JPS62261102A - Bonded magnet for starter motor - Google Patents
Bonded magnet for starter motorInfo
- Publication number
- JPS62261102A JPS62261102A JP61104357A JP10435786A JPS62261102A JP S62261102 A JPS62261102 A JP S62261102A JP 61104357 A JP61104357 A JP 61104357A JP 10435786 A JP10435786 A JP 10435786A JP S62261102 A JPS62261102 A JP S62261102A
- Authority
- JP
- Japan
- Prior art keywords
- bonded magnet
- alloy
- starter motor
- magnet
- motor according
- 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
- 239000007858 starting material Substances 0.000 title claims description 16
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 16
- 239000000956 alloy Substances 0.000 claims abstract description 16
- 239000000843 powder Substances 0.000 claims abstract description 13
- 229910000521 B alloy Inorganic materials 0.000 claims abstract description 10
- 229910052761 rare earth metal Inorganic materials 0.000 claims abstract description 10
- 239000011230 binding agent Substances 0.000 claims abstract description 9
- 238000000748 compression moulding Methods 0.000 claims abstract description 9
- 238000001746 injection moulding Methods 0.000 claims abstract description 7
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 229910052735 hafnium Inorganic materials 0.000 claims abstract description 4
- 229910052742 iron Inorganic materials 0.000 claims abstract description 4
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 4
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 4
- 239000013078 crystal Substances 0.000 claims abstract description 3
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 3
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract 2
- 239000006247 magnetic powder Substances 0.000 claims description 5
- 238000010791 quenching Methods 0.000 claims description 5
- 239000000463 material Substances 0.000 claims description 4
- 238000007731 hot pressing Methods 0.000 claims description 3
- 238000010298 pulverizing process Methods 0.000 claims description 3
- 229910052789 astatine Inorganic materials 0.000 claims description 2
- 238000003754 machining Methods 0.000 claims description 2
- 229910002546 FeCo Inorganic materials 0.000 claims 1
- 229910052799 carbon Inorganic materials 0.000 claims 1
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 abstract description 10
- 238000000034 method Methods 0.000 abstract description 6
- 239000000654 additive Substances 0.000 abstract description 5
- 239000000203 mixture Substances 0.000 abstract description 5
- 230000000996 additive effect Effects 0.000 abstract description 3
- 229910052782 aluminium Inorganic materials 0.000 abstract 1
- 229910000859 α-Fe Inorganic materials 0.000 description 9
- 238000000465 moulding Methods 0.000 description 7
- 229920001187 thermosetting polymer Polymers 0.000 description 6
- 230000007423 decrease Effects 0.000 description 4
- 230000005347 demagnetization Effects 0.000 description 4
- 230000004907 flux Effects 0.000 description 4
- 238000002844 melting Methods 0.000 description 4
- 230000008018 melting Effects 0.000 description 4
- 150000002910 rare earth metals Chemical class 0.000 description 4
- 230000005415 magnetization Effects 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 239000002245 particle Substances 0.000 description 3
- 238000003825 pressing Methods 0.000 description 3
- 238000005245 sintering Methods 0.000 description 3
- 229910000828 alnico Inorganic materials 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 239000003822 epoxy resin Substances 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000005498 polishing Methods 0.000 description 2
- 229920000647 polyepoxide Polymers 0.000 description 2
- 229920005989 resin Polymers 0.000 description 2
- 239000011347 resin Substances 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 239000004593 Epoxy Substances 0.000 description 1
- 229910017061 Fe Co Inorganic materials 0.000 description 1
- 229910017110 Fe—Cr—Co Inorganic materials 0.000 description 1
- PXGOKWXKJXAPGV-UHFFFAOYSA-N Fluorine Chemical compound FF PXGOKWXKJXAPGV-UHFFFAOYSA-N 0.000 description 1
- 239000004677 Nylon Substances 0.000 description 1
- 235000016496 Panda oleosa Nutrition 0.000 description 1
- 240000000220 Panda oleosa Species 0.000 description 1
- ISWSIDIOOBJBQZ-UHFFFAOYSA-N Phenol Chemical compound OC1=CC=CC=C1 ISWSIDIOOBJBQZ-UHFFFAOYSA-N 0.000 description 1
- 239000004952 Polyamide Substances 0.000 description 1
- 239000004642 Polyimide Substances 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000001354 calcination Methods 0.000 description 1
- 239000003638 chemical reducing agent Substances 0.000 description 1
- 239000010941 cobalt Substances 0.000 description 1
- 229910017052 cobalt Inorganic materials 0.000 description 1
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000002178 crystalline material Substances 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000001035 drying Methods 0.000 description 1
- 238000011049 filling Methods 0.000 description 1
- 238000010304 firing Methods 0.000 description 1
- 239000011737 fluorine Substances 0.000 description 1
- 229910052731 fluorine Inorganic materials 0.000 description 1
- 238000005469 granulation Methods 0.000 description 1
- 230000003179 granulation Effects 0.000 description 1
- 238000013007 heat curing Methods 0.000 description 1
- 230000002427 irreversible effect Effects 0.000 description 1
- 229910052745 lead Inorganic materials 0.000 description 1
- 235000012054 meals Nutrition 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 229910001172 neodymium magnet Inorganic materials 0.000 description 1
- 229920001778 nylon Polymers 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 230000002093 peripheral effect Effects 0.000 description 1
- 238000007747 plating Methods 0.000 description 1
- 229920002647 polyamide Polymers 0.000 description 1
- 229920000728 polyester Polymers 0.000 description 1
- 229920001721 polyimide Polymers 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 229910000679 solder Inorganic materials 0.000 description 1
- 229920001169 thermoplastic Polymers 0.000 description 1
- 239000004416 thermosoftening plastic Substances 0.000 description 1
- 229910052718 tin Inorganic materials 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-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
- H01F1/0578—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種又は
２種以上の希土類元素又Ｆｅの１部をＣｏで置換したＲ
−Ｆｅ −Ｃｏ −Ｂ系合金を含みさらに添加元素（
Ｍ）としてＳｉ ＋Ａｚ＋Ｎｂ、Ｚｒ、Ｈｆ、Ｍｏ＋Ｇ
ａ＋Ｐ＋Ｃ９の１種又は２ｆｉ［以上の組み合せを用い
たＲ −Ｆｅ−Ｂ −Ｍ 、 Ｒ−Ｆｅ−Ｃｏ−Ｂ−Ｍ
合金を含む）のスタータモータ用ボンド磁石に関するも
のである。Detailed Description of the Invention [Field of Industrial Application] The present invention relates to an R-Fe-B alloy (R is one or more rare earth elements including Y or R in which a part of Fe is replaced with Co).
-Fe -Co -B alloy including additional elements (
M) as Si +Az+Nb, Zr, Hf, Mo+G
a+P+C9 or 2fi [R-Fe-B-M using the above combination, R-Fe-Co-B-M
This relates to bonded magnets for starter motors (including alloys).
従来からエンジン起動用のスタータモータとしてアーク
セグメント状の７工ライト磁石が一般に使用されている
。特に起動時の負荷が非常に大きいモータにおいては、
電機子反作用による減磁界が大きくなるので減磁耐力の
大きいフェライト磁石が使用されている。BACKGROUND ART Conventionally, an arc segment-shaped seven-piece light magnet has been generally used as a starter motor for starting an engine. Especially for motors that have a very large load at startup,
Since the demagnetizing field due to armature reaction becomes large, ferrite magnets with high demagnetization resistance are used.
しかるに、出力向上のためには残留磁束密度の高いこと
が必要で、しかも高出力になると電機子反作用による減
磁界が増加し、保磁力の高いことも必要となる。However, in order to improve the output, it is necessary to have a high residual magnetic flux density, and moreover, as the output increases, the demagnetizing field due to armature reaction increases, so it is also necessary to have a high coercive force.
更に製造面からも焼結によるため、高出力化に際しダブ
ルコンポーネント法、シングル法等の高性能磁石が提案
、実用に供せられているものの最終的には大型化１重量
化に頼らざるをえない傾向にある。Furthermore, since sintering is used in manufacturing, high-performance magnets such as the double-component method and single method have been proposed and put into practical use in order to increase output, but in the end, we have no choice but to rely on larger and heavier magnets. There tends to be no.
しかしてフェライト磁石ではこの様な要求を全て満すこ
とは困難であシ、出力の向上および磁気特性の点で一定
の限度が存在している。However, it is difficult for ferrite magnets to satisfy all of these requirements, and there are certain limits in terms of output improvement and magnetic properties.
上述したフェライト磁石は、保磁力（ｉＨｃ）は、４５
００〜５００００ｅと、減磁耐力の点では一応満足でき
るものの、残留磁束密度（Ｂｒ）は３７００〜１４００
０ｅ程度であυ、出力の点では必ずしも十分ではなかり
た。The above-mentioned ferrite magnet has a coercive force (iHc) of 45
00 to 50,000e, which is satisfactory in terms of demagnetization resistance, but the residual magnetic flux density (Br) is 3,700 to 1,400.
It was about 0e, which was not necessarily sufficient in terms of output.
更に焼結により製造されるので薄物ができないうえ、一
般的な半径方向磁束磁気回路に使用する場合、空＠面の
精度を出すのが難かしく高度の内面研磨技術を要する。Furthermore, since it is manufactured by sintering, it cannot be made thin, and when used in a general radial flux magnetic circuit, it is difficult to achieve the precision of the empty @ surface and requires advanced internal polishing technology.
したがって、本発明の目的は、上述した従来技術の問題
点を異方性ボンド磁石を応用することによりて解消し、
高い減磁耐力と高出力が得られ、さらにニアネットシェ
ープ形状で製造することによって加工性を大幅に向上さ
せたスタータモータ用磁石を提供することを目的とする
。Therefore, an object of the present invention is to solve the above-mentioned problems of the prior art by applying an anisotropic bonded magnet,
The object of the present invention is to provide a magnet for a starter motor, which can obtain high demagnetization resistance and high output, and has greatly improved workability by manufacturing it in a near net shape shape.
現在、スタータモータ用の磁石としてはフェライト磁石
のほかに、アルニコ磁石、 Ｆｅ −Ｃｒ−Ｃ。Currently, magnets for starter motors include ferrite magnets, alnico magnets, and Fe-Cr-C.
磁石、希土類磁石等が知られているが、アルニコ磁石と
Ｆｅ −Ｃｒ −Ｃｏ磁石は保磁力が約２００００ｅ以
下とフェライト磁石よりもかなり低いため、実用に供し
得ない。これに対し、希土類磁石は残留磁束密度および
保磁力が大きいため、性能の点では十分である。しかし
て希土類磁石でも、希土類コバルト磁石は高価であり、
コストパフォーマンスの点で必ずしも有利であるとは言
えない。Magnets, rare earth magnets, etc. are known, but alnico magnets and Fe-Cr-Co magnets have a coercive force of about 20,000 e or less, which is considerably lower than that of ferrite magnets, so they cannot be put to practical use. On the other hand, rare earth magnets have a large residual magnetic flux density and a large coercive force, so they are sufficient in terms of performance. However, even among rare earth magnets, rare earth cobalt magnets are expensive,
It cannot be said that it is necessarily advantageous in terms of cost performance.
そこで本発明者は、磁気特性が大であシかつ磁気モーメ
ントも大きく、価格的に有利な希土類−鉄一ポロンー鉄
系磁石に注目し、この合金磁石粉末をバインダーで結合
した異方性ボンド磁石をスタータモータ用磁石として用
いることにより、前記目的を達成できることを見出した
０すなわち、平均結晶粒径が０．０１〜０．５μｍに制
御したＲ−Ｆｅ−Ｂ系合金粉（ＲはＹを含む１種又は２
ａ以上の希土類元素、又Ｆｅの一部をＣｏで置換したＲ
−Ｆｅ−Ｂ系合金を含み、爽に添加元素（Ｍ）として、
Ｓｉ、Ａ２ ｒ Ｎｂ ＊ Ｚｒ 、 Ｈｆ ＋ Ｍｏ
＊ Ｇａ ＋ Ｐ ＊ Ｃの１種又は２種以上の組み
合せを用いたＲ−Ｆｅ−Ｂ −Ｍ 、 Ｒ−Ｆｅ−Ｃｏ
−Ｂ−Ｍ合金を含む）を１５〜４０体積チのバインダ
ーと混練し、磁場中圧縮成形、５Ｂ場中射出成形その他
の機械加工に製造されたものである。Therefore, the present inventors focused on rare earth-iron-iron-iron magnets, which have excellent magnetic properties and a large magnetic moment, and are advantageous in price, and created an anisotropic bonded magnet by combining this alloy magnet powder with a binder. It has been found that the above objective can be achieved by using as a magnet for a starter motor. Type 1 or 2
Rare earth elements of a or more, or R in which a part of Fe is replaced with Co
-Including Fe-B alloy, as an additional element (M),
Si, A2 r Nb * Zr, Hf + Mo
*Ga+P*R-Fe-B-M, R-Fe-Co using one type or a combination of two or more types
-B-M alloy) is kneaded with 15 to 40 volumes of binder, and manufactured by compression molding in a magnetic field, injection molding in a 5B field, and other machining processes.
上記合金は、好ましくはＲ：１１〜１８ａｔ％。The above alloy preferably has R: 11 to 18 at%.
Ｂ：４〜１．１ａｔ％＋ Ｃｏ ： ３０ ａ ｔ ％
以下、残部Ｆｅおよび不可避不純物からなる組成とした
ものであり、好ましくはＲ：１１〜１８ａｔ％、Ｂ：４
〜１１ａｔ％ 、 Ｃｏ ： ３０％以下、添加物：
０．００１〜３ａｔ％（添加物ＭはＳｔ 、Ａｔ＋Ｎｂ
、Ｚｒ ＋Ｈｆ ＋Ｍｏ ｔＧａ、Ｐ＋Ｃの１ａ又は
２種以上の組み合せ）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。B: 4 to 1.1 at% + Co: 30 at%
The following composition is composed of the balance Fe and unavoidable impurities, preferably R: 11 to 18 at%, B: 4
~11at%, Co: 30% or less, additives:
0.001 to 3 at% (Additive M is St, At+Nb
, Zr + Hf + Mo tGa, P + C (1a or a combination of two or more), the balance being Fe and unavoidable impurities.
本発明において、Ｒ−Ｆｅ−Ｂ系合金の平均粒径が０．
５μｍを越えると、ｉＨｃが低下し１６０℃における不
可逆減磁率が１０％以上となって著しく熱費定住を低下
させるので不都合である０又、平均粒径が０．０１μｍ
未満であると、成形後のボンド磁石のｉＨｃが低く所定
の永久磁石を得ることができない。よりて、平均粒径を
０．０１〜０．５μｍ、！：ｌａ定した。In the present invention, the average grain size of the R-Fe-B alloy is 0.
If it exceeds 5 μm, the iHc decreases and the irreversible demagnetization rate at 160° C. becomes 10% or more, which significantly reduces heating costs, which is disadvantageous.
If it is less than that, the iHc of the bonded magnet after molding will be low and a desired permanent magnet cannot be obtained. Therefore, the average particle size is 0.01 to 0.5 μm! :la has been decided.
本発明における磁粉の作成は以下のように行う。The magnetic powder in the present invention is produced as follows.
まず、所定の組成の合金を高周波溶解、アーク溶解等で
作成し、本合金を超急冷法によりフレーク化する。超急
冷は単ロール法、双ロール法いずれでもよく、ロール材
質はＦｅ 、 Ｃｕ等を用いる。First, an alloy with a predetermined composition is created by high-frequency melting, arc melting, etc., and the alloy is turned into flakes by an ultra-quenching method. The ultra-quenching may be carried out by either a single roll method or a twin roll method, and the roll material used is Fe, Cu, or the like.
Ｃｕを用いた場合は、Ｃｒメッキを施す方が好ましい０
超急冷は酸化を防ぐため、Ａｒ ｓ Ｈｅ等の不活性雰
囲気中で行う。本フレークを１００〜２００μ調程度の
大きさに粗粉砕する。粗粉砕粉を常温で成形し、成形体
を得る。本成形体を６００〜７５０℃でＨＩＰ又はホッ
トプレスし、比較的結晶粒径の小さい緻密化したブロッ
クを作ることができる。When using Cu, it is preferable to apply Cr plating.
The ultra-quenching is performed in an inert atmosphere such as Ar s He to prevent oxidation. The flakes are coarsely ground to a size of about 100 to 200 μm. The coarsely ground powder is molded at room temperature to obtain a molded body. By HIPing or hot pressing this molded body at 600 to 750°C, a densified block with relatively small crystal grain size can be produced.
本ブロックを再度６００〜７５０℃ですえ込み加工する
ことにより異方性の偏平板をうることかできる。加工率
が大きいほど異方性化度は向上する。By processing this block again at 600 to 750°C, an anisotropic flat plate can be obtained. The degree of anisotropy improves as the processing rate increases.
必要があれば得られた偏平板に６００〜８００℃で熱処
理を加えることにより得られるｉＨｃけ向上する。本偏
平板を粗粉砕することにより、異方性ボンド磁石用粗粉
をうるととができる。If necessary, the resulting flat plate is heat treated at 600 to 800°C to improve the iHc. By coarsely pulverizing this flat plate, coarse powder for an anisotropic bonded magnet can be obtained.
本粗粉に熱硬化性バインダーを加えて磁場中で圧縮成形
後熱硬化させれば、圧縮成形タイプの異方性ボンド磁石
を得ることができる。又、本粗粉に熱可塑性バインダー
を加えて磁場中射出成形すれば射出成形タイプの異方性
ボンド磁石を得ることができる。By adding a thermosetting binder to this coarse powder, compression molding it in a magnetic field, and then thermosetting it, a compression molding type anisotropic bonded magnet can be obtained. Further, by adding a thermoplastic binder to the coarse powder and injection molding it in a magnetic field, an injection molding type anisotropic bonded magnet can be obtained.
バインダー量については、４０ｖｏｌ％を越えるとバイ
ンダーによる非磁性部の増加により成形後の永久磁石体
が所定の磁気特性を発揮するととができず、１５ｖｏｌ
％未満では成形体の機械的性質が充分でなく、割れ、破
損等の欠陥を生じやすいため、１５〜４０ｖｏｌ％とし
た。Regarding the amount of binder, if it exceeds 40 vol%, the permanent magnet after molding will not be able to exhibit the desired magnetic properties due to an increase in the non-magnetic part due to the binder, and if the amount exceeds 15 vol.
If the amount is less than 15% by volume, the mechanical properties of the molded product will not be sufficient and defects such as cracks and breakage will easily occur.
Ｒ−Ｆｅ−Ｂ系合金の好ましい成分範囲は、以下の通り
である。The preferred range of components of the R-Fe-B alloy is as follows.
Ｒ（Ｙを含む希土類元素の１種又は２種以上の組み合せ
）が１１ａ１％未満の場合は充分なｉＨｃが得られず、
１８ａｔチを越えるとＢｒの低下が生ずる。。If R (one type or combination of two or more rare earth elements including Y) is less than 11a1%, sufficient iHc cannot be obtained,
When the temperature exceeds 18at, a decrease in Br occurs. .
よって、Ｒ量は１１〜１８＆ｔ％とした。Therefore, the R amount was set to 11 to 18&t%.
Ｂｔが４ ａｔ ％未満の場合は水系磁石の主相である
ＲｖＦｅｔ４Ｂ相の形成が充分でなく、Ｂｒ ｌ ＩＨ
（！ともに低い。又、Ｂ量が１８ａｔ％を越える場合は
、磁気特性的に好ましくない相の出現によ、９Ｂｒが低
下する。よって、Ｂｔは４〜１１ａｔ％としたＯＣｏ量
が３０ ａｔ％を越えるとキエーリ一点は向上するが主
相の異方性定数が低下し、高ｆＨｃが得られない。よっ
て、Ｃｏ景は３０ ａｔ ％以下とした０添加物量が０
．００１ａｔ％未満の場合は、添加物の効果が不充分で
あシ、３ａｔ％を越えるとＢｒの低下が大きく好ましく
ない。従って、添加物量は０．００１〜３ ａｔ’チと
した〇
なお、本発明の合金中にはフェロボロンに含まれる不純
物Ｎｄや他の希土類元素の還元の際に混入する還元材、
不純物が存在してもよい。When Bt is less than 4 at %, the formation of the RvFet4B phase, which is the main phase of the water-based magnet, is not sufficient, and Br l IH
(!Both are low. Also, when the amount of B exceeds 18 at%, 9Br decreases due to the appearance of a phase that is unfavorable in terms of magnetic properties. Therefore, the amount of OCo is 30 at% while Bt is 4 to 11 at%. If it exceeds 30 at %, the Chieri point will improve, but the anisotropy constant of the main phase will decrease and high fHc will not be obtained.
．． If it is less than 0.001 at%, the effect of the additive will be insufficient, and if it exceeds 3 at%, the Br will drop significantly, which is not preferred. Therefore, the amount of additives was set at 0.001 to 3 at'. Note that the alloy of the present invention contains reducing agents that are mixed in when reducing the impurity Nd contained in ferroboron and other rare earth elements.
Impurities may be present.
前記バインダーとして使用しうる材料としては圧縮成形
の場合は熱硬化性樹脂が最も使いやすい。As for the material that can be used as the binder, thermosetting resin is most easily used in the case of compression molding.
熱的に安定なポリアミド、ポリイミド、ポリエステル、
フェノール、フッ素、ケイ素、エポキシ等が利用できる
。又、Ａｔ、 Ｓｎ 、 Ｐｂおよび各種低融点ハンダ
合金を使用することができる。射出成形の場合は、ＥＶ
Ａ、ナイロン等の熱硬化性樹脂が用途に応じ利用できる
。Thermally stable polyamide, polyimide, polyester,
Phenol, fluorine, silicon, epoxy, etc. can be used. Also, At, Sn, Pb and various low melting point solder alloys can be used. For injection molding, EV
A. Thermosetting resins such as nylon can be used depending on the purpose.
以下実施例により本発明を更に詳細に説明する。 The present invention will be explained in more detail with reference to Examples below.
実施例１
Ｎｄｌ、 Ｆｅ、５ Ｂ、合金をアーク溶解により作成
し、本合金をＡｒ′＃囲気中で単ロールによりフレーク
状薄片を作製した。ロール周速は３０ ｍ／ｓｅｃで得
られた薄片は約３０μｍの厚さをもった不定形でありＸ
線の結果、非晶質と結晶質の混合物であることが解った
。この薄片を３２メツシユ以下となるように粗粉砕し、
金型成形により成形体を作製した。成形圧は６ ｔｏｎ
ｙ佃であシ、磁場印加は行っていない。Example 1 An alloy of Ndl, Fe, 5B was prepared by arc melting, and flakes of this alloy were prepared by a single roll in an Ar'# atmosphere. The peripheral speed of the roll was 30 m/sec, and the flakes obtained were irregularly shaped with a thickness of about 30 μm.
The line results showed that it was a mixture of amorphous and crystalline materials. Coarsely crush this flake to 32 meshes or less,
A molded body was produced by molding. Molding pressure is 6 tons
At Tsukuda, no magnetic field was applied.
成形体の密度は５ 、８ Ｐ／ｃｃである。得られた成
形体を７００℃でホットプレスした。ホットプレスの温
度は７００℃で圧力は２ ｔｏｎ／ｉであるＯホットプ
レスによって得られた密度は７ 、５０ Ｆ／ｃｃでホ
ットプレスによって高密度化が充分はかられた０高密度
化されたバルク体を更に７００℃ですえ込み加工した。The density of the molded body is 5.8 P/cc. The obtained molded body was hot pressed at 700°C. The temperature of the hot press was 700°C and the pressure was 2 ton/i.The density obtained by the hot press was 7. The density obtained by the hot press was 7. The bulk body was further processed at 700°C.
試料の高さはすえ込み加工の前後で圧縮比率が３になる
ように調整した。（す見込み前の高さをｈＯとし、すえ
込み後の高さをｈとするとｈｏ／ｈ ＝ ３ ）
すえ込み加工された試料を粗粉砕し、２５０〜５００μ
ｍの粒度範囲になるように調整し、磁粉を得た。本磁粉
に１６ｖｏｌ％のエポキシ樹脂を乾式で混合し、この粉
末を内径３８ｍＸ２０ｍｍの金型内にＩＥＭ充てんし、
６ｔｏｎ／ＣＩＡの加圧力、１０ＫＯｅの磁場中で横磁
場成形した。次に１２０℃Ｘ ３ ｈｒｓの熱硬化処理
を施して異方性ボンド磁石とした。得られた異方性ボン
ド磁石は、２５ＫＯｅＯ着磁磁場強度で測定するとＢｒ
〜６．８ＫＧ 、 ＢＨｃ 〜６．３ＫＯｅ ＊ｉＨ
ｃ 〜１２．３ＫＯｅ 、 （ＢＨ）ｍａｘ 〜１０．
６ＭＧＯｅの磁気特性が得られた。The height of the sample was adjusted so that the compression ratio was 3 before and after swaging. (If the height before swaging is hO and the height after swaging is h, then ho/h = 3) The swaging processed sample is coarsely ground to a size of 250 to 500μ.
Magnetic powder was obtained by adjusting the particle size to be within the particle size range of m. This magnetic powder is mixed with 16 vol% epoxy resin in a dry method, and this powder is filled into a mold with an inner diameter of 38 m x 20 mm using an IEM.
Transverse magnetic field molding was carried out under a pressure of 6 tons/CIA and a magnetic field of 10 KOe. Next, a thermosetting treatment was performed at 120° C. for 3 hrs to obtain an anisotropic bonded magnet. The obtained anisotropic bonded magnet has Br when measured at a magnetic field strength of 25KOeO.
~6.8KG, BHc ~6.3KOe *iH
c ~12.3KOe, (BH)max ~10.
Magnetic properties of 6MGOe were obtained.
比較のために、Ｎｄ１７ Ｆｅ７６ Ｂｅなる組成の超
急冷した薄片を真空中で６００℃Ｘ１ｈｒの熱処理し、
２５０〜５００μｍに粗粉砕し本実施例と同様の方法で
ボンド磁石とした。ただし、本ボンド磁石は等方性であ
るため圧縮成形の際、磁場印加を行っていない０２５Ｋ
Ｏｅの着磁磁場強度によって得られる磁気特性はＢｒ
〜５．９Ｋ Ｏｅ 、 ＢＨｃ 〜４．９ＫＯｅ ｔ
ｉＨｃ〜１２ 、８ＫＯｅ ＊ （ＢＨ）ｍａｘ 〜６
、６ＭＧＯｅであった。For comparison, an ultra-quenched thin piece of Nd17Fe76Be was heat-treated at 600°C for 1 hr in vacuum.
It was coarsely pulverized to 250 to 500 μm and made into a bonded magnet in the same manner as in this example. However, since this bonded magnet is isotropic, no magnetic field is applied during compression molding at 025K.
The magnetic properties obtained by the magnetizing magnetic field strength of Oe are Br
〜5.9KOe, BHc 〜4.9KOet
iHc~12, 8KOe*(BH)max~6
, 6MGOe.
異方性ボンド磁石は等方性ボンド磁石と比較して、着磁
性が良好で高い磁気特性が得られることが分かる。又比
較のために粉末冶金法で製造した焼結フェライト磁石を
用いた。製法は最も一般的な原料混合、仮焼、粉砕およ
び造粒の後粉末プレス成形、焼成の工程で行なった等方
性フェライト磁石を選んだ。２５ＫＯｅＯ着磁磁場強度
によりて得られる磁気特性はＢｒ 〜４．２ ＫＧ ｒ
ＢＨｃ−３，２ＫＯｅ ｅ量Ｈｃ 〜４ 、０ＫＯａ
ｍ （ＢＨ）ｍａｘ 〜３ 、９ＭＧＯｅであった。It can be seen that anisotropic bonded magnets have better magnetization and higher magnetic properties than isotropic bonded magnets. For comparison, a sintered ferrite magnet manufactured by powder metallurgy was used. We selected an isotropic ferrite magnet that was manufactured using the most common process of mixing raw materials, calcination, pulverization, and granulation, followed by powder press molding and firing. The magnetic properties obtained by the 25KOeO magnetizing magnetic field strength are Br ~ 4.2 KG r
BHc-3,2KOe e amount Hc ~4, 0KOa
m (BH)max ~3, 9MGOe.
このようにＮｄ −Ｆｅ −Ｂ異方性ボンド磁石と比較
し、かなシ低い値であることが分かる。In this way, it can be seen that the kana value is lower than that of the Nd-Fe-B anisotropic bonded magnet.
以上、実施例１で得られた結果を比較例とあわせて第１
表に示す。Above, the results obtained in Example 1 are combined with the comparative example.
Shown in the table.
第 １ 表
実施例２゜
次に実施例１に示した製法で異方性ボンド磁石を成形す
る際、加圧力が磁気特性にどのような影響を与えるかを
示す０組成、超急冷、ホットプレス、模磁場成形、熱硬
化等条件は実施例１と同様である。Table 1 Example 2 Next, when forming an anisotropic bonded magnet using the manufacturing method shown in Example 1, how the pressing force affects the magnetic properties is shown. Conditions such as magnetic field molding, thermosetting, etc. are the same as in Example 1.
結果を第２表に示す。第２表に示した磁気特性は、着磁
強度２５ＫＯｅにて得られた値である。第２表に示した
通り、加圧力を増加することにより、密度が上が）磁気
特性は向上する。なお加圧力２ｔｏｎ／ｉでも実施例１
中に記したフェライト磁石よりもかなり高い特性を示す
ことが分かる。The results are shown in Table 2. The magnetic properties shown in Table 2 are values obtained at a magnetization strength of 25 KOe. As shown in Table 2, by increasing the pressing force, the density increases and the magnetic properties improve. In addition, even if the pressing force is 2 ton/i, Example 1
It can be seen that the characteristics are considerably higher than those of the ferrite magnets mentioned above.
第 ２ 表
実施例３
本磁粉に１６ｖｏｌ％のエポキシ樹脂を乾式で混合した
粉末で実際にｒｌ”＝ ４６．８ｍ 、 ｒ２＝ ４６
６８ｍ 。Table 2 Example 3 This magnetic powder was mixed with 16 vol% epoxy resin in a dry process, and the actual results were as follows: rl" = 46.8 m, r2 = 46
68m.
θ＝７５になる様設計した金型に充てんし、アークセグ
メント形の異方性ボンドスタータセータ用磁石を試作し
た。任意の箇所の磁気特性および寸法、精度１表面鞘状
についてｖ！４食した。A mold designed so that θ=75 was filled with the material, and an arc segment type anisotropic bonded starter magnet was prototyped. Magnetic properties and dimensions at any location, accuracy 1 v! for surface sheath shape! I ate 4 meals.
なお組成、超急冷、ホットプレス、横磁場成形。Composition, ultra-quenching, hot pressing, transverse magnetic field forming.
熱硬化等条件は実施例１と同様である。Conditions such as heat curing are the same as in Example 1.
磁気特性は、前記磁石を端部から中央部まで１０カ所３
×３×３ＩＩＩ＋の寸法に切り出し、２５ＫＯｅ。The magnetic properties are determined by placing the magnet in 10 locations from the end to the center.
Cut to size x3 x 3III+, 25KOe.
着磁強度で測定した結果Ｂｒ：６−５〜６．８ ＫＧ
。Results measured by magnetization strength Br: 6-5 to 6.8 KG
.
ＢＨｃ ６．１〜６．３ ＫＯｅ 、 ｉＨｃ
１２．３ ＫＯｅ、（ＢＨ）ｍａｘｌ ０ 、６ Ｍ
ＧＯｅであり、密度との相対関係も一致してお９かなり
均一化した磁石であることが分かる。BHc 6.1-6.3 KOe, iHc
12.3 KOe, (BH)maxl 0, 6 M
It can be seen that the magnet is GOe and the relative relationship with the density is also consistent, making it a fairly uniform magnet.
寸法精度は金型寸法と熱処理硬化後の寸法を測定した結
果、金型θに対し、±０．２°の精度でありた。また厚
さ方向では、目標値３１ａｌｌに対し、充てん量を段階
的に変化させ、最終的には±０．０５ｍの精度で正確に
圧縮成形することができ、ニアネットシェープのスター
タモータ磁石が製作可能である。As for the dimensional accuracy, as a result of measuring the mold dimensions and the dimensions after heat treatment and hardening, the accuracy was ±0.2° with respect to the mold θ. In addition, in the thickness direction, the filling amount can be changed in stages with respect to the target value of 31all, and the final compression molding can be performed accurately with an accuracy of ±0.05m, producing a near net shape starter motor magnet. It is possible.
表面鞘状は、ポンドと粉末が均一に充てんするため、７
エ２イトの焼結直後の状態よシもかなシ良く、１．６Ｓ
程度と内面研磨を施す必要はないものと判断できる。The surface sheath shape allows the pound and powder to be filled uniformly, so
The state of E2ite immediately after sintering is good, 1.6S
It can be judged that there is no need to perform internal polishing.
上記の異方性ボンド磁石を自動車用スタータモータに組
み込み、通常の条件でテストしたところ、同形状のＳｒ
フェライト磁石と比ベモータ出力は、１．０５〜１．４
０倍に向上することが確認できた。When the above anisotropic bonded magnet was incorporated into an automobile starter motor and tested under normal conditions, it was found that Sr.
The motor output compared to the ferrite magnet is 1.05 to 1.4.
It was confirmed that the improvement was 0 times.
Claims (7)
Ｆｅ−Ｂ系合金粉（ＲはＹを含む１種又は２種以上の希
土類元素、又Ｆｅの１部をＣｏで置換したＲ−ＦｅＣｏ
−Ｂ系合金を含み、更に添加元素（Ｍ）として、Ｓｉ、
Ａｔ、Ｎｂ、Ｚｒ、Ｈｆ、Ｍｏ、Ｇａ、Ｐ、Ｃ、の１種
又は２種以上の組み合せを用いたＲ−Ｆｅ−Ｂ−Ｍ系、
Ｒ−Ｆｅ−Ｃｏ−Ｂ−Ｍ系合金を含む）を１５〜４０ｖ
ｏｌ％のバインダーと混練し、磁場中圧縮成形、磁場中
射出成形その他の機械加工により製造されたことを特徴
とするスタータモータ用ボンド磁石。(1) R- with an average crystal grain size of 0.01 to 0.5 μm
Fe-B alloy powder (R is one or more rare earth elements including Y, or R-FeCo in which a part of Fe is replaced with Co)
- Contains a B-based alloy, and further contains Si, as an additional element (M),
R-Fe-B-M system using one or a combination of two or more of At, Nb, Zr, Hf, Mo, Ga, P, C,
R-Fe-Co-B-M alloy) from 15 to 40v
1. A bonded magnet for a starter motor, characterized in that the bonded magnet is kneaded with a binder of 0.1% and manufactured by compression molding in a magnetic field, injection molding in a magnetic field, and other machining processes.
、Ｂ：４〜１１ａｔ％、Ｃｏ：３０ａｔ％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
記載のスタータモータ用ボンド磁石。(2) R-Fe-B alloy powder has R: 11 to 18 at%
, B: 4 to 11 at%, Co: 30 at% or less, remainder:
A bonded magnet for a starter motor according to claim 1, comprising Fe and unavoidable impurities.
フレークをＨＩＰ、ホットプレスにより高密度化後、塑
性変形により異方性化した素材を粗粉砕して得られる磁
粉を用いることを特徴とする特許請求の範囲第１項記載
のスタータモータ用ボンド磁石。(3) Use magnetic powder obtained by coarsely pulverizing the flakes of R-Fe-B alloy powder obtained by ultra-quenching, densifying them by HIP and hot pressing, and making the material anisotropic by plastic deformation. A bonded magnet for a starter motor according to claim 1, characterized in that:
工としたことを特徴とする特許請求の範囲第１項記載の
スタータモータ用ボンド磁石。(4) The bonded magnet for a starter motor according to claim 1, characterized in that warm swaging is used as the means for imparting the plastic deformation.
あることを特徴とする特許請求の範囲第１項記載のスタ
ータモータ用ボンド磁石。(5) The bonded magnet for a starter motor according to claim 1, wherein the amount of the additional element added is 0.001 to 3 at%.
２５ｍｍ以下の形状を有する射出成形により成形された
特許請求の範囲第１項記載のスタータモータ用ボンド磁
石。(6) The bonded magnet for a starter motor according to claim 1, which is molded by injection molding and has a shape with an inner diameter of 10 to 15 mm, an outer diameter of 13 to 18 mm, and a height of 25 mm or less.
れた特許請求の範囲第１項記載のスタータモータ用ボン
ド磁石。(7) The bonded magnet for a starter motor according to claim 1, which is formed into a near-net shape by compression molding.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61104357A JPS62261102A (en) | 1986-05-07 | 1986-05-07 | Bonded magnet for starter motor |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61104357A JPS62261102A (en) | 1986-05-07 | 1986-05-07 | Bonded magnet for starter motor |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS62261102A true JPS62261102A (en) | 1987-11-13 |
Family
ID=14378604
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP61104357A Pending JPS62261102A (en) | 1986-05-07 | 1986-05-07 | Bonded magnet for starter motor |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS62261102A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH03227502A (en) * | 1988-10-04 | 1991-10-08 | Hitachi Metals Ltd | Heat-resisting bond magnet and its manufacture and pm motor |
| EP0772211A1 (en) * | 1995-11-06 | 1997-05-07 | Seiko Epson Corporation | Rare earth bonded magnet, rare earth magnetic composition, and method for manufacturing rare earth bonded magnet |
| FR2822903A1 (en) * | 2001-03-30 | 2002-10-04 | Mitsubishi Electric Corp | Starter for internal combustion engine, comprises wound rotor and rare earth permanent field magnets also switch which energises rotor and directly engages rotor pinion to engine using electromagnet |
-
1986
- 1986-05-07 JP JP61104357A patent/JPS62261102A/en active Pending
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH03227502A (en) * | 1988-10-04 | 1991-10-08 | Hitachi Metals Ltd | Heat-resisting bond magnet and its manufacture and pm motor |
| EP0772211A1 (en) * | 1995-11-06 | 1997-05-07 | Seiko Epson Corporation | Rare earth bonded magnet, rare earth magnetic composition, and method for manufacturing rare earth bonded magnet |
| KR100238371B1 (en) * | 1995-11-06 | 2000-01-15 | 야스카와 히데아키 | Rare-earth bonded magnet, rare-earth bonded magnetic composition and method for manufacturing rare-earth bonded magnet |
| FR2822903A1 (en) * | 2001-03-30 | 2002-10-04 | Mitsubishi Electric Corp | Starter for internal combustion engine, comprises wound rotor and rare earth permanent field magnets also switch which energises rotor and directly engages rotor pinion to engine using electromagnet |
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