JPS6047721B2 - Permanent magnet manufacturing method - Google Patents
Permanent magnet manufacturing methodInfo
- Publication number
- JPS6047721B2 JPS6047721B2 JP56103434A JP10343481A JPS6047721B2 JP S6047721 B2 JPS6047721 B2 JP S6047721B2 JP 56103434 A JP56103434 A JP 56103434A JP 10343481 A JP10343481 A JP 10343481A JP S6047721 B2 JPS6047721 B2 JP S6047721B2
- Authority
- JP
- Japan
- Prior art keywords
- weight
- aging treatment
- permanent magnet
- temperature range
- stage
- 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.)
- Expired
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
- H01F1/06—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 in the form of particles, e.g. powder
- H01F1/08—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 in the form of particles, e.g. powder pressed, sintered, or bound together
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F41/00—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties
- H01F41/02—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets
- H01F41/0253—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets for manufacturing permanent magnets
-
- 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
- H01F1/06—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 in the form of particles, e.g. powder
- H01F1/08—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 in the form of particles, e.g. powder pressed, sintered, or bound together
- H01F1/086—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 in the form of particles, e.g. powder pressed, sintered, or bound together sintered
Landscapes
- Engineering & Computer Science (AREA)
- Power Engineering (AREA)
- Manufacturing & Machinery (AREA)
- Hard Magnetic Materials (AREA)
- Powder Metallurgy (AREA)
Description
【発明の詳細な説明】
本発明はサマリウム−コバルト系の永久磁石の製造方
法に係り、特にＳｍ。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a method for manufacturing a samarium-cobalt permanent magnet, particularly Sm.
Ｃｏ、、系の永久磁石の製造方法に関する。 従来Ｓｍ
。The present invention relates to a method of manufacturing a Co-based permanent magnet. Conventional Sm
.
Ｃｏ、、系永久磁石としては、各種組成のものが提案さ
れているが、Ｃｏの一部をＣｕＮＦｅ及びＴｉで置換す
ることにより保磁力（■ｃ）、残留磁束密度（Ｂｒ）お
よび最大エネルギー積（（ＢＨ）ｍａｘ）あるいは耐酸
化性の改善が図られ ている。Co-based permanent magnets with various compositions have been proposed, but by replacing a portion of Co with CuNFe and Ti, the coercive force (■c), residual magnetic flux density (Br), and maximum energy product can be improved. ((BH)max) or improved oxidation resistance.
本発明は、このようなＳｍ。（ＣＯＮＣＵ）ＦｅＮＴｉ
）、、系の永久磁石の製造方法の改良に関す るもので
ある。前記の特性のうちでも（ＢＨ）ｍａｘ及びＢｒが
、モーター等の用途においては特に重要で、可能な限り
大きいことが望まれるが、ＩＨｃがある一定値以上ない
と（ＢＨ）ｍａｘ）Ｂｒを高めることは困難である。従
つて（ＢＨ）ｍａｘ）Ｂｒの大きい永久磁石を得るため
には、ＩＨｃを大き くすることも必要である。 とこ
ろで、Ｓｍ。The present invention is directed to such Sm. (CONCU)FeNTi
), , system permanent magnet manufacturing method. Among the above characteristics, (BH)max and Br are particularly important in applications such as motors, and are desired to be as large as possible, but if IHc is not above a certain value, (BH)max)Br will be increased. That is difficult. Therefore, in order to obtain a permanent magnet with a large (BH)max)Br, it is also necessary to increase the IHc. By the way, Sm.
（Ｃｏ、ＣｕＮＦｅ）Ｔｉ）、、系の磁石では、Ｆｅ含
量を増したり、Ｃｕ含量を減らすと残留磁束密度を増加
させ得ることが知られている。しかし、Ｆｅ含有を増し
たり、Ｃｕ含量を減らすと保磁力を低下して来るため、
単純にＦｅ含量を増−しＣｕ含量を減らすことによつて
残留磁束密度や最大エネルギー積の向上を図ることでな
い。そのため、従来のＳｍ。（ＣｏＮＣＵ）ＦｅＮＴｉ
）、、系の磁石は、保磁力をある値以上に維持しながら
、残留磁束密度を可能な限り大きくすることを目的とし
て）その組成が決定された。例えば、特公昭５５一１５
０９６号公報記載のＳｍ２（Ｃｏ、Ｃｕ、、Ｆｅ）Ｔｉ
）、７系の磁石では、ＣＵ５〜２鍾量％、Ｆｅ２〜１５
重量％である。また特開昭５２−１０９１９１号公報記
載の磁石では、ＣＵ９〜１鍾量％、Ｆｅ３〜１鍾量％で
ある。これらの組成は、Ｃｕ含量及びＦｅ含量の変動に
伴つて起る、残留磁束密度と保持力の変化を妥協的に適
合させた結果であるから、必ずしも十分なものとは言え
ないものであつた。残留磁束密度を低下させるＣｕ分を
減らし、これを向上させるＦｅ分を増加させ、同時に保
磁力を一定値以上に保持することができれば、残留密度
及び最大エネルギー積が大きい優れた永久磁石を得るこ
とができる。It is known that in (Co, CuNFe)Ti) system magnets, the residual magnetic flux density can be increased by increasing the Fe content or decreasing the Cu content. However, as the Fe content increases or the Cu content decreases, the coercive force decreases.
It is not possible to improve the residual magnetic flux density or the maximum energy product by simply increasing the Fe content and decreasing the Cu content. Therefore, the conventional Sm. (CoNCU)FeNTi
), the composition of the magnet was determined with the aim of increasing the residual magnetic flux density as much as possible while maintaining the coercive force above a certain value. For example, the special public service 55-15
Sm2(Co, Cu,,Fe)Ti described in Publication No. 096
), 7 series magnets have a CU5~2 weight%, Fe2~15
Weight%. Further, in the magnet described in JP-A-52-109191, the CU is 9-1% by weight and the Fe is 3-1% by weight. These compositions were not necessarily satisfactory because they were the result of compromising adaptation to changes in residual magnetic flux density and coercive force that occur with variations in Cu content and Fe content. . If it is possible to reduce the Cu content, which lowers the residual magnetic flux density, and increase the Fe content, which improves it, and at the same time maintain the coercive force above a certain value, it is possible to obtain an excellent permanent magnet with a large residual density and maximum energy product. I can do it.
本発明は、かかる永久磁石の製造方法の提供を目的とす
るものである。本発明者らが、永久磁石を構成する合金
の組成及びその処理過程について鋭意研究を重ねたとこ
ろ、合金の組成をＳｍ（ＣＯ，．Ｃｕ，．Ｆｅ．．Ｔｉ
）ｚの式で表した場合、Ｚ〉６．９でしかも焼結後に特
定の時効処理を施すと、Ｆｅ量を増しＣｕ量を減らすこ
とによつても従来の知見とは全く逆に保磁力を増加させ
得ることを見出した。この新しい発見に基いて以下に記
す発明を完成し、Ｓｍ２（ＣＯ、Ｃｕ，．Ｆｅ，．Ｔｉ
）１７系磁石の残留磁束密度及び最大エネルギー積を著
しく高めることに成功した。即ち、本発明は、サマリウ
ム２３〜２踵量％と、チタン０．２〜７重量％と、銅３
〜９重量％と、鉄１４重量％より多く２５重量％以下と
、残部として主としてコバルトであ委部分とからなる金
属粉末を、磁界中で成形し、焼結後３５０〜９００℃の
温度範囲において高温側から低温側へ多段階に時効処理
を施す永久磁石の製造方法であつて、少なくと．も、第
１段の時効処理を８００〜９００℃の温度範囲で行ない
、第２段の時効処理を６００〜８００℃の温度範囲で行
なうことを特徴とする。本発明の効果は磁石を構成する
金属元素の組成と、処理方法なかでも時効処理パターン
との結合ｊにおいて奏されるものである。The present invention aims to provide a method for manufacturing such a permanent magnet. The present inventors conducted intensive research on the composition of the alloy that constitutes the permanent magnet and its processing process, and found that the composition of the alloy was Sm(CO, .Cu, .Fe...Ti).
) When expressed by the formula z, if Z>6.9 and a specific aging treatment is performed after sintering, the coercive force will decrease even by increasing the amount of Fe and decreasing the amount of Cu, contrary to conventional knowledge. We have found that it is possible to increase Based on this new discovery, we completed the invention described below.
) We succeeded in significantly increasing the residual magnetic flux density and maximum energy product of the 17 series magnet. That is, the present invention contains 23-2% by weight of samarium, 0.2-7% by weight of titanium, and 3% by weight of copper.
A metal powder consisting of ~9% by weight of iron, more than 14% by weight and up to 25% by weight of iron, and the remainder mainly cobalt is compacted in a magnetic field, and after sintering is heated in a temperature range of 350 to 900°C. A permanent magnet manufacturing method that performs aging treatment in multiple stages from a high temperature side to a low temperature side. Also, the first stage aging treatment is performed at a temperature range of 800 to 900°C, and the second stage aging treatment is performed at a temperature range of 600 to 800°C. The effects of the present invention are achieved by the combination j of the composition of the metal elements constituting the magnet and the aging treatment pattern among the treatment methods.
原料金属粉末において、Ｓｍが２３重量％未満では保磁
力の増加はなく、２踵量％を超えた場合でも増加はない
。In the raw metal powder, if Sm is less than 23% by weight, there is no increase in coercive force, and even if it exceeds 2% by weight, there is no increase.
また、磁束密度が低下し、最大エネルギー積の増大もな
い。Ｔｉが０．２重量％未満でっあると保磁力の増大が
顕著でなく、７重量％を超えると磁束密度が低下する。
Ｃｕが３重量％未満では保磁力の増大はなく、９重量％
を超えると磁束密度が低下するとともに時効硬化性が低
く、最大エネルギー積の増大もほとんどない。Ｆｅが１
４重量％以下では、保磁力の増大は得られず、残留磁束
密度や最大エネルギー積の向上もほとんどない。Ｆｅが
２５重量％を超えると、保磁力が著しく減少し時効硬化
性も極めて低くて最大エネルギー積が減少する。本発明
において、焼結工程や時効処理工程は真空、窒素、希ガ
スなどの不活性雰囲気において行う必要があり、焼結は
約１０５０〜１２５０℃の温度で行ノわれる。Furthermore, the magnetic flux density decreases and the maximum energy product does not increase. If Ti is less than 0.2% by weight, the coercive force will not increase significantly, and if it exceeds 7% by weight, the magnetic flux density will decrease.
If Cu is less than 3% by weight, there is no increase in coercive force, and if Cu is less than 9% by weight.
If it exceeds , the magnetic flux density decreases, the age hardenability is low, and there is almost no increase in the maximum energy product. Fe is 1
If it is less than 4% by weight, no increase in coercive force is obtained, and there is almost no improvement in residual magnetic flux density or maximum energy product. When Fe exceeds 25% by weight, the coercive force is significantly reduced, the age hardenability is also extremely low, and the maximum energy product is reduced. In the present invention, the sintering process and the aging process must be performed in a vacuum, in an inert atmosphere such as nitrogen, or a rare gas, and the sintering is performed at a temperature of about 1050 to 1250°C.
なお焼結に関しては、２段以上の焼結を施すことも可能
である。時効処理は本発明において非常に重要な工程で
あり、この処理を施すことによつて保磁力、及び最大エ
ネルギー積が著しく向上する。Regarding sintering, it is also possible to perform sintering in two or more stages. Aging treatment is a very important step in the present invention, and by performing this treatment, coercive force and maximum energy product are significantly improved.
時効処理は．３５０℃から９００℃の温度範囲において
、高い温度から低い温度へ２以上の段階からなる多段階
で行う必要がある。この際、少なくとも、第１段の時効
処理を８００〜９００℃の温度範囲で行ない、第２段の
時効処理を６００〜８００℃の温度範囲で行なうが、第
３段目以降の時効処理は必ずしも必要ではない。しかし
ながら、第３段目以降の時効処理を施す場合は、その時
効処理の温度範囲を３５０℃以上であつて第２段の時効
処理温度以下としなければならない。このような時効処
理パターンの好ましい例をあげると、Ｃｕ≧７．５重量
％においては、第１段の時効処理を８００〜９００℃の
温度範囲で行ない、その後順次６００〜８００℃の温度
範囲での第２段、４００〜７００℃の温度範囲での第３
段の処理を少なくとも含む時効処理が好ましく、また、
Ｃｕ〈７．５重量％においては、第１段の時効処理を８
００〜９００℃の温度範囲で行ない、その後順次６５０
〜８００℃での第２段、４５０〜７００℃での第３段、
３５０〜６００℃での第４段の処理を少なくとも含む時
効処理が好ましい。以下、本発明を実施例により具体的
に説明する。What is the aging process? In the temperature range from 350°C to 900°C, it is necessary to carry out the process in multiple stages consisting of two or more stages from high temperature to low temperature. At this time, at least the first stage aging treatment is performed in a temperature range of 800 to 900°C, and the second stage aging treatment is performed in a temperature range of 600 to 800°C, but the third stage and subsequent stages of aging treatment are not necessarily performed. Not necessary. However, when performing aging treatment in the third stage or later, the temperature range of the aging treatment must be 350° C. or higher and lower than the second stage aging treatment temperature. To give a preferable example of such an aging treatment pattern, when Cu≧7.5% by weight, the first stage aging treatment is performed in a temperature range of 800 to 900°C, and then sequentially in a temperature range of 600 to 800°C. the second stage at a temperature range of 400-700°C.
Preferably, aging treatment includes at least stage treatment, and
When Cu<7.5% by weight, the first aging treatment was performed at 8% by weight.
It is carried out in the temperature range of 00 to 900℃, and then sequentially heated to 650℃.
2nd stage at ~800°C, 3rd stage at 450-700°C,
Preferably, the aging treatment includes at least a fourth stage treatment at 350 to 600°C. Hereinafter, the present invention will be specifically explained with reference to Examples.
実施例
以下の実施例においては、本発明ν係る永久磁石を次の
ようにして製造した。EXAMPLES In the following examples, permanent magnets according to the present invention were manufactured as follows.
所要の組成比で各金属元素の粉末を配合し、約４ｋ９を
真空高周波誘導加熱炉で溶融後冷却し、得られた均一な
インゴットを粗粉砕機ジェットミルにより粉砕して微粉
末とした。この微粉末を所定の押型に充填し、２０００
０エルステッドの磁界をかけながら２２ｔ．０ｎ１ｄの
圧力で圧縮成形した。得られた成形品にアルゴンガス雰
囲気中で所定温度、所定時間の焼結処理を施した後、直
ちに室温まで冷却しアルゴンガス雰囲気中て、所定の多
段階時効処理に供した。以下において％は重量％を表す
。実施例１
１Ｈｃｌ（ＢＨ）ＭａｘのＣｕ含量依存性と時効処理の
効果○組成：Ｓｍ２６．５％、Ｔｌｌ．２Ｏ％、ＣＵ６
〜１１．５％、Ｆｅｌ６．Ｏ％、ＣＯ部。Powders of each metal element were blended in a required composition ratio, approximately 4k9 was melted in a vacuum high-frequency induction heating furnace, and then cooled, and the resulting uniform ingot was ground into fine powder using a coarse grinder jet mill. This fine powder was filled into a predetermined mold, and
22t while applying a magnetic field of 0 oersted. Compression molding was performed at a pressure of 0n1d. The obtained molded product was subjected to a sintering treatment at a predetermined temperature and for a predetermined time in an argon gas atmosphere, and then immediately cooled to room temperature and subjected to a predetermined multi-step aging treatment in an argon gas atmosphere. In the following, % represents weight %. Example 1 Cu content dependence of 1Hcl(BH)Max and effect of aging treatment ○Composition: Sm26.5%, Tll. 20%, CU6
~11.5%, Fel6. O%, CO part.
○焼結条件：１１８０℃×１時間。○Sintering conditions: 1180°C x 1 hour.
○時効処理：（８５０℃、３扮）＋（７５０℃、１時間
）＋（６５０℃、２時間）＋（５５０゜Ｃ１４時間）比
較のために、時効処理を行なわないほかは実施例１と同
様にして別の永久磁石（比較例１）を製造した。○Aging treatment: (850°C, 3 times) + (750°C, 1 hour) + (650°C, 2 hours) + (550°C 14 hours) For comparison, the same as Example 1 except that no aging treatment was performed. Another permanent magnet (Comparative Example 1) was manufactured in the same manner.
第１図に、得られた永久磁石のＣｕ含量と、ＩＨＣ及び
（ＢＨ）Ｍａｘとの関係を示す。FIG. 1 shows the relationship between the Cu content of the obtained permanent magnet and IHC and (BH)Max.
Ａ・・・・ ・・・・実施例１のＩＨｃｌａ・・・・
・・・比較例１のＩＨＣｌ
Ｂ・・・・ ・・・実施例１の（ＢＨ）Ｍａｘ、ｂ・・
・・・・・・・・比較例１の（ＢＨ）ＭａｘＯ図から明
らかなように、本発明の実施例１は、ＣＵ９％以下でも
保磁力が大きく、（ＢＨ）Ｍａｘのピークも時効前１０
〜１１％（Ｃｕ）であつたものが７〜８％以下のところ
にシフトし、かつ（ＢＨ）Ｍａｘの値もかなり大きくな
つた。A... ...IHcla of Example 1...
...IHCl B of Comparative Example 1... (BH)Max, b of Example 1...
......As is clear from the (BH)MaxO diagram of Comparative Example 1, Example 1 of the present invention has a large coercive force even at CU9% or less, and the peak of (BH)Max also reaches 10% before aging.
What was ~11% (Cu) shifted to 7-8% or less, and the value of (BH)Max also became considerably large.
実施例２
ＩＨＣのＦｅ含量依存性
○組成：Ｓｍ２５．８％、Ｔｌｌ．５Ｏ％、ＣＵ６．７
Ｏ％、Ｆｅｌｌ〜１９％、ＣＯ残部。Example 2 Fe content dependence of IHC Composition: Sm25.8%, Tll. 50%, CU6.7
O%, Fell ~ 19%, CO balance.
Ｏ焼結条件：１１７５゜Ｃ×１時間。O sintering conditions: 1175°C x 1 hour.
○時効処理：（８５０℃、３扮）＋（７５０℃、１時間
）＋（６５０℃、２時間）＋（５５０℃、４時間）得ら
れた永久磁石のＦｅ含量とＩＨｃの関係を第２図に示す
。○Aging treatment: (850°C, 3 times) + (750°C, 1 hour) + (650°C, 2 hours) + (550°C, 4 hours) The relationship between the Fe content and IHc of the obtained permanent magnet was As shown in the figure.
Ｆｅ含量が多い程１Ｈｃが大きくなり、本発明の範囲で
あるＦｅが１４％より多いところでは飽和状態に達して
いる。このように、Ｆｅ含量の増加に伴つてＩＨＣが増
すということが従来の知見とは全く異なり本発明の一つ
の特徴である。実施例３実施例に係る試料３１〜３８と
比較試料３１〜４４を製造した。1Hc increases as the Fe content increases, and reaches a saturation state where Fe is more than 14%, which is the range of the present invention. Thus, one feature of the present invention, which is completely different from conventional knowledge, is that IHC increases as the Fe content increases. Example 3 Samples 31 to 38 according to the example and comparative samples 31 to 44 were manufactured.
各試料の組成、焼結条件を第１表に示した。時効処理の
条件は、すべて次のとおりであつた。番号で示した時効
処理のパターンは、それぞれ次のとおりである。（時効
処理パターン）
１８５０℃、３０ｒＴ１１ｎ＋７５０゜Ｃ１１ｈｒ＋６
５０℃、２１１ｒｓ＋５５００Ｃ．．４ｈｒｓ＋４５０
℃、８１１ｒｓ２８５０℃、３０ｒＴ１１ｎ＋６５０℃
、４１１ｒｓ３７５０℃、３１１ｒｓ４９５０℃、３０
ｒｎｉｎ＋（時効パターン１）ノ５３５０℃、１００ｈ
ｒｓ比較例は組成又は時効処理が本発明の範囲外にある
ものである。The composition and sintering conditions of each sample are shown in Table 1. All conditions for aging treatment were as follows. The aging processing patterns indicated by numbers are as follows. (Aging treatment pattern) 1850°C, 30rT11n+750°C11hr+6
50℃, 211rs+5500C. ．． 4hrs+450
℃, 811rs2850℃, 30rT11n+650℃
, 411rs3750℃, 311rs4950℃, 30
rnin+ (aging pattern 1) 5350°C, 100h
The rs comparative example has a composition or aging treatment outside the scope of the present invention.
製造した永久磁石のＢｒ，．ＩＨｃｌ（ＢＨ）Ｍａｘを
第１表に併記した。また、実施例の試料３１及び比較試
料３５につい７て、時効処理の経過に伴うＩＨｃの変化
を表したものが第３図である。Br of the manufactured permanent magnet. IHcl(BH)Max is also listed in Table 1. Further, FIG. 3 shows the changes in IHc of Example Sample 31 and Comparative Sample 35 as the aging treatment progresses.
曲線ａが試料３１で、ｂが比較試料３５である。第３図
によると、本発明の実施例である試料１の場合焼結後時
効処理前では保磁力が小さく十分な最大エネルギー積を
得ることができないが、本発明による時効処理によつて
保磁力が急増し、従つて最大エネルギー積も増大するこ
とがわかる。Curve a is sample 31 and curve b is comparative sample 35. According to FIG. 3, in the case of sample 1, which is an example of the present invention, the coercive force is small before aging treatment after sintering, and it is not possible to obtain a sufficient maximum energy product, but the coercive force is increased by the aging treatment according to the present invention. It can be seen that the maximum energy product increases rapidly and therefore the maximum energy product also increases.
第１図は、ＩＨｃｌ（ＢＨ）ＭａＸ（７）ＣＵ含量依存
性と時効処理の効果を表す図で、第２図はＩＨｃ（７）
Ｆｅ含量依存性を表す図で、第３図は実施例及ひ比較例
についての時効処理に伴う保磁力の変化を表した図であ
る。Figure 1 shows IHcl(BH)MaX(7) CU content dependence and the effect of aging treatment, and Figure 2 shows IHc(7)
FIG. 3 is a diagram showing Fe content dependence, and FIG. 3 is a diagram showing changes in coercive force due to aging treatment for Examples and Comparative Examples.
Claims (1)
重量％と、銅３〜９重量％と、鉄１４重量％より多く２
５重量％以下と、残部として主としてコバルトである部
分とからなる金属粉末を、磁界中で成形し、焼結後３５
０〜９００℃の温度範囲において高温側から低温側へ多
段階に時効処理を施す永久磁石の製造方法であつて、少
なくとも、第１段の時効処理を８００〜９００℃の温度
範囲で行ない、第２段の時効処理を６００〜８００℃の
温度範囲で行なうことを特徴とする永久磁石の製造方法
。1 23-27% by weight of samarium and 0.2-7% by weight of titanium
2% by weight, 3-9% by weight of copper, and 14% by weight of iron.
A metal powder consisting of 5% by weight or less and the remainder being mainly cobalt is compacted in a magnetic field and after sintering it
A method for producing a permanent magnet in which aging treatment is performed in multiple stages from a high temperature side to a low temperature side in a temperature range of 0 to 900°C, the method comprising: performing aging treatment in at least the first stage in a temperature range of 800 to 900°C; A method for producing a permanent magnet, characterized by performing two-stage aging treatment in a temperature range of 600 to 800°C.
Priority Applications (5)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP56103434A JPS6047721B2 (en) | 1981-07-03 | 1981-07-03 | Permanent magnet manufacturing method |
| US06/392,593 US4578125A (en) | 1981-07-03 | 1982-06-28 | Permanent magnet |
| KR8202899A KR860001237B1 (en) | 1981-07-03 | 1982-06-29 | Permanent magnet |
| DE8282105921T DE3269965D1 (en) | 1981-07-03 | 1982-07-02 | Permanent magnet |
| EP82105921A EP0069362B1 (en) | 1981-07-03 | 1982-07-02 | Permanent magnet |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP56103434A JPS6047721B2 (en) | 1981-07-03 | 1981-07-03 | Permanent magnet manufacturing method |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS586105A JPS586105A (en) | 1983-01-13 |
| JPS6047721B2 true JPS6047721B2 (en) | 1985-10-23 |
Family
ID=14353926
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP56103434A Expired JPS6047721B2 (en) | 1981-07-03 | 1981-07-03 | Permanent magnet manufacturing method |
Country Status (2)
| Country | Link |
|---|---|
| JP (1) | JPS6047721B2 (en) |
| KR (1) | KR860001237B1 (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS603105A (en) * | 1983-06-21 | 1985-01-09 | Toshiba Corp | Manufacture of permanent magnet |
-
1981
- 1981-07-03 JP JP56103434A patent/JPS6047721B2/en not_active Expired
-
1982
- 1982-06-29 KR KR8202899A patent/KR860001237B1/en not_active Expired
Also Published As
| Publication number | Publication date |
|---|---|
| KR840000952A (en) | 1984-03-26 |
| JPS586105A (en) | 1983-01-13 |
| KR860001237B1 (en) | 1986-08-30 |
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