JPS63157844A - Manufacture of permanent magnet material - Google Patents
Manufacture of permanent magnet materialInfo
- Publication number
- JPS63157844A JPS63157844A JP61302625A JP30262586A JPS63157844A JP S63157844 A JPS63157844 A JP S63157844A JP 61302625 A JP61302625 A JP 61302625A JP 30262586 A JP30262586 A JP 30262586A JP S63157844 A JPS63157844 A JP S63157844A
- Authority
- JP
- Japan
- Prior art keywords
- weight
- stage aging
- hours
- sintering
- permanent magnet
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 239000000463 material Substances 0.000 title claims abstract description 9
- 238000004519 manufacturing process Methods 0.000 title claims description 5
- 230000032683 aging Effects 0.000 claims abstract description 38
- 238000001816 cooling Methods 0.000 claims abstract description 19
- 239000000956 alloy Substances 0.000 claims abstract description 11
- 229910052761 rare earth metal Inorganic materials 0.000 claims abstract description 9
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 8
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 5
- 229910052802 copper Inorganic materials 0.000 claims abstract description 4
- 239000000203 mixture Substances 0.000 claims description 16
- 238000005245 sintering Methods 0.000 abstract description 21
- 238000010438 heat treatment Methods 0.000 abstract description 16
- 229910052742 iron Inorganic materials 0.000 abstract description 3
- 239000010949 copper Substances 0.000 description 17
- 239000010955 niobium Substances 0.000 description 16
- 238000000034 method Methods 0.000 description 15
- 238000005259 measurement Methods 0.000 description 9
- 230000005415 magnetization Effects 0.000 description 6
- 230000007423 decrease Effects 0.000 description 5
- 230000000694 effects Effects 0.000 description 3
- 150000002910 rare earth metals Chemical class 0.000 description 3
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 2
- 229910052684 Cerium Inorganic materials 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910002549 Fe–Cu Inorganic materials 0.000 description 1
- 229910001257 Nb alloy Inorganic materials 0.000 description 1
- 229910052772 Samarium Inorganic materials 0.000 description 1
- 229910017052 cobalt Inorganic materials 0.000 description 1
- 239000010941 cobalt Substances 0.000 description 1
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 1
- 238000000748 compression moulding Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 229910052727 yttrium Inorganic materials 0.000 description 1
- VWQVUPCCIRVNHF-UHFFFAOYSA-N yttrium atom Chemical compound [Y] VWQVUPCCIRVNHF-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
- H01F1/0555—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 pressed, sintered or bonded together
- H01F1/0557—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 pressed, sintered or bonded together sintered
Abstract
Description
【発明の詳細な説明】
［産業上の利用分野］
本発明は、希土類元素とコバルトを主成分とするＲ、Ｃ
ｏ、、系（但しＲはＹを含む希土類元素）永久磁石材料
の製造方法に関し、更に詳しくは、それに銅とニオブを
添加した２−１７型希土類磁石合金の製造方法に関する
ものである。[Detailed Description of the Invention] [Industrial Application Field] The present invention is directed to R, C, containing rare earth elements and cobalt as main components.
The present invention relates to a method for manufacturing a permanent magnet material of type 2-17 (where R is a rare earth element containing Y), and more specifically to a method for manufacturing a 2-17 type rare earth magnet alloy to which copper and niobium are added.
［従来の技術］
Ｒ−Ｃｏ−Ｆｅ−Ｃｕ系の２−１７型希土類永久磁石合
金は従来公知である。この系の合金材料において、Ｃｕ
の添加は保磁力を高める効果があり１０重量％以上は必
要であるとされていた。しかしＣｕの添加量が増大する
と残留磁化Ｂｒが低下してしまう。[Prior Art] The R-Co-Fe-Cu type 2-17 rare earth permanent magnet alloy is conventionally known. In this type of alloy material, Cu
It was believed that the addition of 10% by weight or more was necessary because it had the effect of increasing the coercive force. However, as the amount of Cu added increases, the residual magnetization Br decreases.
この問題を解決するため適量のＮｂ（ニオブ）を複合添
加する技術が報告されている（特公昭５５−４８０９３
号公報）。それによればＣｕを５〜１２重量％含有させ
、Ｎｂを０．２〜４重量％添加している。In order to solve this problem, a technique has been reported in which a suitable amount of Nb (niobium) is added in combination (Japanese Patent Publication No. 55-48093
Publication No.). According to this, Cu is contained in an amount of 5 to 12% by weight, and Nb is added in an amount of 0.2 to 4% by weight.
［発明が解決しようとする問題点］
上記の技術ではＣｕの含有量を減少させたとは言え、ま
だ５〜１２重量％は必要でありＢｒを向上させ難い問題
があった。[Problems to be Solved by the Invention] Although the above technique reduces the Cu content, 5 to 12% by weight is still required, and there is a problem in that it is difficult to improve Br.
本発明の目的は、Ｃｕが５重量％以下という低い組成領
域のＲ−Ｃｏ−Ｆｅ−Ｃｕ−Ｎｂ磁石合金材料において
も、熱処理条件を適切に設定することによって永久磁石
の保磁力を実用範囲まで高めることができ、結果として
高エネルギー積を有する永久磁石材料の製造方法を提供
することにある。The purpose of the present invention is to increase the coercive force of permanent magnets to a practical range by appropriately setting heat treatment conditions even in R-Co-Fe-Cu-Nb magnet alloy materials with a low Cu content of 5% by weight or less. The object of the present invention is to provide a method for producing a permanent magnet material that can be improved and has a high energy product as a result.
［問題点を解決するための手段］
本発明者等はＲ−Ｃｏ−Ｆｅ−Ｃｕ−Ｎｂ系の希土類永
久磁石合金材料に関しＣｕＯ量を極力少なくしつつ永久
磁石としての保磁力を実用範囲まで高めうる方法につい
て種々検討した結果、焼結し溶体化処理を施した材料に
ついて２段時効を行い、第２段時効を第１段時効よりも
高い温度で行い所定の速度で冷却することによって前記
目的を達成できることを見出し、本発明を完成させるに
至ったものである。[Means for Solving the Problems] The present inventors have developed an R-Co-Fe-Cu-Nb rare earth permanent magnet alloy material by increasing the coercive force as a permanent magnet to a practical range while minimizing the amount of CuO. As a result of various studies on methods of aging, we found that the above objective could be achieved by performing two-stage aging on the sintered and solution-treated material, performing the second aging at a higher temperature than the first aging, and cooling at a predetermined rate. The present invention has been completed based on the discovery that the following can be achieved.
即ち本発明において素材となる原料とその重量比率は、
２２〜２８重量％のＲ（但しＲはＹ（イツトリウム）を
含む希土類元素の１種もしくは２種以上）、２３重量％
以下のＦｅ。That is, the raw materials and their weight ratios in the present invention are as follows:
22 to 28% by weight of R (where R is one or more rare earth elements including Y (yttrium)), 23% by weight
The following Fe.
０．１〜５重量％のＣｕ、０．１〜６重量％のＮｂ、残
部がＣｏからなる組成である。The composition consists of 0.1 to 5% by weight of Cu, 0.1 to 6% by weight of Nb, and the balance Co.
このような組成の合金をまず１１８０〜１２５０℃で焼
結し、１１００〜１２４０℃で且つ焼結温度より１０〜
８０℃低い温度で溶体化処理を行う。次に第１段時効と
して４００〜９００℃で１時間以上等温処理し、第２段
時効として第１段時効よりも高い温度の７００〜１００
０℃で等温処理を行う。その後、毎分０．２〜１０℃の
冷却速度で連続的に３００〜６００℃まで冷却するもの
である。An alloy with such a composition is first sintered at 1180-1250°C, and then heated at 1100-1240°C and 10-10°C below the sintering temperature.
Solution treatment is performed at a temperature 80°C lower. Next, as the first stage aging, isothermal treatment is performed at 400 to 900 °C for more than 1 hour, and as the second stage aging, the temperature is 700 to 100 °C, which is higher than the first stage aging.
Perform isothermal treatment at 0°C. Thereafter, it is continuously cooled to 300 to 600°C at a cooling rate of 0.2 to 10°C per minute.
本発明の特徴は、上記のように第１段時効よりも高い温
度で第２段時効を行い、引き続いて徐冷する点にある。A feature of the present invention is that, as described above, the second stage aging is performed at a higher temperature than the first stage aging, followed by slow cooling.
本発明において合金の組成比率や処理条件等は全て以下
に述べる実施例に示すような実験結果に基づいている。In the present invention, the alloy composition ratio, processing conditions, etc. are all based on experimental results as shown in the Examples described below.
まずＲ，Ｃｏ、 Ｆｅの比率は、この種の三元系組成
物で一般的に使用されているものとほぼ同様である。Ｒ
を２２〜２８重量％としたのは２２重量％未満では保磁
力が低下し、２８重量％超えると残留磁化が低下するか
らである。Ｆｅの添加量の上限を２３重量％とじたのは
、ｉＨｃが低下するからである。First, the ratios of R, Co, and Fe are approximately the same as those commonly used in ternary compositions of this type. R
is set to 22 to 28% by weight because if it is less than 22% by weight, the coercive force will decrease, and if it exceeds 28% by weight, the residual magnetization will decrease. The reason why the upper limit of the amount of Fe added is set at 23% by weight is that iHc decreases.
Ｃｕの含有量を０．１〜５重量％とじたのは、従来は５
重量％以上でないと保磁力がでなかったが熱処理条件を
適切に設定することによって保磁力を実用範囲まで高め
られるとともにＢｒを向上することができたためである
。さらに０．１〜５重量％の範囲において熱処理時間を
短くする場合はＣｕの添加量を多くし、そうでない、つ
まり冷却速度を遅くできる場合にはＣｕの含有量を少な
くできる等の調整も可能である。Ｎｂの添加量を０．１
〜６重量％とじたのは、６重量％を超えると４πＩ−Ｈ
ループの角形性が悪くなるからである。Conventionally, the Cu content was limited to 0.1 to 5% by weight.
This is because the coercive force could not be obtained unless it was at least % by weight, but by appropriately setting the heat treatment conditions, the coercive force could be increased to a practical range and the Br could be improved. Furthermore, in the range of 0.1 to 5% by weight, if the heat treatment time is to be shortened, the amount of Cu added can be increased; otherwise, if the cooling rate can be slowed down, the amount of Cu can be decreased. It is. The amount of Nb added is 0.1
~6% by weight is because if it exceeds 6% by weight, 4πI-H
This is because the squareness of the loop deteriorates.
焼結温度を１１８０〜１２５０℃としたのは、一般に焼
結温度が高いほど密度が上がり残留磁化が高くなるため
１１８０℃以上としたものであり、１２５０℃を超える
と焼結体が溶は残留磁化がかえって低くなるからである
。また焼結温度より１０〜８０℃低い１１ｏｏ〜１２４
０℃で溶体化処理を行うのは、そのような溶体化処理に
よって角形性が向上するためである。The reason why the sintering temperature was set at 1180 to 1250°C was because the higher the sintering temperature, the higher the density and the higher the residual magnetization. This is because the magnetization becomes lower on the contrary. Also, 11oo~124 is 10~80℃ lower than the sintering temperature.
The reason why the solution treatment is performed at 0° C. is that such solution treatment improves the squareness.
また第１段目よりも高い温度で第２段目の時効処理を行
い、その温度から連続冷却するのは、それによってＣｕ
が５重量％以下の場合でも高い保磁力を保たせることが
できるからである。In addition, the second stage of aging treatment is performed at a higher temperature than the first stage, and continuous cooling is performed from that temperature.
This is because a high coercive force can be maintained even when the amount is 5% by weight or less.
［作用］
このような特殊な熱処理条件を採用することによって、
Ｒ−Ｃｏ−Ｆｅ−Ｃｕ−Ｎｂ系の合金磁石材料において
Ｃｕを５重量％以下に少なくしても、永久磁石の保磁力
を実用性の範囲まで高めることができる。[Effect] By adopting such special heat treatment conditions,
Even if the amount of Cu in the R-Co-Fe-Cu-Nb alloy magnet material is reduced to 5% by weight or less, the coercive force of the permanent magnet can be increased to a practical level.
［実施例１］
（前工程）
必要とする合金を高周波溶解炉で溶解し、ショークラッ
シャーによって粗粉砕した後、シェドミルにより微粉砕
し、この微粉砕粉体を１５ｋｏｅの磁場中で形成圧３
ｔｏｎ／ｃｍ”で圧縮成形した。[Example 1] (Pre-process) The required alloy is melted in a high frequency melting furnace, coarsely pulverized by a show crusher, and then finely pulverized by a shed mill.
Compression molding was carried out at a pressure of 100,000 ton/cm.
（焼結体の組成） Ｓｍ＝２３．０重量％、Ｃｕ＝３．６重量％。(Composition of sintered body) Sm=23.0% by weight, Cu=3.6% by weight.
Ｆｅ＝１５．６重量％、Ｎｂ＝Ｏ〜７重量％。Fe=15.6% by weight, Nb=O~7% by weight.
残部をＣｏとする。The remainder is Co.
（熱処理）
Ｎｂの添加量に応じて１１８０〜１２５０℃で５時間の
焼結を行い、１１００〜１２４０℃で５時間の溶体化処
理を行った。そして第１段時効を７００℃で２時間行い
、第２段時効として９００℃で３時間保持し、０．５℃
／分の冷却速度で４００℃まで冷却した。Ｎｂの添加量
（重量％）に対するｂＨｃの測定結果を第１表に示す。(Heat treatment) Sintering was performed at 1180 to 1250°C for 5 hours depending on the amount of Nb added, and solution treatment was performed at 1100 to 1240°C for 5 hours. Then, the first stage aging was performed at 700°C for 2 hours, the second stage aging was held at 900°C for 3 hours, and the temperature was 0.5°C.
The mixture was cooled to 400° C. at a cooling rate of /min. Table 1 shows the measurement results of bHc with respect to the amount of Nb added (wt%).
第１表
この表から分かるように、Ｎｂが含まれていなかったり
Ｎｂの含有量が多くなって７重量％にもなると、ｂＨｃ
が大きく低下し、４π■−Ｈループの角形性が悪化して
いまう。Table 1 As can be seen from this table, when Nb is not included or when the Nb content increases to 7% by weight, bHc
is greatly reduced, and the squareness of the 4π■-H loop deteriorates.
［実施例２］ （前工程）・・・実施例１に同じ （焼結体の組成） Ｓｍ＝２３．０重量％、Ｃｕ＝Ｏ〜６重量％。[Example 2] (Pre-process)...Same as Example 1 (Composition of sintered body) Sm=23.0% by weight, Cu=O~6% by weight.
Ｆｅ＝１５．６重量％、Ｎｂ＝３重量％、残部をｃｏと
する。Fe=15.6% by weight, Nb=3% by weight, and the balance is co.
（熱処理）・・・実施例１に同じ Ｃｕの含有量の変化に対するｂ）（ｃ、ｉＨｃ。(Heat treatment)...Same as Example 1 b) (c, iHc) for changes in Cu content.
Ｂｒ、（ＢＨ）ｍａｘの測定結果を第２表に示す。The measurement results of Br and (BH)max are shown in Table 2.
第２表
この第２表から本発明では高いエネルギー積が得られる
ことが分かる。Table 2 It can be seen from Table 2 that a high energy product can be obtained in the present invention.
［実施例３］
（前工程）・・・実施例１に同じ
（焼結体の組成）
Ｓｒｎ＝２３．０重量％、Ｃｏ＝５４．７重量％、Ｆｅ
−１５，６重量％、Ｃｕ＝３．９重量％、Ｎｂ＝２．８
重量％。[Example 3] (Pre-process)...Same as Example 1 (composition of sintered body) Srn = 23.0% by weight, Co = 54.7% by weight, Fe
-15.6% by weight, Cu=3.9% by weight, Nb=2.8
weight%.
（熱処理）
１１７０〜１２７０℃で５時間の焼結を行い、溶体化処
理として焼結温度より２０℃低めの温度で５時間保持し
、第１段時効として７００℃で２時間保持し、第２段時
効として９００℃で３時間保持し、その温度から０．５
℃／分の冷却速度で４００℃まで冷却した。焼結温度に
対するｂＨｃ、ｉＨｃ、Ｂｒおよび密度の測定結果を第
３表に示す。(Heat treatment) Sintering was performed at 1170 to 1270°C for 5 hours, and as a solution treatment, it was held at a temperature 20°C lower than the sintering temperature for 5 hours, as a first stage aging, it was held at 700°C for 2 hours, and as a second stage aging, it was held at 700°C for 2 hours. Hold at 900℃ for 3 hours as stage aging, and from that temperature 0.5
It was cooled to 400°C at a cooling rate of °C/min. Table 3 shows the measurement results of bHc, iHc, Br and density with respect to sintering temperature.
（以下余白）
第３表
第３表より焼結温度を高くすると密度は高く、Ｂｒが向
上するが、１２５０℃を超えると焼結体の溶融のため磁
気特性全体が低下することが分かる。(Left space below) Table 3 It can be seen from Table 3 that increasing the sintering temperature increases the density and improves Br, but when it exceeds 1250°C, the overall magnetic properties deteriorate due to melting of the sintered body.
［実施例４］
（前工程）・・・実施例１に同じ
（焼結体の組成）・・・実施例３に同じ（熱処理）
１２５０℃で５時間焼結し、１０１０〜１２３０℃で５
時間の溶体化処理を行った。第１段時効として７００℃
で２時間保持し、第２段時効を９００℃で３時間行った
。そして０．５℃／分の冷却速度で４００℃まで冷却し
た。溶体化温度に対するｂＨｃの測定結果を第４表に示
す。[Example 4] (Pre-process)...Same as Example 1 (Composition of sintered body)...Same as Example 3 (Heat treatment) Sintered at 1250°C for 5 hours, sintered at 1010-1230°C for 5 hours.
A time solution treatment was performed. 700℃ as first stage aging
The sample was held at 900° C. for 2 hours, and second stage aging was performed at 900° C. for 3 hours. Then, it was cooled to 400°C at a cooling rate of 0.5°C/min. Table 4 shows the measurement results of bHc with respect to solution temperature.
第４表
適切な溶体化温度を加えることによりｂＨｃが良くなる
ことが分かる。Table 4 shows that bHc can be improved by adding an appropriate solution temperature.
［実施例５］
（前工程）・・・実施例１に同じ
（焼結体の組成）・・・実施例３に同じ（熱処理）
１２５０℃で５時間の焼結を行い、１２３０℃で５時間
の溶体化処理を行った。そして第１段時効として６００
〜８００℃で２時間保持し、第２段時効を９００℃で３
時間行い冷却した。[Example 5] (Pre-process)...Same as Example 1 (Composition of sintered body)...Same as Example 3 (Heat treatment) Sintering was performed at 1250°C for 5 hours, and sintering was performed at 1230°C for 5 hours. A time solution treatment was performed. And 600 as the first stage statute of limitations.
Hold at ~800℃ for 2 hours, and perform second stage aging at 900℃ for 3 hours.
Cooled for a while.
第１段時効の温度に対するｂＴ（ｃ、１）（ｃの測定結
果を第５表に示す。Table 5 shows the measurement results of bT (c, 1) (c) with respect to the temperature of the first stage aging.
（以下余白）
第５表
適切な第１段時効温度によりｂＨｃが良くなることが分
かる。(Margin below) Table 5 It can be seen that bHc improves with an appropriate first stage aging temperature.
［実施例６］
（前工程）・・・実施例１に同じ
（焼結体の組成）・・・実施例３に同じ（熱処理）
１２５０℃で５時間の焼結を行い、１２３０℃で５時間
の溶体化処理を行った。そして第１段時効として７００
℃で０．５〜８時間保持し、第２段時効を９００℃で３
時間行い、０．５℃／分の冷却速度で４００℃まで冷却
した。第１段時効の保持時間に対するｂＨｃ、ｉＨｃの
測定結果を第６表に示す。[Example 6] (Pre-process)...Same as Example 1 (Composition of sintered body)...Same as Example 3 (Heat treatment) Sintering was performed at 1250°C for 5 hours, and sintering was performed at 1230°C for 5 hours. A time solution treatment was performed. and 700 as the first stage statute of limitations.
℃ for 0.5 to 8 hours, and second stage aging at 900℃ for 3 hours.
The mixture was cooled to 400°C at a cooling rate of 0.5°C/min. Table 6 shows the measurement results of bHc and iHc with respect to the holding time of the first stage aging.
第６表
第１段時効時間を１時間以上、好ましくは２時間以上加
えないとｂＨｃがよくならないことが分かる。It can be seen that bHc does not improve unless the first stage aging time in Table 6 is added for 1 hour or more, preferably 2 hours or more.
［実施例７］
（前工程）・・・実施例１に同じ
（焼結体の組成）・・・実施例３に同じ（熱処理）
１２５０℃で５時間の焼結を行い、１２３０℃で５時間
の溶体化処理を行った。そして第１段時効として７００
℃で２時間保持し、第２段時効を８５０〜９５０℃で２
時間行い、０． ５℃／分の冷却速度で４００℃まで冷
却した。第２段時効の温度に対するｂＨｃ、ｉＨｃの測
定結果を第７表に示す。[Example 7] (Pre-process)...Same as Example 1 (Composition of sintered body)...Same as Example 3 (Heat treatment) Sintering was performed at 1250°C for 5 hours, and sintering was performed at 1230°C for 5 hours. A time solution treatment was performed. and 700 as the first stage statute of limitations.
℃ for 2 hours, and second stage aging at 850-950℃ for 2 hours.
time, 0. It was cooled to 400°C at a cooling rate of 5°C/min. Table 7 shows the measurement results of bHc and iHc with respect to the temperature of the second stage aging.
第７表
第２段時効の温度を上げるとｉＨｃがでるが、しかし適
切な温度を加えないとｂＨｃが悪くなることが分かる。It can be seen that iHc increases when the temperature of the second stage aging in Table 7 is increased, but bHc deteriorates unless an appropriate temperature is applied.
［実施例８］
（前工程）・・・実施例１に同じ
（焼結体の組成）・・・実施例３と同じ（熱処理）
１２５０℃で５時間の焼結を行い、１２３０℃で５時間
の溶体化処理を行った。そして第１段時効として７００
℃で２時間保持し、第２段時効を９００℃で２時間行い
、０．２〜ｂ／分の冷却速度で４００℃まで冷却した。[Example 8] (Pre-process)...Same as Example 1 (Composition of sintered body)...Same as Example 3 (Heat treatment) Sintering was performed at 1250°C for 5 hours, and sintering was performed at 1230°C for 5 hours. A time solution treatment was performed. and 700 as the first stage statute of limitations.
℃ for 2 hours, second stage aging was performed at 900℃ for 2 hours, and cooled to 400℃ at a cooling rate of 0.2 to b/min.
冷却速度に対するｂＨｃ、ｉＨｃの測定結果を第８表に
示す。Table 8 shows the measurement results of bHc and iHc with respect to the cooling rate.
第８表
第８表より冷却速度を遅くするとｉＨｃは増加するが、
しかし適切な冷却速度をとらないとｂＨｃが悪くなる。Table 8 From Table 8, iHc increases when the cooling rate is slowed, but
However, if an appropriate cooling rate is not taken, bHc will deteriorate.
［実施例９］
（前工程）・・・実施例１と同じ
（焼結体の組成）
Ｓｍ＝Ｏ〜２５．０重量％、Ｃｅ＝０〜２５゜０重量％
（但しＳｍ＋Ｃｅ＝２５．０重量％）。[Example 9] (Pre-process)... Same as Example 1 (composition of sintered body) Sm = O ~ 25.0% by weight, Ce = 0 ~ 25°0% by weight
(However, Sm+Ce=25.0% by weight).
Ｃｏ＝５３．４重量％、Ｆｅ＝１５．２重量％。Co=53.4% by weight, Fe=15.2% by weight.
Ｃｕ＝３．６重量％、Ｎｂ＝２．８重量％。Cu=3.6% by weight, Nb=2.8% by weight.
（熱処理）
Ｃｅの添加量に応じて１１６０〜１２５０℃で５時間の
焼結を行い、１１３０−１２４０℃で５時間の溶体化処
理を行った。そして第１段時効として６００℃で３時間
保持し、第２段時効を８００℃で４時間行い、０．５℃
／分で４００℃まで冷却した。ＳｍとＣｅの割合に対す
るｂＨｃ、１）（ｃ、Ｂｒの測定結果を第９表に示す。(Heat treatment) Sintering was performed at 1160-1250°C for 5 hours depending on the amount of Ce added, and solution treatment was performed at 1130-1240°C for 5 hours. Then, the first stage aging was held at 600°C for 3 hours, the second stage aging was performed at 800°C for 4 hours, and the temperature was 0.5°C.
/min to 400°C. Table 9 shows the measurement results of bHc, 1) (c, and Br) with respect to the ratio of Sm and Ce.
第９表
第９表より、Ｓｍの一部を（、ｅで置換しても実用範囲
の特性が得られ、結果としてＳｍ以外の希土類において
も本発明を通用できることが分かる。From Table 9, it can be seen that even if a part of Sm is replaced with (, e), characteristics within a practical range can be obtained, and as a result, the present invention can be applied to rare earths other than Sm.
［発明の効果］
本発明は上記のように焼結後に溶体化処理を行い、先ず
第１段時効を行い、次にその第１段時効よりも高い温度
で第２段時効を行ってから連続的に所定温度まで冷却す
る熱処理工程を採用したことによって、Ｃｕの量を５重
量％以下に低くしても従来技術と同程度の永久磁石に必
要な保磁力を発現させることができ、しかもＣｕが低い
分だけ残留磁化が低くならず、高いエネルギー積を発生
させることができる優れた効果が生じる。[Effect of the invention] As described above, the present invention performs solution treatment after sintering, first performs first stage aging, then performs second stage aging at a higher temperature than the first stage aging, and then continuously By adopting a heat treatment process in which the amount of Cu is lowered to 5% by weight or less, it is possible to develop the coercive force required for a permanent magnet equivalent to that of the conventional technology. Since the residual magnetization is low, the residual magnetization does not decrease and a high energy product can be generated.
Claims (1)
素の１種もしくは２種以上）、２３重量％以下のＦｅ、
０．１〜５重量％のＣｕ、０．１〜６重量％のＮｂ、残
部がＣｏからなる組成の合金を、１１８０〜１２５０℃
で焼結し、１１００〜１２４０℃で且つ焼結温度より１
０〜８０℃低い温度で溶体化処理を行い、第１段時効と
して４００〜９００℃で１時間以上等温処理し、第２段
時効として第１段時効よりも高温の７００〜１０００℃
で等温処理し、引き続いて毎分０．２〜１０℃の冷却速
度で連続的に３００〜６００℃まで冷却することを特徴
とする永久磁石材料の製造方法。1, 22 to 28% by weight of R (wherein R is one or more rare earth elements including Y), 23% by weight or less of Fe,
An alloy having a composition of 0.1 to 5 wt% Cu, 0.1 to 6 wt% Nb, and the balance Co was heated at 1180 to 1250°C.
sintered at 1100-1240℃ and 1
Solution treatment is performed at a temperature 0 to 80°C lower, first stage aging is isothermal treatment at 400 to 900°C for 1 hour or more, and second stage aging is 700 to 1000°C, which is higher than the first stage aging.
1. A method for producing a permanent magnet material, which comprises isothermally treating the material at a temperature of 300° C. and subsequently cooling it continuously to 300° C. to 600° C. at a cooling rate of 0.2° C. to 10° C. per minute.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61302625A JPS63157844A (en) | 1986-12-18 | 1986-12-18 | Manufacture of permanent magnet material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61302625A JPS63157844A (en) | 1986-12-18 | 1986-12-18 | Manufacture of permanent magnet material |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS63157844A true JPS63157844A (en) | 1988-06-30 |
| JPH0328503B2 JPH0328503B2 (en) | 1991-04-19 |
Family
ID=17911234
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP61302625A Granted JPS63157844A (en) | 1986-12-18 | 1986-12-18 | Manufacture of permanent magnet material |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS63157844A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2015037041A1 (en) * | 2013-09-13 | 2015-03-19 | 株式会社 東芝 | Permanent magnet, motor, and power generator |
| WO2017046826A1 (en) * | 2015-09-15 | 2017-03-23 | 株式会社 東芝 | Permanent magnet and dynamo electric machine |
| US20210343457A1 (en) * | 2017-09-15 | 2021-11-04 | Kabushiki Kaisha Toshiba | Permanent magnet, rotary electrical machine, and vehicle |
-
1986
- 1986-12-18 JP JP61302625A patent/JPS63157844A/en active Granted
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2015037041A1 (en) * | 2013-09-13 | 2015-03-19 | 株式会社 東芝 | Permanent magnet, motor, and power generator |
| US9502165B2 (en) | 2013-09-13 | 2016-11-22 | Kabushiki Kaisha Toshiba | Permanent magnet, motor, and generator |
| WO2017046826A1 (en) * | 2015-09-15 | 2017-03-23 | 株式会社 東芝 | Permanent magnet and dynamo electric machine |
| CN107430916A (en) * | 2015-09-15 | 2017-12-01 | 株式会社东芝 | Permanent magnet and electric rotating machine |
| CN107430916B (en) * | 2015-09-15 | 2019-10-25 | 株式会社东芝 | Permanent magnet and rotating electric machine |
| US10943716B2 (en) | 2015-09-15 | 2021-03-09 | Kabushiki Kaisha Toshiba | Permanent magnet and rotary electrical machine |
| US20210343457A1 (en) * | 2017-09-15 | 2021-11-04 | Kabushiki Kaisha Toshiba | Permanent magnet, rotary electrical machine, and vehicle |
| US11676747B2 (en) * | 2017-09-15 | 2023-06-13 | Kabushiki Kaisha Toshiba | Permanent magnet, rotary electrical machine, and vehicle |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0328503B2 (en) | 1991-04-19 |
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