から明らかなように、何れの組成のものも不可逆
ｔＪＪｉ磁率は極めて低い値を示し、熱安定性が良好で
あることを表わしている。As is clear from Table 3, irreversible tJJi magnetic coefficients of all compositions showed extremely low values, indicating good thermal stability.
以上記述のように１本発明のボンド磁石は比較的高温環
境下においても不可逆減磁率が小さく。As described above, the bonded magnet of the present invention has a small irreversible demagnetization rate even in a relatively high temperature environment.
熱安定性が極めて良好である。また成形性も良好である
ため、比較的複雑な形状のものでも高能率で成形するこ
とができる。従ってモーター等の回転機の構成要素とし
て広く適用できる効果がある。Extremely good thermal stability. Furthermore, since the moldability is good, even relatively complicated shapes can be molded with high efficiency. Therefore, it has the effect of being widely applicable as a component of rotating machines such as motors.
第１図および第２図は各々Ｎｄ−Ｆｅ−Ｂ系急冷薄片磁
石の残留磁束密度および保磁力の組成依存性を示す図、
第３図は残留磁束密度および保磁力のＣｏ置換量依存性
を示す図、第４図は温度と不可逆減磁率との関係を示す
図である。Figures 1 and 2 are diagrams showing the composition dependence of the residual magnetic flux density and coercive force of Nd-Fe-B based rapidly solidified flake magnets, respectively;
FIG. 3 is a diagram showing the dependence of residual magnetic flux density and coercive force on the amount of Co substitution, and FIG. 4 is a diagram showing the relationship between temperature and irreversible demagnetization rate.
Claims (2)
Ｆｅ−Ｂ系合金（ＲはＹを含む１種または２種以上の希
土類元素並びにＦｅの一部をＣｏで置換したＲ−Ｆｅ−
Ｃｏ−Ｂ系合金を含む）と、体積構成比で１５〜４０％
のバインダーからなることを特徴とするボンド磁石。(1) R- with an average crystal grain size of 0.01 to 0.5 μm
Fe-B alloy (R is one or more rare earth elements including Y and R-Fe- in which a part of Fe is replaced with Co)
(including Co-B alloy) and 15 to 40% volume composition ratio
A bonded magnet characterized by comprising a binder.
：１１〜１８％、Ｂ：４〜１１％、Ｃｏ：３０％以下、
残部Ｆｅおよび不可避不純物からなる特許請求の範囲第
１項記載のボンド磁石。(2) The R-Fe-B alloy has an atomic percentage of R
: 11 to 18%, B: 4 to 11%, Co: 30% or less,
The bonded magnet according to claim 1, wherein the balance is Fe and unavoidable impurities.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60211546A JPS6271201A (en) | 1985-09-25 | 1985-09-25 | Bond magnet |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60211546A JPS6271201A (en) | 1985-09-25 | 1985-09-25 | Bond magnet |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS6271201A true JPS6271201A (en) | 1987-04-01 |
Family
ID=16607613
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP60211546A Pending JPS6271201A (en) | 1985-09-25 | 1985-09-25 | Bond magnet |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6271201A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH01251702A (en) * | 1988-03-31 | 1989-10-06 | Tokin Corp | Plastic magnet and manufacture thereof |
| JPH0246704A (en) * | 1988-08-09 | 1990-02-16 | Tokin Corp | Manufacture of compound magnet |
| WO2003017293A1 (en) * | 2001-08-14 | 2003-02-27 | General Electric Company | Permanent magnet for electromagnetic device and method of making |
-
1985
- 1985-09-25 JP JP60211546A patent/JPS6271201A/en active Pending
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH01251702A (en) * | 1988-03-31 | 1989-10-06 | Tokin Corp | Plastic magnet and manufacture thereof |
| JPH0246704A (en) * | 1988-08-09 | 1990-02-16 | Tokin Corp | Manufacture of compound magnet |
| WO2003017293A1 (en) * | 2001-08-14 | 2003-02-27 | General Electric Company | Permanent magnet for electromagnetic device and method of making |
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