JPS62262403A - Manufacture of rare earth permanent magnet - Google Patents
Manufacture of rare earth permanent magnetInfo
- Publication number
- JPS62262403A JPS62262403A JP61105966A JP10596686A JPS62262403A JP S62262403 A JPS62262403 A JP S62262403A JP 61105966 A JP61105966 A JP 61105966A JP 10596686 A JP10596686 A JP 10596686A JP S62262403 A JPS62262403 A JP S62262403A
- Authority
- JP
- Japan
- Prior art keywords
- rare earth
- ingot
- permanent magnet
- iron
- earth permanent
- 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
- 229910052761 rare earth metal Inorganic materials 0.000 title claims abstract description 20
- 150000002910 rare earth metals Chemical class 0.000 title claims abstract description 18
- 238000004519 manufacturing process Methods 0.000 title claims description 9
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 26
- 229910052742 iron Inorganic materials 0.000 claims abstract description 13
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims abstract description 10
- 229910052796 boron Inorganic materials 0.000 claims abstract description 10
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 8
- 239000000956 alloy Substances 0.000 claims abstract description 8
- 238000010438 heat treatment Methods 0.000 claims abstract description 8
- 238000000034 method Methods 0.000 claims description 10
- 239000000203 mixture Substances 0.000 claims description 9
- 150000003624 transition metals Chemical group 0.000 claims description 3
- 229910017052 cobalt Inorganic materials 0.000 claims description 2
- 239000010941 cobalt Substances 0.000 claims description 2
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 claims description 2
- 230000005415 magnetization Effects 0.000 claims description 2
- 229910052723 transition metal Inorganic materials 0.000 claims 1
- 229910052684 Cerium Inorganic materials 0.000 abstract description 2
- 229910052779 Neodymium Inorganic materials 0.000 abstract description 2
- 229910052727 yttrium Inorganic materials 0.000 abstract description 2
- 229910052777 Praseodymium Inorganic materials 0.000 abstract 1
- 229910052746 lanthanum Inorganic materials 0.000 abstract 1
- 230000000052 comparative effect Effects 0.000 description 8
- 238000000227 grinding Methods 0.000 description 7
- 238000005266 casting Methods 0.000 description 6
- 239000000835 fiber Substances 0.000 description 5
- 238000010586 diagram Methods 0.000 description 4
- 238000002844 melting Methods 0.000 description 4
- 230000008018 melting Effects 0.000 description 4
- 239000000843 powder Substances 0.000 description 4
- 238000000465 moulding Methods 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- 229910000722 Didymium Inorganic materials 0.000 description 2
- 241000224487 Didymium Species 0.000 description 2
- 229910052692 Dysprosium Inorganic materials 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 239000006247 magnetic powder Substances 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 229910052693 Europium Inorganic materials 0.000 description 1
- 229910052689 Holmium Inorganic materials 0.000 description 1
- 229910052765 Lutetium Inorganic materials 0.000 description 1
- 229910052772 Samarium 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
- 230000032683 aging Effects 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- GWXLDORMOJMVQZ-UHFFFAOYSA-N cerium Chemical compound [Ce] GWXLDORMOJMVQZ-UHFFFAOYSA-N 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- -1 l1ir Inorganic materials 0.000 description 1
- 238000010309 melting process Methods 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 238000010298 pulverizing process Methods 0.000 description 1
- 239000000700 radioactive tracer Substances 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 238000004904 shortening Methods 0.000 description 1
- 238000005245 sintering 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
- 238000004857 zone melting Methods 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
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、基本組成が希土類金属、鉄およびボロンから
なる希土類永久磁石の製造方法に閃する〔従来の技術〕
従来、基本組成が希土類金属、鉄およびボロンからなる
合金インゴットのマクロ組識を柱状組該とするために、
鋳造金型の構造の改良などにより鋳造後の冷却速度を制
御していた。[Detailed Description of the Invention] [Industrial Application Field] The present invention relates to a method for producing a rare earth permanent magnet whose basic composition is a rare earth metal, iron, and boron [Prior Art] Conventionally, the basic composition is a rare earth metal, iron, and boron. In order to make the macrostructure of an alloy ingot consisting of iron and boron into a columnar structure,
The cooling rate after casting was controlled by improving the structure of the casting mold.
しかしながら、上記の手段は数tの溶解では可能である
が、数十〜数百tの溶解では極めてFf(Mであり、か
つ鋳造組識が完全には得られず、さらに溶解工程に時間
が要するなど社産には向いていないといった問題点を有
している。However, although the above method is possible with melting of several tons, melting of tens to hundreds of tons results in extremely low Ff (M), and the casting structure cannot be completely obtained, and the melting process takes a long time. It has problems such as the fact that it is not suitable for company production.
本発明は以上の問題点を解決するもので、その目的とす
るところは、数十〜数百tといった量産時の溶解におい
ても、インゴットのマクロ組識を柱状組識とし、磁気性
能を向上させ品質を安定させる希土類永久磁石の製造方
法を提供することにある。The present invention solves the above problems, and its purpose is to make the macrostructure of the ingot into a columnar structure and improve the magnetic performance even during melting during mass production of tens to hundreds of tons. The purpose of the present invention is to provide a method for manufacturing rare earth permanent magnets that stabilizes quality.
本発明の希土類永久磁石の製造方法は、基本組成が希土
類金属、鉄およびボロンからなり、ゾーン加熱法により
インゴットのマクロ組識を柱状組繊とした合金を使用し
て磁石化することを特徴とする。The method for producing a rare earth permanent magnet of the present invention is characterized in that the basic composition is a rare earth metal, iron, and boron, and magnetization is performed using an alloy in which the macrostructure of an ingot is made into columnar fibers by a zone heating method. do.
一般に溶融金属がるつぼから鋳型に鋳こまれたとき、溶
融金属は先ず鋳型壁と接触して、おびただしい核生成を
生じる程度1で急冷され、チル層を形成する。次に、鋳
型へ熱が流れるため、鋳型壁に垂直に内部に向かって柱
状組繊が伸びてくる。さらに熱の流れがなくなると、柱
状組繊にかわり等軸組識が現れ、鋳型内での凝固が完了
する。Generally, when molten metal is poured from a crucible into a mold, the molten metal first contacts the walls of the mold and is rapidly cooled to a degree of 1 which causes extensive nucleation, forming a chill layer. Next, as heat flows into the mold, the columnar fibers extend inward perpendicular to the mold wall. When the heat flow further ceases, an equiaxed structure appears instead of a columnar structure, and solidification in the mold is completed.
したがって、第2図に示すように、鋳造時のマクロ組識
はチル組誠(1’I 、柱状組繊(2)および等軸組識
(3,)から形成される。Therefore, as shown in FIG. 2, the macrostructure at the time of casting is formed of a chilled structure (1'I), a columnar structure (2), and an equiaxed structure (3,).
基本組成が希土類金属、鉄およびボロンからなるインゴ
ットのマクロ組識を柱状組誠とすることにより、インゴ
ットの粉砕性が向上し、さらに得られる永久磁石の磁気
性能も向上する。By making the macrostructure of the ingot whose basic composition is a rare earth metal, iron, and boron into a columnar structure, the crushability of the ingot is improved, and the magnetic performance of the obtained permanent magnet is also improved.
しかし、前述のように、インゴットのマクロ組識を柱状
組麟とすることは、特に泣産時に困難となりてくる。However, as mentioned above, it is difficult to make the macrostructure of the ingot into a columnar structure, especially when the ingot is in a cryogenic state.
そこで、鋳造上がりのインゴットを第1図に示すように
、ゾーンメルティングやゾーンリファイニングと同様な
装置を用い、インゴットの一部分を帯状に溶融し、この
帯域(ゾーン)を移動させることにより、異方性結晶成
長が可能となり、柱状組鎮が得られるのである。Therefore, as shown in Figure 1, a part of the ingot after casting is melted in a band shape using equipment similar to zone melting or zone refining, and this zone is moved. Oriental crystal growth becomes possible, and a columnar structure can be obtained.
なお、基本組成が希土類金属、鉄およびボロンからなる
希土類永久磁石としては゛Na−?θ−B磁石が知られ
ているが、希土類金にとしては、Y、La、Oe、Pr
、Nd、Pm、Sm、Eu。In addition, as a rare earth permanent magnet whose basic composition is rare earth metal, iron, and boron, there is "Na-?" θ-B magnets are known, but examples of rare earth gold include Y, La, Oe, and Pr.
, Nd, Pm, Sm, Eu.
Gd、T’b、Dy、Ho、l1ir、Tm、Ybおよ
びLuの希土類元素のうちの1種または2種以上であれ
ば良く、ジジム(Pr−Na)やセリウム・ジジム(O
e−P r−N d)でも十分な磁気性能が得られ、供
給面・価格面から有利である。さらに、DyやTb等の
重希土類元素の少量添加により、保磁力1Hcを増大さ
せることができ、温度特性の実質的な改善が達成される
。Any one or more of the rare earth elements Gd, T'b, Dy, Ho, l1ir, Tm, Yb and Lu may be used, and didymium (Pr-Na) and cerium didymium (O
e-P r-N d) can also provide sufficient magnetic performance and is advantageous from the standpoint of supply and price. Furthermore, by adding a small amount of heavy rare earth elements such as Dy and Tb, the coercive force 1Hc can be increased and a substantial improvement in temperature characteristics can be achieved.
また、鉄の一部をコバルトでfil決することによりキ
ューリ一温度の向上が計られ、他の遷移金属群でtif
換しても磁気性能や耐食性等が改善される〔実施例〕
以下、本発明について実施例に基づいて詳細に説明する
。In addition, by filling part of iron with cobalt, the Curie temperature was improved, and with other transition metal groups, tif
[Example] The present invention will be described in detail based on Examples below.
(実施例−1)
Nd15?e77]3g の組成になるように高周波溶
解炉を用いアルゴンガスB)囲気下で溶解、鋳造し、3
0KPの合金を得た。得られたインゴットには、柱状組
成は、わずかしか含まれてなく、はとんどが等軸m緑で
あった。このインゴットを第1図に示す装置を用い、ゾ
ーン加熱を施したところ、はぼ完全に柱状組戯となった
。(Example-1) Nd15? Melt and cast in a high-frequency melting furnace under argon gas B) atmosphere so that the composition becomes 3g.
An alloy of 0KP was obtained. The obtained ingot contained only a small amount of columnar composition and was mostly equiaxed green. When this ingot was subjected to zone heating using the apparatus shown in FIG. 1, it became almost completely columnar.
また、比較例として、柱状組繊がわずがしか含んでいな
い鋳造上がりのインゴットも用意した。As a comparative example, a cast ingot containing only a small amount of columnar fibers was also prepared.
これらのインゴットをスタンプミルな用い一#32メツ
シュの粉末とし、ボールミルを用い粉砕時間を変えて微
粉砕し、その時の粉末の平均粒径を1・S−5−S・を
用い測定した。These ingots were made into powder with a #32 mesh using a stamp mill, and finely ground using a ball mill while changing the grinding time, and the average particle size of the powder was measured using a 1.S-5-S.
その結果を第3図に示す。The results are shown in FIG.
第3図より明らかなように、比較例と比べ、本発明は短
い時間で微粉末となっていることが分かる。インゴット
のマクロ組識を比べてみても、本発明の方が完全な柱状
組繊になっていることからも、マクロ組識を柱状組繊と
することにより、粉砕性が向上し、たといえる。As is clear from FIG. 3, it can be seen that the powder of the present invention becomes fine powder in a shorter time than that of the comparative example. Comparing the macrostructures of the ingots, the ingots of the present invention have more complete columnar fibers, so it can be said that the crushability is improved by making the macrostructure into columnar fibers.
(実施例−2)
NdlL5D7L5’!8670010BB となる
ように、実施例−1と同様の方法を用い、粉砕時間を変
えて微粉砕し、本発明と比較例の所定の磁性粉末を作成
した。この磁性粉末を15KOeの磁場中で配向させて
154/、、ノの成形圧で圧l?1成形させ、アルコン
ガス雰囲気中で1000〜1200tl’)/i適温度
で焼結、400〜1000℃の最適温度で時効を施した
。(Example-2) NdlL5D7L5'! 8670010BB, using the same method as in Example-1, changing the grinding time, to create predetermined magnetic powders of the present invention and comparative examples. This magnetic powder was oriented in a magnetic field of 15 KOe, and the molding pressure was 154/. 1 molding, sintering at an appropriate temperature of 1000 to 1200 tl'/i in an Alcon gas atmosphere, and aging at an optimum temperature of 400 to 1000°C.
得られた磁石なりHトレーサーを用い磁気性能を測定し
た。得られた磁気性能のうち最も大きなポイントとなる
保磁力(iHc)と粉砕時間との関係を第4図に示す。Magnetic performance was measured using the obtained magnet or H tracer. FIG. 4 shows the relationship between the coercive force (iHc), which is the most significant point in the obtained magnetic performance, and the grinding time.
第4図から明らかだが、比較例と比べ、本発明は短い時
間でiHcが最大値に到達していて、かつその最大値も
大きな値とならている。すなわち、マクロ組識を柱状組
鎗とすることにより、単に粉砕性が向上するだけでなく
、得られる磁石の磁気性能を改善させるのである。As is clear from FIG. 4, iHc reaches the maximum value in a shorter time in the present invention than in the comparative example, and the maximum value is also a large value. That is, by forming the macrostructure into a columnar molding, not only the crushability is improved, but also the magnetic performance of the resulting magnet is improved.
(実施例−3)
(Osへ2PrO,1N110.SD7α1)ls?e
sToolOBaの合金を振動ミルを用いて粉砕時間を
変えて微粉砕し、実施例−1と同様の方法を用−1本発
明と比較例の所定の磁石を作成した。(Example-3) (2PrO to Os, 1N110.SD7α1)ls? e
The alloy of sToolOBa was finely pulverized using a vibration mill while changing the pulverization time, and the same method as in Example 1 was used to create predetermined magnets of the present invention and comparative example.
同様に保磁力(iHc)と粉砕時間の関係を第5図に示
した。Similarly, the relationship between coercive force (iHc) and grinding time is shown in FIG.
第5図から明らかなように、本発明ではボールミルを用
いたときに比べると・多少低い1Hcとなっているが十
分実用になるのに対し、比較例では満足なiHcを得る
ことはできなかった。As is clear from Fig. 5, in the present invention, 1Hc is somewhat lower than when using a ball mill, but it is sufficiently practical, whereas in the comparative example, it was not possible to obtain a satisfactory iHc. .
以上述べたように、本発明によれば、基本組成が希土類
金属、鉄およびボロンからなり、ゾーン加熱法によりイ
ンゴットのマクロ組識を柱状組識とした合金を使用して
磁石化することにより、従来に比べて粉砕性が向上し、
粉砕工程に要する時間が大幅に短縮されるだけでなく、
得られる永久磁石の磁気性能をも大きく改善され、特に
ボールミルに比べて粉砕効率が格段に良く大量生産には
欠かすことができない振動ミルを用いても、十分実用と
なるfIi気性能が得られるようになり、工程時間の短
縮、址産の向上、コストダウン、品質の安定性などに多
大の効果を有するものである。As described above, according to the present invention, by magnetizing using an alloy whose basic composition consists of rare earth metals, iron, and boron, and which has a columnar structure in the macro structure of the ingot by the zone heating method, Improved crushability compared to conventional methods,
Not only is the time required for the crushing process significantly reduced;
The magnetic performance of the resulting permanent magnet has also been greatly improved, and in particular, the crushing efficiency is much better than that of a ball mill, and even when using a vibration mill, which is indispensable for mass production, sufficient fIi performance can be obtained for practical use. This has great effects in shortening process time, improving yield, reducing costs, and stabilizing quality.
第1図は、本発明のゾーン加熱法を示す図。
1・・・・・・帯状加熱装置
2・・・・・・柱状組識部
3・・・・・・未処理部
第2図は、鋳造時のインゴットの断面図。
1・・・・・・チル組識
2・・・・・・柱状組識
3・・・・・・等軸組識
fg3図は、本発明と比較例の粉砕時間と平均粒径の関
係図。
第4図は、本発明と比較例の粉砕時間と保磁力(1HO
)の関係図。
第5図は、振動ミルでの本発明と比較例の粉砕時間と保
磁力(iHo )の関係図である。
以 上
出願人 セイコーエプソン株式会社
/ z 6− ノo 20
Δ12 /ρ0 2er。
メ分紳13待関 口にYコ
第3図
/ 2 夕 10 20 rO1w 2
ρ0料降時間〔し〕
第4図
ケ 10 Z117 rO/co
2a。
顔耕日侍間[y−4〕
第5図FIG. 1 is a diagram showing the zone heating method of the present invention. 1... Strip heating device 2... Column structure portion 3... Untreated portion FIG. 2 is a sectional view of the ingot during casting. 1... Chill structure 2... Column structure 3... Equiaxed structure fg3 Figure is a diagram showing the relationship between grinding time and average particle size of the present invention and comparative example. . Figure 4 shows the grinding time and coercive force (1HO
) relationship diagram. FIG. 5 is a diagram showing the relationship between the grinding time and coercive force (iHo) of the present invention and a comparative example using a vibratory mill. Applicant: Seiko Epson Corporation/Z6-No.20
Δ12/ρ0 2er. Mebushin 13 Machi Seki Yko figure 3 at the mouth / 2 Evening 10 20 rO1w 2
ρ0 shipping time [shi] Figure 4 ke 10 Z117 rO/co
2a. Face Koichi Samurai [y-4] Figure 5
Claims (2)
、ゾーン加熱法によりインゴットのマクロ組識を柱状組
識とした合金を使用して磁石化することを特徴とする希
土類永久磁石の製造方法。(1) A method for producing a rare earth permanent magnet, characterized in that the basic composition is a rare earth metal, iron, and boron, and magnetization is performed using an alloy in which the macrostructure of the ingot is a columnar structure by a zone heating method.
属群から選ばれた少なくとも1種以上の遷移金属群で置
換した特許請求の範囲第1項記載の希土類永久磁石の製
造方法。(2) The method for producing a rare earth permanent magnet according to claim 1, wherein a part of the iron is replaced with at least one transition metal group selected from the group of transition metals other than iron, such as cobalt.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP61105966A JPS62262403A (en) | 1986-05-09 | 1986-05-09 | Manufacture of rare earth permanent magnet |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP61105966A JPS62262403A (en) | 1986-05-09 | 1986-05-09 | Manufacture of rare earth permanent magnet |
Publications (1)
Publication Number | Publication Date |
---|---|
JPS62262403A true JPS62262403A (en) | 1987-11-14 |
Family
ID=14421527
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP61105966A Pending JPS62262403A (en) | 1986-05-09 | 1986-05-09 | Manufacture of rare earth permanent magnet |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS62262403A (en) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US5431747A (en) * | 1992-02-21 | 1995-07-11 | Tdk Corporation | Master alloy for magnet production and a permanent alloy |
-
1986
- 1986-05-09 JP JP61105966A patent/JPS62262403A/en active Pending
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US5431747A (en) * | 1992-02-21 | 1995-07-11 | Tdk Corporation | Master alloy for magnet production and a permanent alloy |
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