JPS6227548A - Permanent magnet alloy - Google Patents
Permanent magnet alloyInfo
- Publication number
- JPS6227548A JPS6227548A JP60166314A JP16631485A JPS6227548A JP S6227548 A JPS6227548 A JP S6227548A JP 60166314 A JP60166314 A JP 60166314A JP 16631485 A JP16631485 A JP 16631485A JP S6227548 A JPS6227548 A JP S6227548A
- Authority
- JP
- Japan
- Prior art keywords
- permanent magnet
- temperature
- rare earth
- earth elements
- rare
- 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
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
- H01F1/0577—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 sintered
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〉
本発明は高価で資源希少なコバルトを全く使用しない、
磁石特性の温度係数のすぐれた希土類・鉄系高性能永久
磁石材料に関する。[Detailed Description of the Invention] <Industrial Application Field> The present invention does not use cobalt, which is expensive and a scarce resource, at all.
Concerning rare earth/iron-based high-performance permanent magnet materials with excellent magnetic temperature coefficients.
〈従来の技術〉
現在の代表的な永久磁石材料はアルニコ、ハードフェラ
イトおよび希土類コバルト磁石である。<Prior Art> Current typical permanent magnet materials are alnico, hard ferrite, and rare earth cobalt magnets.
最近のコバルトの原料事情の不安定化にともない。Due to the recent instability in the raw material situation for cobalt.
コバルトを２０〜３０重量％含むアルニコ磁石の需要は
減り、鉄の酸化物を主成分とする安価なハードフェライ
トが磁石材料の主流を占めるようになった。一方、希土
類コバルト磁石は最大エネルギー積２０ＭＧＯｅ以上を
有する高性能磁石であるが、コバルトを５０〜６５重量
％も含むうえ、希土類鉱石中にあまり含まれていないＳ
ｍを多量に使用するため大変高価である。しかし、他の
磁石に比べて、磁気特性が格段に高いため、主として小
型で、付加価値の高い磁気回路に多く使われるようにな
つた。The demand for alnico magnets containing 20 to 30% by weight of cobalt has decreased, and inexpensive hard ferrite, whose main component is iron oxide, has become the mainstream magnet material. On the other hand, rare earth cobalt magnets are high-performance magnets with a maximum energy product of 20 MGOe or more, but they also contain 50 to 65% by weight of cobalt and S, which is not contained in rare earth ores.
It is very expensive because it uses a large amount of m. However, because their magnetic properties are much higher than that of other magnets, they have come to be used mainly in small, high-value-added magnetic circuits.
本出願人は先に高価なＳｍ’ＰＣｏを含有しない新しい
高性能永久磁石としてＦｅ−Ｂ−Ｒ系。The present applicant has previously developed the Fe-B-R system as a new high-performance permanent magnet that does not contain expensive Sm'PCo.
Ｆｅ−Ｂ−Ｒ−Ｍ系（ＲはＹを含む希土類元素のうち少
なくとも１種２Ｍは添加元素）永久磁石を提案した。（
特開昭５９−４６００８号、特開昭５９−８９４０１号
）
しかしながら、前記Ｆｅ−Ｂ−Ｒ系、Ｆｅ−Ｂ−Ｒ−Ｍ
系合金の残留磁化Ｂｒの室温附近での温度係数αは多く
のＳｍ−Ｃｏ系に比べて劣っていた。これは前記合金の
キュリ一点が一般に３００℃前後〜３７０℃と低いため
であった。We have proposed a permanent magnet of the Fe-BRM system (R is at least one rare earth element including Y and 2M is an additive element). (
However, the Fe-B-R system
The temperature coefficient α of residual magnetization Br of the system alloy near room temperature was inferior to many Sm-Co systems. This is because the Curie point of the alloy is generally as low as around 300°C to 370°C.
また本出願人は、前記合金のキュリ一点を上昇し、磁石
合金の磁石特性の温度係数改善のため。The applicant also raised the Curie point of the alloy and improved the temperature coefficient of the magnetic properties of the magnet alloy.
Ｃｏを含有した磁石合金をも提案した（特開昭５９−６
４７３３号、特開昭５９−１３２１０４号）。He also proposed a magnetic alloy containing Co (Japanese Patent Laid-Open No. 59-6
No. 4733, JP-A-59-132104).
更に本出願人は希土類の一部を重希土類（Ｔｂ。Furthermore, the applicant has selected heavy rare earths (Tb) as part of the rare earths.
Ｄｙ、Ｈｏ）で置換する事によって温度特性の飛躍的な
改善を実現できる事を示した（特開昭６Ｏ−６１７０９
）。It was shown that a dramatic improvement in temperature characteristics could be achieved by replacing Dy, Ho) (Japanese Patent Application Laid-Open No. 60-61709).
).
〈解決すべき問題点〉
しかしながら前記Ｃｏ含有のＦｅ−Ｃｏ−Ｂ−Ｒ系、
Ｆｅ−Ｃｏ−Ｂ−Ｒ−Ｍ系合金は磁石特性の温度係数
の安定化に有効であるが、Ｃｏの量を多くすると磁石特
性の劣化（特に保持力の減少）を招来するため、Ｃｏ添
加によるＢｒの温度係数αの改善はα−−ｏ、ｏｇ％／
℃程度が限度であった。<Problems to be solved> However, the Co-containing Fe-Co-BR system,
Fe-Co-B-RM-based alloys are effective in stabilizing the temperature coefficient of magnetic properties, but increasing the amount of Co leads to deterioration of magnetic properties (particularly a decrease in coercive force). The improvement in the temperature coefficient α of Br is α−-o, og%/
The limit was about ℃.
また２重希土類（Ｔｂ、Ｄｙ、Ｈｏ）で希土類の一部を
置換する方法によっては、高い保磁力を保ったままαの
値を一部、０２％／℃程度にまで改善できるが、キュリ
一点が低いために使用しうる温度範囲は狭い事が問題で
あった。この事は使用温度が１５０℃前後にまで上昇す
る進行波管では致命的な欠点である。Also, depending on the method of replacing a part of the rare earth element with a double rare earth element (Tb, Dy, Ho), it is possible to partially improve the value of α to about 0.2%/℃ while maintaining a high coercive force. The problem was that the usable temperature range was narrow because the temperature was low. This is a fatal drawback for traveling wave tubes whose operating temperature rises to around 150°C.
本発明は上述の高度な温度安定性の要求を充足するべく
さらに従来のＦｅＢＲ系ないしＦｅＢＲＭ系磁石を改良
することを基本的目的とする。The basic object of the present invention is to further improve conventional FeBR-based or FeBRM-based magnets in order to satisfy the above-mentioned requirements for high temperature stability.
〈問題点の解決手段〉
本発明によれば、上述の目的は下記の永久磁石（１）に
より達成される。<Means for solving the problem> According to the present invention, the above-mentioned object is achieved by the following permanent magnet (1).
（１）下記Ｒ１と下記Ｒ２の和をＲ（希土類元素）とし
たとき原子比で０≦Ｒ２／Ｒ１≦２．３を満足し原子百
分比テＲ１２，０〜４０％、Ｂ４〜２０％＋ Ｃｏ １
８％以下、及び残部Ｆｅ及び不可避の不純物がら成る磁
気異方性焼結永久磁石（但し、Ｒ１はＤｙ。(1) When the sum of R1 below and R2 below is R (rare earth element), the atomic ratio satisfies 0≦R2/R1≦2.3, and the atomic percentage R12, 0-40%, B4-20% + Co 1
A magnetically anisotropic sintered permanent magnet consisting of 8% or less, and the balance being Fe and unavoidable impurities (however, R1 is Dy).
Ｔｂ、Ｈｏの内一種以上でＲの３０％以上８０１％以下
、Ｒ２はＮｄとＰｒの合計が８０％以上で、残りはＲ１
以外のＹを包含する希土類元素の少なくとも一種）。One or more of Tb and Ho is 30% to 801% of R, R2 is 80% or more of Nd and Pr in total, and the rest is R1
(at least one rare earth element containing Y other than Y).
さらに１本発明の第２の視点として、上記永久磁石（１
）において、Ｆｅに部分的に代わり下記の所定％以下の
添加元素Ｍの一種以上（但し１Ｍとして二種以上の前記
添加元素を含む場合は２Ｍ含量は当該の添加元素のうち
最大値を有するものの原子百分比以下）を含む磁気異方
性焼結永久磁石が提供される。Furthermore, as a second aspect of the present invention, the permanent magnet (1
), one or more of the following additive elements M partially replaces Fe in a predetermined percentage or less (however, if 1M includes two or more of the above-mentioned additive elements, the 2M content is the one that has the maximum value among the said additive elements) magnetically anisotropic sintered permanent magnets are provided.
添加元素Ｍは下記の通りである： Ｔｉ ３ ％、 Ｚｒ ３．３％。The additive element M is as follows: Ti 3%, Zr 3.3%.
Ｈｆ ３．３％、 Ｃｒ ４．５％。Hf 3.3%, Cr 4.5%.
Ｍｎ ５ ％、 Ｎｉ ｅ ％。Mn 5%, Ni e%.
Ｔａ ７％、 Ｇｅ ３．５％。Ta 7%, Ge 3.5%.
Ｓｎ’ １．５Ｌ Ｓｂ １％。Sn' 1.5L Sb 1%.
８１ ５ ％、 Ｎｏ ５．２％。81 5%, No 5.2%.
Ｎｂ ９ ％、 Ａｌ ５ ％。Nb 9%, Al 5%.
ｖ ５．５％、Ｗ ５ ％。V 5.5%, W 5%.
Ｓｔ ５．０％、 Ｚｎ ０．
５％ 。St 5.0%, Zn 0.
5%.
〈好適な態様に基づ〈発明の開示及び作用〉以下に本発
明をさらに詳述する。<Disclosure and operation of the invention> The present invention will be described in further detail below based on preferred embodiments.
航空機に用いられる進行波管や自動誘導装置用計器など
の用途には高い保磁力と残留磁化Ｂｒの高い温度安定性
が広い温度範囲に渡って要求される。従来のＳｍＣｏ
磁石などではＥｒ等で７〜８
Ｓｍを置換することによってＢｒをかなり犠牲にしても
αの値（絶対値）を小さくすることがはかられてきた。For applications such as traveling wave tubes used in aircraft and instruments for automatic guidance systems, high coercive force and high temperature stability of residual magnetization Br are required over a wide temperature range. Conventional SmCo
In magnets, attempts have been made to reduce the value (absolute value) of α by replacing 7 to 8 Sm with Er or the like, even if Br is sacrificed considerably.
ＳｍやＣｏを全く含まないＦｅ−Ｂ−Ｒ系、Ｆｅ−Ｂ−
Ｒ−Ｍ系では磁気特性の温度係数が大きいため、そのす
ぐれた磁気特性にもかかわらず前記の用途には使用でき
なかった。Fe-B-R system containing no Sm or Co, Fe-B-
Since the temperature coefficient of the magnetic properties of the RM system is large, it could not be used for the above-mentioned applications despite its excellent magnetic properties.
Ｃｏ添加による方法（特開昭５９−６４７３３号。Method by adding Co (Japanese Patent Application Laid-Open No. 59-64733).
特開昭５９−１３２１０４号）ではαの改善は−０，０
８％／℃が限度である上、保磁力がＣｏの量とともに減
少するので、Ｃｏを含む Ｆｅ−Ｃｏ−Ｂ−Ｒ系、
Ｆｅ−Ｃｏ−Ｂ−Ｒ−Ｍ系でも前記の用途にはなお不十
分であった。In JP-A-59-132104), the improvement of α is -0.0.
Since the limit is 8%/℃ and the coercive force decreases with the amount of Co, Fe-Co-B-R system containing Co,
Even the Fe-Co-BRM system was still insufficient for the above-mentioned applications.
本出願人は以上のことから出発しさらに改善をめざして
前記Ｆｅ−Ｂ−Ｒ系、Ｆｅ−Ｂ−Ｒ−Ｍ系磁石合金中の
主相であるＲ Ｆｅ１４Ｂ化合物（単結晶）の磁気的
性質を全てのＲについて詳細に調べたところ、軽希土類
Ｒ２と重希土類Ｒ１を含む（ＲＩ Ｒ２） Ｆｅ
Ｂを主相とし１−ｘ ｘ ２ １４
て含む合金を磁石化すれば、αの値を非常に小さくでき
ることがわかった。この方法はＲ１がＴｂ。Starting from the above, the present applicant aims to further improve the magnetic properties of the R Fe14B compound (single crystal) which is the main phase in the Fe-B-R and Fe-B-R-M magnet alloys. When we investigated all R in detail, we found that (RI R2) Fe, including light rare earth R2 and heavy rare earth R1
It has been found that by magnetizing an alloy containing 1-x x 2 14 B as a main phase, the value of α can be made extremely small. In this method, R1 is Tb.
Ｄｙ、Ｈｏのうち少なくとも一種の場合にのみ可能であ
ることもわかった（特開昭６Ｏ−６１７０９）。It was also found that this is possible only in the case of at least one of Dy and Ho (Japanese Patent Laid-Open No. 60-61709).
しかし、キュリ一点が低いためにαを小さくできる温度
範囲が狭く、αの値の温度変化も大きかった。However, because the Curie point is low, the temperature range in which α can be reduced is narrow, and the temperature change in the value of α is large.
そこで本出願人は、Ｃｏ添加を併用する事によってキュ
リ一温度を上昇せしめ、より高い温度特性を実現せしめ
るべく検討を行ない、Ｃｏ添加と重希土類（Ｔｂ、Ｄｙ
、Ｈｏ）添加とを併用する方法が極めて有効であ□る事
を知見した。その原理は以下のごとくである。Therefore, the present applicant investigated the possibility of raising the Curie temperature and realizing higher temperature characteristics by combining Co addition and heavy rare earth (Tb, Dy).
, Ho) was found to be extremely effective. The principle is as follows.
図１は本発明による永久磁石組成を含む合金中にある主
成分であり、磁気的に硬い相の一例として１重希土類と
してＨＯを含む正方晶化合物の（Ｎｄ Ｈｏ）
（Ｆｅ Ｃｏ） Ｂの１−ｘ ｘ ２
１−）’ ｙ １４飽和磁束密度の規格化温
度（Ｔ ／ Ｔ ｃ ）に対する依存性を示す。Ｈｏ、
Ｃｏをともに添加しない系（ｘ＝ｙ＝ｏ）では、永久磁
石の使用温度を一３０℃〜６０℃とした場合図１の温度
軸（Ｔ ／ Ｔ ｃ ）上ではＡで示した部分に対応し
、第１図に示した磁束密度一温度（Ｉ−Ｔ）曲線上のａ
−ｂの部分で動作する事になり、Ｂｒの温度係数αの値
はその絶対値が大きい。Ｃｏのみを添加した系ではキュ
リ一温度（Ｔｃ）の上昇のため、同じ温度範囲はＢの部
分に移り対応する磁化一温度曲線はｃ −ｄで示した部
分となり、αの値が改善される。また、Ｈｏのみを添加
すると１例えばｘ−０，４の時は磁石の動作温度範囲は
ｅ−ｆであり、ａ−ｂ。Figure 1 shows the main components in an alloy containing a permanent magnet composition according to the present invention, and as an example of a magnetically hard phase, a tetragonal compound (NdHo) containing HO as a single rare earth element is shown.
(Fe Co) 1-x x 2 of B
1-)' y14 The dependence of the saturation magnetic flux density on the normalized temperature (T/Tc) is shown. Ho,
In a system in which Co is not added (x = y = o), when the operating temperature of the permanent magnet is -30°C to 60°C, it corresponds to the part indicated by A on the temperature axis (T / T c ) in Figure 1. and a on the magnetic flux density-temperature (IT) curve shown in Figure 1.
It will operate in the -b part, and the absolute value of the temperature coefficient α of Br is large. In the system in which only Co is added, the Curie temperature (Tc) increases, so the same temperature range shifts to part B, and the corresponding magnetization-temperature curve becomes the part shown by c - d, improving the value of α. . Further, when only Ho is added, the operating temperature range of the magnet is e-f and a-b when x-0,4, for example.
ｃ−ｄの時に比べてαの値は飛躍的に改善される。The value of α is dramatically improved compared to the case of c-d.
更に、Ｈｏを含む系にＣＯを合わせて添加すれば。Furthermore, if CO is added to the system containing Ho.
Ｔｃの上昇によって温度領域はＴ ／ Ｔ ｃ軸上でｇ
−ｅに移り、αの値が更に改善されるとともに。Due to the increase in Tc, the temperature region becomes g on the T/Tc axis.
-e, and the value of α is further improved.
その使用温度範囲は拡大される。Its operating temperature range is expanded.
以上の効果は重希土類がＨｏ以外の場合でも。The above effects can be obtained even when the heavy rare earth is other than Ho.
Ｔｂ、ＤＹ、 についても同様にあることが判った。It was found that the same holds true for Tb, DY, and so on.
またＴｂ、Ｄｙ、Ｈｏの３種を適当な比率で混合したも
のを用いる事もできる。Furthermore, a mixture of Tb, Dy, and Ho in an appropriate ratio can also be used.
即ち、希土類元素ＲのうちＤｙ、Ｔｂ、Ｈｏの一種以」
二のＲ１と、Ｎｄ９Ｐｒなどの軽希土類元素Ｒ２を特定
比率に組み合わせ含有し、更にＦｅの一部をＣｏで置換
することによって、従来ＰｅＢＲ系磁石では得られなか
った高い保磁力とＢｒの温度係数の顕著な改善を達成す
ることができた。That is, among the rare earth elements R, one or more of Dy, Tb, and Ho.
By containing a combination of R1 and light rare earth element R2 such as Nd9Pr in a specific ratio, and further substituting a part of Fe with Co, high coercive force and temperature coefficient of Br, which could not be obtained with conventional PeBR magnets, are achieved. We were able to achieve a significant improvement in
更に１本発明による特定のＲ及びＣｏ含をの成分系では
、 １ｌｌｃの増大のみならず、減磁曲線の角形性の改
善、即ち磁気回路中の動作点の変動に対する安定性を増
大する効果を具備することが判った。Furthermore, the specific R and Co-containing component system according to the present invention has the effect of not only increasing 1llc but also improving the squareness of the demagnetization curve, that is, increasing the stability against fluctuations in the operating point in the magnetic circuit. It turned out to be equipped.
本発明の永久磁石材料の主相はＦｅ−Ｒ−Ｂ正方品化合
物であり中心組成はＲ２Ｆｅ１４Ｂであると考えられる
。また、主相の粒界相としてＲリッチな非磁性相が有効
量存在することが重要である。It is believed that the main phase of the permanent magnet material of the present invention is a Fe-R-B tetragonal compound, and the central composition is R2Fe14B. Further, it is important that an effective amount of an R-rich nonmagnetic phase exists as a grain boundary phase of the main phase.
非磁性相はわずかてもイ（効であり例えば１ｖ０１％は
十分な量である。Even a small amount of the non-magnetic phase is effective; for example, 1v01% is a sufficient amount.
なおＦｅＢＲ系磁石のｉＨｃを増大させるために様々の
検討を行った結果、以下の方法が有効である。In addition, as a result of various studies to increase the iHc of FeBR magnets, the following method is effective.
即ち。That is.
（１） Ｒ（Ｒ＋Ｒ２）又はＢの含有量を多くする（２
）Ｒ／Ｒ１の比率を特定範囲とする（３）Ｃｏを特定含
有量とする
（４）添加元素Ｍを加える（ Ｉ’ｅＢＲＭ系磁石）。(1) Increase the content of R (R+R2) or B (2
) Setting the R/R1 ratio within a specific range (3) Setting Co in a specific content (4) Adding the additive element M (I'eBRM magnet).
しかしながら、Ｒ又はＢの含有量を増加する方法は、各
々１ｌｌｃを増大するが、含有量が多くなるにつれてＢ
ｒが低下し、その結果（Ｂｌｌ）ｍａｘの値も低くなる
。However, the method of increasing the content of R or B increases 1llc each, but as the content increases, B
r decreases, and as a result, the value of (Bll)max also decreases.
Ｒ２／Ｒ１の値が大な程（ＢＨ）ｆｆｌａｘが大きくな
るがαの値もその絶対値が大となるので、Ｒ２／Ｒ１の
値は前記範囲内とする必要がある。The larger the value of R2/R1 (BH), the larger the fflax becomes, but the absolute value of the value of α also becomes larger, so the value of R2/R1 needs to be within the above range.
また、Ｆｅの一部を特定量のＣＯにて置換することによ
りキュリ一点の上昇により、熱安定性を増すと同時にＲ
２の置換量を少なくすることができるが、Ｃｏの添加量
が多くなりすぎると、 ｉＨｃの低下をきたし、高い磁
気特性を保つことかできなくなる。In addition, by replacing a part of Fe with a specific amount of CO, thermal stability is increased by one Curie point, and at the same time R
Although the amount of substitution of 2 can be reduced, if the amount of Co added is too large, iHc decreases and high magnetic properties cannot be maintained.
また、添加元素ＭもｉＨｃ増大の効果を有するが。Additionally, the additive element M also has the effect of increasing iHc.
添加量の増加につれて（ＢＨ）ｆｆｌａｘが低下し飛躍
的な改善効果には繋がらない。As the amount added increases, (BH) fflax decreases and does not lead to a dramatic improvement effect.
本発明の永久磁石においては１重希土類元素Ｒ１として
＋ ＤＹ ｒ Ｔ ｂ ｒ Ｈｏの少くとも１種を含有
することと、Ｒ２としてＮｄ、Ｐｒを主体とすることと
、さらにＲ２／Ｒ１の比率を特定範囲とし、Ｃｏを特定
量倉荷しＲ，Ｂの所定範囲内の組成とに基づき、特に時
効処理を施した場合のＢｒの温度係数の安定化とｌ１ｌ
ｃの増大が顕著である。即ち、上記特定の組成の合金か
らなる磁気異方性焼結体に時効処理を施すと、Ｂｒの値
を損ねることなく ＩＨｃを増大させ、さらに減磁曲線
の角形性改善の効果もあり、 （ＢＨ）ｆｆｌａｘは同
等かまたはそれ以上となり、その効果は顕著である。な
お。In the permanent magnet of the present invention, the single rare earth element R1 contains at least one of + DY r T b r Ho, R2 is mainly composed of Nd and Pr, and the ratio of R2/R1 is Stabilization of the temperature coefficient of Br and l1l, especially when aging treatment is performed, based on a specific range, a specific amount of Co stored, and the composition of R and B within a predetermined range.
The increase in c is significant. That is, when a magnetically anisotropic sintered body made of an alloy with the above-mentioned specific composition is subjected to aging treatment, IHc is increased without impairing the Br value, and there is also the effect of improving the squareness of the demagnetization curve. BH) fflax is the same or higher, and the effect is significant. In addition.
Ｒ，Ｂ、Ｃｏの範囲と、Ｈｏ、Ｄｙ、Ｔｂの少くとも１
種の含を量と（Ｎｄ＋Ｐｒ）の量を規定することにより
２時効処理前においてもＨ１ｅ約１０ｋＯｅ以北が達成
され、Ｒ内におけるＲ１の所定の含Ｈにより時効処理の
効果がさらに著しく付加される。The range of R, B, Co and at least one of Ho, Dy, Tb
By specifying the content of seeds and the amount of (Nd+Pr), H1e of about 10 kOe or more can be achieved even before the aging treatment, and the effect of the aging treatment is further significantly added by the predetermined H content of R1 in R. Ru.
即ち１本発明によれば（Ｂｔ（）ｍａｘ １０ ＭＧＯ
ｅ以上を保有したまま、 １ｉｆｅ １０ ｋｏｅ以上
で示される十分な安定性を兼ね備え、しかもＢｒの温度
係数を一３０℃から６０°Ｃの範囲で絶対値で０．０５
％／’Ｃ以下におさえ、従来の高性能磁石よりも広範な
用途に適用し得る高性能磁石を提供する。That is, according to the present invention, (Bt()max 10 MGO
It has sufficient stability as shown by 1 ife 10 koe or more while maintaining the temperature coefficient of Br of 0.05 in absolute value in the range of -30°C to 60°C.
%/'C or less, and provides a high-performance magnet that can be applied to a wider range of uses than conventional high-performance magnets.
（Ｂｌｌ）ｍａｘ 、 ｉＨｃの最大値は各々３０．２
ＭＧＯｅ（後述第１表、 Ｎｏ、 １）、１７． ０
ｋＯｅ （第１表、Ｎ０１１２）を示した。The maximum values of (Bll)max and iHc are each 30.2
MGOe (Table 1 below, No. 1), 17. 0
kOe (Table 1, N0112).
本発明の永久磁石に用いるＲは、ＲとＲ２の和より成る
が、ＲとしてＹを包含し、Ｎｄ、Ｐｒ。R used in the permanent magnet of the present invention is the sum of R and R2, and R includes Y, Nd, Pr.
Ｌａ、Ｃｅ、Ｔｂ、Ｄｙ、Ｈｏ、Ｅｕ、Ｐｍ。La, Ce, Tb, Dy, Ho, Eu, Pm.
Ｌｕの希土類元素である。そのうちＲ１はＤＹ。Lu is a rare earth element. Of these, R1 is DY.
Ｔｂ、Ｈｏの３種のうち少なくとも１種を用いて。Using at least one of three types: Tb and Ho.
その含有量はＲの３０％以上８０％以下でＲ２は上記３
種以外の希土類元素を示し、特に軽希土類の内Ｎ ｄと
Ｐｒの合；１゛を８０％以上包含するもの（特に９５％
以」二のもの）を用いる。Its content is 30% or more and 80% or less of R, and R2 is the above 3
Indicates rare earth elements other than species, especially those containing 80% or more of the combination of Nd and Pr (particularly 95%) of light rare earths.
(2) shall be used.
これらＲは必ずしも純希土類元素でなくてもよく、工業
上入手可能な範囲で製造上不可避な不純物（Ｓｍ、Ｇｄ
、Ｅ ｒ、Ｔｍ、Ｙｂ、等の他の希土類元素Ｃａ、Ｍｇ
、Ｆｅ、Ｔｉ、Ｃ，Ｏ等）を微慣含有するものでも差支
えない。なおＳｍ。These R do not necessarily have to be pure rare earth elements, but may contain impurities (Sm, Gd,
, Er, Tm, Yb, etc., other rare earth elements Ca, Mg
, Fe, Ti, C, O, etc.). Furthermore, Sm.
Ｅｒ及びＴｍのＲ２Ｆｅ１４Ｂは室温以下で一軸異方性
を示さない。R2Fe14B of Er and Tm does not exhibit uniaxial anisotropy below room temperature.
Ｂ（ホウ素）としては、純ボロン又はフェロボロンを用
いることができ、不純物としてＡＩ。Pure boron or ferroboron can be used as B (boron), and AI can be used as the impurity.
Ｓｉ、Ｃ等を含むものも用いることができる。Materials containing Si, C, etc. can also be used.
本発明の永久磁石は、既述のＲをＲとＲ２の合計として
原子比で０≦Ｒ２／Ｒ１≦ ２．３を満足し原子百分比
でＲ１２，０〜４０％、８４〜２０％、Ｃｏ１８％以下
、残部Ｆｅの組成においてαの絶対値が０．０５％以下
、保磁力ＩＨｃ約１０ ｋｏｅ以上、残留磁束密度Ｂ
ｒ ８ ｋＧ以上、最大エネルギー積（ＢＨ）Ｂｘｌ
０ＭＧＯｅ以上の高保磁力、高いＢ「の温度安定性。The permanent magnet of the present invention satisfies the atomic ratio of 0≦R2/R1≦2.3, where R is the sum of R and R2, and the atomic percentage is R12, 0-40%, 84-20%, Co18%. Below, in the composition of the remaining Fe, the absolute value of α is 0.05% or less, the coercive force IHc is about 10 koe or more, and the residual magnetic flux density B
r 8 kG or more, maximum energy product (BH) Bxl
High coercive force of 0MGOe or higher, high temperature stability of B.
高エネルギー積を示す。ここにαは一３０℃以上６０℃
以下の温度範囲について上記の値を満足できる。Shows high energy product. Here α is -30℃ or more 60℃
The above values can be satisfied for the following temperature ranges.
０．８６≦Ｒ２／ Ｒｔ≦ ０．８８．Ｒ１３〜１９％
、８ ５〜１１％、Ｃｏ１５％〜２０％、残部Ｆｅの組
成はαの絶対値が一３０℃から６０°Ｃの温度範囲で０
．０２％／’Ｃ以下最大エネルギー積（ＢＨ）ｍａｘ
１２ ＭＧＯｅ以上を示し。0.86≦R2/Rt≦0.88. R13-19%
, 8 5-11%, Co 15%-20%, balance Fe composition, the absolute value of α is 0 in the temperature range from 130°C to 60°C.
．． 02%/'C or less Maximum energy product (BH) max
12 Indicates MGOe or higher.
好ましい範囲である。This is a preferable range.
また、Ｒ１としてはＨｏ、またはＨＯとＤｙの組み合せ
が特に望ましい。Further, as R1, Ho or a combination of HO and Dy is particularly desirable.
Ｒの量を１２，０％以上としたのは、Ｒがこの量よりも
少なくなると水系合金化合物中にＦｅが析出して保磁力
が急激に低下するためである。Ｒの上限を４０％とした
のは、４０％以上でも保磁力は１０ｋＯｅ以上の大きい
値を示すがＢｒが低下して（Ｂｉｔ）ｍａｘ １０ Ｍ
ＧＯｅ以上を実現するために必要なりｒ（約７ ｋＧ）
が得られなくなるからである。The reason why the amount of R is set to 12.0% or more is because if the amount of R is less than this amount, Fe will precipitate in the water-based alloy compound and the coercive force will drop sharply. The reason why the upper limit of R is set to 40% is that even if it is 40% or more, the coercive force shows a large value of 10 kOe or more, but the Br decreases (Bit) max 10 M
Required to achieve GOe or higher (approximately 7 kG)
This is because it becomes impossible to obtain.
Ｒ２／Ｒ１の比を２．３以下としたのは、Ｂｒの温度係
数αの絶対値がこの範囲で一３０℃から６０℃の温度範
囲で０，０５％／℃を越えず、しかも（ＢＨ）ｍａｘ
１０ ＭＧＯｅ以上を得るために必要なりｒの値が確保
されるためである。The reason why the ratio of R2/R1 is set to 2.3 or less is that the absolute value of the temperature coefficient α of Br does not exceed 0.05%/℃ in the temperature range from -30℃ to 60℃ in this range, and (BH )max
This is because the value of r required to obtain 10 MGOe or more is secured.
本発明において、Ｒ／Ｒ１比の増大に伴い飽和磁束密度
Ｂｓは温度の変化に従い第１図に示す如く変化する。第
１図において例えばｘ−０，４゜０．７は夫々Ｒ２／Ｒ
１比１．５，０．４に凡そ対応する。αの絶対値が最小
である温度範囲はＸの値の増大と共に高７Ｈ側ヘシフト
する傾向がある。In the present invention, as the R/R1 ratio increases, the saturation magnetic flux density Bs changes as shown in FIG. 1 as the temperature changes. In Figure 1, for example, x-0, 4°0.7 are R2/R, respectively.
1 ratio approximately corresponds to 1.5 and 0.4. The temperature range in which the absolute value of α is minimum tends to shift toward the high 7H side as the value of X increases.
また、第１図をベースとし所定の温度範囲内において最
小のαを達成するＲ ／Ｒ１比が適宜選択可能である
。なおＲ２／Ｒ１比は第１図では（１−ｘ）／ で与
えられる。第１図は重希土類がＨｏの場合であるが２例
えばＨｏの代りにＤｙを用いればＢｓの温度変化は規格
化された温度に対し第２図のようになり、これにもとづ
いて同様の設計が可能である。Furthermore, based on FIG. 1, the R/R1 ratio that achieves the minimum α within a predetermined temperature range can be selected as appropriate. Note that the R2/R1 ratio is given by (1-x)/ in FIG. Figure 1 shows the case where the heavy rare earth is Ho.2 For example, if Dy is used instead of Ho, the temperature change of Bs will be as shown in Figure 2 with respect to the normalized temperature, and based on this, similar designs can be made. is possible.
本発明の第２の視点によれば添加元素Ｍを所定量以下含
む。この添加元素ＭはｉＨｃを増し、減磁曲線の角形性
を増す効果があるが、一方その添加量が増すに従い、Ｎ
ｉを除いて１本発明による永久磁石の主相であるＲ２Ｆ
８１４Ｂ化合物のキュリ一温度を下げる事によってＢｒ
の温度係数の低下をきたすか、又は非磁性化合物の析出
を招いてＢｒを減少せしめることにより磁気エネルギー
積の低下をきたすか、更に或いは永久磁石の焼結組織に
影響を及ぼして抗磁力を劣化せしめるかのいずれか、又
はこれらの要因の複合した原因によって磁石特性の劣化
をきたす。従って、添加元素の各々の上限は下記の値以
下と定められる。According to the second aspect of the present invention, the additive element M is contained in a predetermined amount or less. This additive element M has the effect of increasing iHc and increasing the squareness of the demagnetization curve, but on the other hand, as the amount added increases, N
R2F, which is the main phase of the permanent magnet according to the present invention, except for i
By lowering the Curie temperature of the 814B compound, Br
The temperature coefficient of the permanent magnet decreases, or the magnetic energy product decreases by inviting the precipitation of non-magnetic compounds and reducing Br, or the coercive force deteriorates by affecting the sintered structure of the permanent magnet. Deterioration of magnetic properties is caused by either one of these factors or a combination of these factors. Therefore, the upper limit of each additive element is determined to be less than or equal to the value below.
Ｔｊ ３ ％、 Ｚｒ ３．３％。Tj 3%, Zr 3.3%.
Ｉ１１’ ３．３％、 Ｃｒ ４．５％。I11' 3.3%, Cr 4.5%.
Ｍｎ ５ ％、 旧 ６ ％。Mn 5%, old 6%.
Ｔａ ７ ％、 Ｇｅ ３．５％。Ta 7%, Ge 3.5%.
Ｓｎ １．５％、 Ｓｂ Ｌ ％。Sn 1.5%, Sb L%.
Ｂｉ ５％、 Ｍｏ ５．２％。Bi 5%, Mo 5.2%.
Ｎｂ ９ ％、 Ａｌ ５ ％。Nb 9%, Al 5%.
■５．５％、Ｗ ５ ％。■5.5%, W 5%.
Ｓｔ ５．０％、 Ｚｎ ０．５％但し、
２種以上のＭを添加する場合のＭ合計の上限は、実際に
添加された当該のＭ元素の各上限値のうち最大値を有す
るものの値以下となる。例えばＴｉ、Ｎ ｉ、Ｎｂを添
加した場合には、Ｎｂの９％以下となる。Ｍとしては、
Ｖ、Ｎｂ、Ｔａ。St 5.0%, Zn 0.5%However,
When two or more types of M are added, the upper limit of the total M is less than or equal to the maximum value among the upper limit values of the M elements actually added. For example, when Ti, Ni, and Nb are added, the amount becomes 9% or less of Nb. As for M,
V, Nb, Ta.
Ｍｏ、Ｗ、Ｃｒ、Ａ １が好ましい。なおＮｉ。Mo, W, Cr, and A1 are preferred. Furthermore, Ni.
Ｍ ｎの限度はｉ Ｈｃから定められる。但し上記添加
元素Ｍの含ｅ−２は一般にＢｒの所望値に応じて適宜上
記範囲内で選択でき、一部のＭ（Ｓｂ、Ｓｎ。The limit of M n is determined from i Hc. However, the content e-2 of the additional element M can generally be selected appropriately within the above range depending on the desired value of Br, and may include some M (Sb, Sn, etc.).
Ｚｎ等）を除き一役に０．１〜３原子％以下（好ましく
は１９６以下、特に０．５％以下）が育効である。なお
これらの添加元素Ｍは母合金中に＋Ｓ ’ＧＩＴさせて
おくことができ、酸化物又は他の構成元素との混合酸化
物として母合金製造のための直接還元の際の出発原料中
に配合しておくこともできる。A content of 0.1 to 3 atomic % or less (preferably 196 or less, especially 0.5% or less) is effective for growth, excluding Zn, etc.). These additional elements M can be left in the master alloy as +S'GIT, and can be incorporated into the starting materials during direct reduction for producing the master alloy as oxides or mixed oxides with other constituent elements. You can also leave it as is.
このＭはまた。泣界相成分中に合金化して添加すること
もできる。この拉界柑成分は、Ｒ５０原子％以上のＲ−
Ｆｅ合金もしくはＲ５０原子％以上。This M is again. It can also be added as an alloy to the phase component. This Lakaikan component contains R50 atomic% or more of R-
Fe alloy or R50 atomic% or more.
Ｂ４０原子９６以下、残部Ｆｅから成るＲ−Ｂ−Ｆｅ合
金の１以上、又はこれらと、金属コバルト；金属ホウ素
；フェロボロン；Ｒ１５原子％以下。One or more R-B-Fe alloys consisting of 96 atoms or less of B40 and the balance Fe, or together with metal cobalt; metal boron; ferroboron; and R15 atomic % or less.
Ｂ３ｇ原子％以上、残部Ｆｅから成るＢリッチＢ−Ｆｅ
−Ｃｏ−Ｒ合金からなる群から選ばれた１以１−の粉末
との混合物から構成できるものである。B-rich B-Fe consisting of 3g atomic % or more of B and the balance Fe
It can be composed of a mixture with one or more powders selected from the group consisting of -Co-R alloys.
本発明の永久磁石は焼結体として得られ、その平均結晶
粒径は、 ＦｅＢＣｏＲ系において１〜８０μｍ。The permanent magnet of the present invention is obtained as a sintered body, and its average crystal grain size is 1 to 80 μm in FeBCoR system.
ＰｅＢＲＣｏＭ系において１〜９０μｍの範囲にあるこ
とが重要である（好ましくは夫々２〜４０μｍ）。In the PeBRCoM system it is important to have a range of 1 to 90 μm (preferably 2 to 40 μm respectively).
焼結は９００〜１２００℃の温度で行うことができる。Sintering can be carried out at a temperature of 900-1200°C.
時効処理は焼結後３５０℃以上当該焼結温度以下、好ま
しくは４５０〜８００℃で行うことができる。さらに好
ましい時効処理は次の通りである。The aging treatment can be carried out after sintering at a temperature of 350°C or higher and lower than the sintering temperature, preferably 450 to 800°C. A more preferable aging treatment is as follows.
即ち、焼結後７５０〜１０００℃（好ましくは７７０〜
９２０℃）の温度で１次熱処理を行い。That is, after sintering, the temperature is 750-1000°C (preferably 770-1000°C).
The first heat treatment was performed at a temperature of 920°C.
その後３〜２０００℃／ｍ１ｎ（好ましくは２０〜ｂ
度まで冷却し、さらに４８０〜７００℃（好ましくは５
５０〜６５０℃）の温度で２次熱処理する。Thereafter, it is cooled to 3 to 2000°C/m1n (preferably 20 to 20°C), and then further cooled to 480 to 700°C (preferably
A secondary heat treatment is performed at a temperature of 50 to 650°C.
熱処理は凡そ０．５〜１２時間行う。The heat treatment is performed for approximately 0.5 to 12 hours.
焼結に供する合金粉末は０．３〜８０μｍ（好ましくは
１〜４０μｍ、特に好ましくは２〜２０μｍ）の平均粒
度のものが適当である。これらの焼結条件等については
、すでに同一出願人の出願に係る特開昭５９−２１５４
６０号、５９−２１９４５２号に開示されている。The alloy powder used for sintering has an average particle size of 0.3 to 80 μm (preferably 1 to 40 μm, particularly preferably 2 to 20 μm). These sintering conditions, etc. have already been disclosed in Japanese Patent Application Laid-Open No. 59-2154 filed by the same applicant.
No. 60, No. 59-219452.
なお、特にαの値が０．０５％／℃以下の高い磁気特性
の温度安定性を実現するためには、減磁曲線の角型性を
良好にするために酸素、炭素。In addition, in order to achieve high temperature stability of magnetic properties with an α value of 0.05%/°C or less, oxygen and carbon are used to improve the squareness of the demagnetization curve.
Ｃａの含有量を規制することが好ましい。即ち。It is preferable to regulate the content of Ca. That is.
本発明に用いる合金粉末の酸素含有量は６０００ｐｐｍ
以下、炭素含有量は１０００ ｐｐＩ１１以下、’Ｃａ
含有量は２０００ ｐｐｍ以下にすることが好ましい。The oxygen content of the alloy powder used in the present invention is 6000 ppm
Below, the carbon content is 1000 ppI11 or less, 'Ca
The content is preferably 2000 ppm or less.
即ち１本発明に用いる合金粉末に含まれる酸素は最も酸
化しやすい希土類元素と結合して希土類酸化物を形成し
、酸素含有量が６０００ ｐｐｍを越えると永久磁石中
に酸化物（Ｒ２０３）として４％以上残留することにな
り、磁石特性とくに保磁力が１０ｋＯｅ以下になるので
好ましくない。That is, 1. The oxygen contained in the alloy powder used in the present invention combines with the rare earth element that is most easily oxidized to form a rare earth oxide, and when the oxygen content exceeds 6000 ppm, it is dissolved in the permanent magnet as an oxide (R203). % or more remains, which is not preferable because the magnetic properties, especially the coercive force, become less than 10 kOe.
含有炭素量が１０００ ｐｐｍを越えると酸素の場合と
同様炭化物（ＲＣ２）として永久磁石中に残留し著しい
保磁力の低下を生ずる。If the carbon content exceeds 1000 ppm, it remains in the permanent magnet as carbide (RC2), similar to the case with oxygen, resulting in a significant decrease in coercive force.
またカルシウム含有量が２０００ ｐＰｆｆｌを越える
と後続のこの合金粉末を用いて磁石化する途中の焼結工
程において還元性の極めて高いＣａ蒸気を多量に発生し
、熱処理炉をいちじるしく汚染することになって、場合
によっては熱処理炉の炉壁を損耗して工業的に安定な生
産が不可能となる。Furthermore, if the calcium content exceeds 2000 pPffl, a large amount of highly reducing Ca vapor will be generated during the subsequent sintering process during which this alloy powder is used to create a magnet, which will seriously contaminate the heat treatment furnace. In some cases, the furnace wall of the heat treatment furnace may be damaged, making industrially stable production impossible.
また、でき上った永久磁石中に含まれる。Ｃａｆｆ１も
多くなって磁石特性の劣化を生ずる。なお、上記の酸素
、炭素、（ａ含有量の条件は合金粉末（配合・混合を含
む）微粉末状態で達成することが好ましい。It is also included in the finished permanent magnet. Caff1 also increases, causing deterioration of the magnet characteristics. Note that it is preferable that the above-mentioned oxygen, carbon, and (a) content conditions are achieved in the state of alloy powder (including blending and mixing) in a fine powder state.
なお最終製品中のＭｇ、Ｐは各１．７原子％以下（Ｂｒ
による）とし、Ｓ、Ｃｕは各２原子％以下とする（Ｂｒ
による）が、これらはいずれもＢｒの減少を招くので少
ない程よい。Note that Mg and P in the final product are each 1.7 at% or less (Br
), and S and Cu are each 2 atomic % or less (Br
However, since both of these lead to a decrease in Br, the smaller the better.
〈実施例〉
以下本発明の態様及び効果について実施例に従って説明
する。試料はつぎの工程によって作成した。<Examples> Aspects and effects of the present invention will be described below with reference to Examples. The sample was prepared by the following steps.
不純物について約１ ｋｇの合金を高周波炉によっテ溶
解し、鉄ハース上に鋳造してインゴットを得た。出発原
料はＦｅとして純度９９．９％の電解鉄、Ｂとしてフェ
ロボロン合金（１９，３８％Ｂ、５．３２％ＡＩ、０．
７４％Ｓｉ、０．０３％Ｃ２残部Ｆｅ）、Ｃｏとして純
度９９．９％の電解Ｃｏ、Ｒとして純度９９．７％以上
（不純物は主として他の希土類金属）を使用。Approximately 1 kg of the alloy containing impurities was melted in a high frequency furnace and cast on an iron hearth to obtain an ingot. The starting materials are electrolytic iron with a purity of 99.9% as Fe, and ferroboron alloy (19.38% B, 5.32% AI, 0.9% as B).
74% Si, 0.03% C2 balance Fe), electrolytic Co with a purity of 99.9% as Co, and purity 99.7% or more as R (impurities are mainly other rare earth metals).
このインゴットをショークラッシャーで粉砕し。Crush this ingot with a show crusher.
更にフロン中でボールミルにより微粉砕して粉末を得た
。この粉末の平均粒径はフィッシャーの粒度計にて約２
２μであった。粉末は約１０ｋＯｅの磁場中で配向され
て磁場方向に垂直な方向から圧縮した。得られたグリー
ンコンパクトは充分な脱ガス処理の後、Ａｒ雰囲気中で
約１０８０℃〜１１２０℃の温度で１．５時間焼結し、
更に熱処理をほどこした。磁石特性は通常のＢ−Ｈ及び
Ｉ−Ｈトレーサーを用い閉回路で行った。熱処理は８０
０℃Ｘｌｈの後急冷し６３０℃ｘｉｈの２次熱処理を行
った。The mixture was further pulverized using a ball mill in Freon to obtain a powder. The average particle size of this powder is approximately 2
It was 2μ. The powder was oriented in a magnetic field of about 10 kOe and compressed from a direction perpendicular to the direction of the magnetic field. After sufficient degassing, the obtained green compact was sintered in an Ar atmosphere at a temperature of about 1080°C to 1120°C for 1.5 hours.
Further heat treatment was applied. Magnetic properties were measured in a closed circuit using conventional B-H and I-H tracers. Heat treatment is 80
After heating at 0°C xlh, it was rapidly cooled and subjected to a secondary heat treatment at 630°C xih.
得られた試料を加工研摩後、電磁石型の磁石特性試験に
よって磁石特性を調べた。After processing and polishing the obtained sample, the magnetic properties were investigated by an electromagnetic type magnetic property test.
ＲとしてＤｙ、Ｔｂ、Ｈｏ、Ｒ２としてＮｄｌ 又はＰｒを用いＲとＲ２を組合せた合金を作り。Dy, Tb, Ho as R, Ndl as R2 Or make an alloy combining R and R2 using Pr.
上記の工程により磁石化した。その結果を比較例と共に
第１表に示す。It was magnetized by the above steps. The results are shown in Table 1 along with comparative examples.
（以下余白）
第１表においてｆｉｌｅ、Ｂ ｒ 、 （Ｂｌｌ）ｍａ
ｘの値は室温付近（２５℃）での測定値を示しＢｒの温
度係数αの値は一３０℃〜６０℃での絶対値の最大値に
符号を付したものを示す。(Margins below) In Table 1, file, B r , (Bll)ma
The value of x indicates the value measured near room temperature (25°C), and the value of the temperature coefficient α of Br indicates the maximum absolute value at -30°C to 60°C with a sign attached.
第３図に、第１表に示した実施例番号２，３゜４のＢｒ
の温度変化を比較例２１．２２と比較して示す。In Fig. 3, Br of Example No. 2,3゜4 shown in Table 1 is shown.
The temperature changes in Comparative Examples 21 and 22 are shown below.
第１図は正方品化合物（ＮｄＨｏ）
ｌ−Ｘ Ｘ ２
（Ｆｅ Ｃｏ ） Ｂの飽和磁束密度をキュリ
１−ｙ ｙ １４
一温度で規格化した温度Ｔ ／ Ｔ ｃに対して示した
ものであり、斜線で示した部分ＡはＣＯを含まない系の
実質的な使用温度範囲（−３０℃から６０℃とする）を
示し２部分ＢはＣｏを含む＜ｙ−０，２０）系に対する
同じ温度範囲を示す。
第２図は正方晶化合物（Ｎ ｄ Ｄ ｙ Ｘ） ２
−ｘ
（Ｆｅ Ｃｏ ） Ｂの飽和磁束密度４ｙｒ■
ｓ−ｙｙ１４
の温度変化及び使用温度範囲を第１図と同様の方法で示
したものである。
第３図は本発明の実施例と比較例を示す。即ち実施例２
．３．４と比較例２１．２２におけるＢ「の温度変化を
示す。
出願人 住友特殊金属株式会社
代理人 弁理士 加藤朝道 （他１乙）図面の浄ｊＦ
（内容に変更なし）
第１図
Ｔ／Ｔｃ
（ププ艷ルｉイぴＡ、リヒ温）５１〕
第２図
Ｔ／Ｔｃ
手続：？１市正書防式）
昭和６０年１１月２２日Figure 1 shows the saturation magnetic flux density of the tetragonal compound (NdHo)l-Xx2(FeCo)B versus temperature T/Tc normalized by Curie 1-yy14 temperature. , the shaded part A shows the practical operating temperature range (from -30°C to 60°C) for the system without CO, and the 2nd part B shows the same temperature range for the <y-0,20) system containing Co. Indicates a range. Figure 2 shows a tetragonal compound (N d D y X) 2
-x (Fe Co ) B saturation magnetic flux density 4yr■
The temperature change and operating temperature range of s-yy14 are shown in the same manner as in FIG. 1. FIG. 3 shows an example of the present invention and a comparative example. That is, Example 2
．． 3.4 and B in Comparative Example 21.22. Applicant Sumitomo Special Metals Co., Ltd. Agent Patent Attorney Asamichi Kato (and 1 other B) Drawing cleaning
(No change in content) Figure 1 T/Tc (Pupu 艷Rui Iipia, Rihi On) 51] Figure 2 T/Tc Procedure:? 1 City Seishobo Ceremony) November 22, 1985
Claims (2)
としたとき原子比でＲ＿２／Ｒ＿１≦２．３を満足し原
子百分比でＲ１２．０〜４０％、Ｂ４〜２０％、Ｃｏ１
８％以下及び残部Ｆｅ及び不可避の不純物から成る磁気
異方性焼結永久磁石（但し、Ｒ＿１はＤｙ、Ｔｂ、Ｈｏ
の内一種以上でＲの３０％以上８０％以下、Ｒ＿２はＮ
ｄとＰｒの合計が８０％以上で、残りはＲ＿１以外のＹ
を包含する希土類元素の少なくとも一種）。(1) The sum of R_1 below and R_2 below is R (rare earth element)
When the atomic ratio satisfies R_2/R_1≦2.3, the atomic percentage is R12.0-40%, B4-20%, Co1
Magnetic anisotropic sintered permanent magnet consisting of 8% or less and the balance Fe and unavoidable impurities (however, R_1 is Dy, Tb, Ho
One or more of the following, 30% or more and 80% or less of R, R_2 is N
The sum of d and Pr is 80% or more, and the rest is Y other than R_1
at least one rare earth element including
としたとき原子比でＲ＿２／Ｒ＿１≦２．３を満足し原
子百分比でＲ１２．０〜４０％、Ｂ４〜２０％、Ｃｏ１
８％以下、下記の所定％以下の添加元素Ｍの一種以上（
但し、Ｍとして二種以上の前記添加元素を含む場合は、
Ｍ含量は当該の添加元素のうち最大値を有するものの原
子百分比以下）、及び残部Ｆｅ及び不可避の不純物から
成る磁気異方性焼結永久磁石：（但し、Ｒ＿１はＤｙ、
Ｔｂ、Ｈｏ、の内一種以上でＲの３０％以上８０％以下
、Ｒ＿２はＮｄとＰｒの合計が８０％以上で、残りがＲ
＿１以外のＹを包含する希土類元素の少なくとも一種で
あり、添加元素Ｍは下記の通り： Ｔｉ３％、Ｚｒ３．３％、 Ｈｆ３．３％、Ｃｒ４．５％、 Ｍｎ５％、Ｎｉ６％、 Ｔａ７％、Ｇｅ３．５％、 Ｓｎ１．５％、Ｓｂ１％、 Ｂｉ５％、Ｍｏ５．２％、 Ｎｂ９％、Ａｌ５％、 Ｖ５．５％、Ｗ５％、 Ｓｉ５．０％、Ｚｎ０．５％ ）。(2) The sum of R_1 below and R_2 below is R (rare earth element)
When the atomic ratio satisfies R_2/R_1≦2.3, the atomic percentage is R12.0-40%, B4-20%, Co1
8% or less, one or more of the following specified percentages of additive elements M (
However, if M contains two or more of the above additive elements,
A magnetically anisotropic sintered permanent magnet consisting of M content (the atomic percentage of which has the maximum value among the added elements), and the remainder being Fe and unavoidable impurities: (However, R_1 is Dy,
One or more of Tb, Ho, 30% to 80% of R, R_2 is 80% or more of Nd and Pr in total, and the rest is R.
At least one kind of rare earth element including Y other than _1, and the additive elements M are as follows: Ti3%, Zr3.3%, Hf3.3%, Cr4.5%, Mn5%, Ni6%, Ta7%, Ge3.5%, Sn1.5%, Sb1%, Bi5%, Mo5.2%, Nb9%, Al5%, V5.5%, W5%, Si5.0%, Zn0.5%).
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60166314A JPS6227548A (en) | 1985-07-27 | 1985-07-27 | Permanent magnet alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60166314A JPS6227548A (en) | 1985-07-27 | 1985-07-27 | Permanent magnet alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS6227548A true JPS6227548A (en) | 1987-02-05 |
| JPH0570700B2 JPH0570700B2 (en) | 1993-10-05 |
Family
ID=15829049
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP60166314A Granted JPS6227548A (en) | 1985-07-27 | 1985-07-27 | Permanent magnet alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6227548A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0395625A2 (en) * | 1989-04-28 | 1990-10-31 | BÖHLER YBBSTALWERKE Ges.m.b.H. | Process of Manufacturing a Permanent Magnet or Permanent Magnet Material |
| EP0425469A2 (en) * | 1989-10-25 | 1991-05-02 | BÖHLER YBBSTALWERKE Ges.m.b.H. | Permanent magnet (material) and production process |
| US20110062372A1 (en) * | 2009-09-15 | 2011-03-17 | Qing Gong | Rare earth magnetic materials and methods thereof |
-
1985
- 1985-07-27 JP JP60166314A patent/JPS6227548A/en active Granted
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0395625A2 (en) * | 1989-04-28 | 1990-10-31 | BÖHLER YBBSTALWERKE Ges.m.b.H. | Process of Manufacturing a Permanent Magnet or Permanent Magnet Material |
| EP0425469A2 (en) * | 1989-10-25 | 1991-05-02 | BÖHLER YBBSTALWERKE Ges.m.b.H. | Permanent magnet (material) and production process |
| US20110062372A1 (en) * | 2009-09-15 | 2011-03-17 | Qing Gong | Rare earth magnetic materials and methods thereof |
| EP2478528A1 (en) * | 2009-09-15 | 2012-07-25 | BYD Company Limited | Rare earth permanent magnetic material and preparation method thereof |
| JP2013504881A (en) * | 2009-09-15 | 2013-02-07 | ビーワイディー カンパニー リミテッド | Rare earth permanent magnetic material and preparation method thereof |
| EP2478528A4 (en) * | 2009-09-15 | 2013-06-26 | Byd Co Ltd | Rare earth permanent magnetic material and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0570700B2 (en) | 1993-10-05 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US7618497B2 (en) | R-T-B based rare earth permanent magnet and method for production thereof | |
| JP2751109B2 (en) | Sintered permanent magnet with good thermal stability | |
| WO2013191276A1 (en) | Sintered magnet | |
| US10083783B2 (en) | Rare earth based magnet | |
| JP2001189206A (en) | Permanent magnet | |
| JP2015119130A (en) | Rare earth magnet | |
| JP2000114017A (en) | Permanent magnet and material thereof | |
| JP5999080B2 (en) | Rare earth magnets | |
| JPH0316761B2 (en) | ||
| JP2015119131A (en) | Rare earth magnet | |
| JP2009010305A (en) | Method for manufacturing rare-earth magnet | |
| JPS61221353A (en) | Material for permanent magnet | |
| JP3296507B2 (en) | Rare earth permanent magnet | |
| JPS6223959A (en) | High-efficiency permanent magnet material | |
| JPS6227548A (en) | Permanent magnet alloy | |
| JP6255977B2 (en) | Rare earth magnets | |
| JPS6247455A (en) | Permanent magnet material having high performance | |
| JPS59163803A (en) | Permanent magnet | |
| JPS62170455A (en) | Permanent magnet alloy | |
| JPH05267027A (en) | Manufacture of raw material powder for r-fe-b group permanent magnet and alloy powder for adjusting raw material powder | |
| JP2983902B2 (en) | Ultra low temperature permanent magnet material | |
| JPH0536494B2 (en) | ||
| JPH02259038A (en) | Rare earth magnetic alloy | |
| JP2514155B2 (en) | Method for manufacturing permanent magnet alloy | |
| JPH089756B2 (en) | Permanent magnet material |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| S533 | Written request for registration of change of name |
Free format text: JAPANESE INTERMEDIATE CODE: R313533 |
|
| R350 | Written notification of registration of transfer |
Free format text: JAPANESE INTERMEDIATE CODE: R350 |
|
| EXPY | Cancellation because of completion of term |