JPH04152503A - Rare earth permanent magnet - Google Patents
Rare earth permanent magnetInfo
- Publication number
- JPH04152503A JPH04152503A JP2277065A JP27706590A JPH04152503A JP H04152503 A JPH04152503 A JP H04152503A JP 2277065 A JP2277065 A JP 2277065A JP 27706590 A JP27706590 A JP 27706590A JP H04152503 A JPH04152503 A JP H04152503A
- Authority
- JP
- Japan
- Prior art keywords
- rare earth
- earth elements
- heat treatment
- permanent magnet
- 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.)
- Pending
Links
- 229910052761 rare earth metal Inorganic materials 0.000 title claims abstract description 28
- 150000002910 rare earth metals Chemical class 0.000 title claims abstract description 7
- 238000010438 heat treatment Methods 0.000 claims abstract description 18
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 15
- 239000000956 alloy Substances 0.000 claims abstract description 15
- 239000000203 mixture Substances 0.000 claims abstract description 13
- 238000000034 method Methods 0.000 claims abstract description 9
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 6
- 229910052733 gallium Inorganic materials 0.000 claims abstract description 4
- 229910052732 germanium Inorganic materials 0.000 claims abstract description 4
- 229910052738 indium Inorganic materials 0.000 claims abstract description 4
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 4
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 4
- 229910052718 tin Inorganic materials 0.000 claims abstract description 4
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 3
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 3
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 3
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 3
- 238000004519 manufacturing process Methods 0.000 claims description 7
- 238000010791 quenching Methods 0.000 claims description 7
- 238000001816 cooling Methods 0.000 claims 1
- 239000000463 material Substances 0.000 abstract description 3
- 229910052782 aluminium Inorganic materials 0.000 abstract description 2
- 229910052710 silicon Inorganic materials 0.000 abstract description 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 13
- 150000001875 compounds Chemical class 0.000 description 8
- 230000007423 decrease Effects 0.000 description 6
- 239000006247 magnetic powder Substances 0.000 description 5
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 4
- 239000007788 liquid Substances 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- 230000000171 quenching effect Effects 0.000 description 4
- 229910017112 Fe—C Inorganic materials 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 230000004907 flux Effects 0.000 description 3
- 229910052742 iron Inorganic materials 0.000 description 3
- 230000005415 magnetization Effects 0.000 description 3
- 229910052777 Praseodymium Inorganic materials 0.000 description 2
- 239000000654 additive Substances 0.000 description 2
- 230000000996 additive effect Effects 0.000 description 2
- 229910052786 argon Inorganic materials 0.000 description 2
- 239000011230 binding agent Substances 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- QIVUCLWGARAQIO-OLIXTKCUSA-N (3s)-n-[(3s,5s,6r)-6-methyl-2-oxo-1-(2,2,2-trifluoroethyl)-5-(2,3,6-trifluorophenyl)piperidin-3-yl]-2-oxospiro[1h-pyrrolo[2,3-b]pyridine-3,6'-5,7-dihydrocyclopenta[b]pyridine]-3'-carboxamide Chemical compound C1([C@H]2[C@H](N(C(=O)[C@@H](NC(=O)C=3C=C4C[C@]5(CC4=NC=3)C3=CC=CN=C3NC5=O)C2)CC(F)(F)F)C)=C(F)C=CC(F)=C1F QIVUCLWGARAQIO-OLIXTKCUSA-N 0.000 description 1
- 229910001339 C alloy Inorganic materials 0.000 description 1
- 229910052684 Cerium Inorganic materials 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910052692 Dysprosium Inorganic materials 0.000 description 1
- 229910052693 Europium Inorganic materials 0.000 description 1
- 229910052688 Gadolinium Inorganic materials 0.000 description 1
- 229910052689 Holmium Inorganic materials 0.000 description 1
- 229910052779 Neodymium Inorganic materials 0.000 description 1
- 229910052772 Samarium Inorganic materials 0.000 description 1
- 229910052771 Terbium Inorganic materials 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- 239000013590 bulk material Substances 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000007731 hot pressing Methods 0.000 description 1
- 230000007774 longterm Effects 0.000 description 1
- 238000010298 pulverizing process Methods 0.000 description 1
- 239000010453 quartz Substances 0.000 description 1
- 229910002059 quaternary alloy Inorganic materials 0.000 description 1
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N silicon dioxide Inorganic materials O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 1
- 229910052727 yttrium Inorganic materials 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
- H01F1/058—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IVa elements, e.g. Gd2Fe14C
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、希土類−鉄系永久磁石およびその製造方法に
関するものであり、とくに従来の技術では困難であった
高保磁力、高エネルギー積を実現するものである。[Detailed Description of the Invention] [Industrial Application Field] The present invention relates to a rare earth-iron permanent magnet and a method for manufacturing the same, and in particular realizes high coercive force and high energy product, which have been difficult with conventional techniques. It is something to do.
［従来の技術］
この種の既知の材料は、正方品構造を有するＲ２Ｆｅ１
４Ｂ （ただしＲは希土類元素を示す。）である。Ｂを
Ｃで置き換えたＲ２Ｆｅ１４Ｇはキュリー温度はＲ２Ｆ
ｅ１４Ｂよりもやや低いが異方性磁界は大きく、新しい
永久磁石材料の候補として注目されている（例えば、Ｒ
，Ｇｒｏｓｓｉｎｇｅｒ他：Ｊ、Ｍａｇｎ、Ｍａｇｎ、
Ｍａｔ、８３．１９９０．１３０〜１３２頁及び特開平
１−７３０５１号公報）。[Prior Art] A known material of this kind is R2Fe1 with a square structure.
4B (R represents a rare earth element). R2Fe14G in which B is replaced with C has a Curie temperature of R2F
Although the anisotropy field is slightly lower than that of e14B, it has a large anisotropic magnetic field and is attracting attention as a candidate for a new permanent magnet material (for example, R
, Grossinger et al.: J. Magn.
Mat, 83.1990. pages 130-132 and JP-A-1-73051).
例えば、Ｓｔａｄｅ１ｍａｉｅｒ他はバルクの［）ｙ−
Ｆｅ−Ｃ合金において、鋳造後、熱処理をすることによ
って１Ｈｃ＝１２．５ｋｏｅの保磁力を得たことを報告
している。 （Ｈ，Ｈ，Ｓ ｔ ａ ｄ ｅ１ｍａｉｅ
ｒ他： Ｍａｔ、Ｌｅｔｔｅｒｓ ４．１９８６．３
７７〜３８０頁）。For example, Stadelmaier et al.
It has been reported that a coercive force of 1Hc=12.5koe was obtained by heat-treating an Fe-C alloy after casting. (H,H,Stad e1maie
r et al.: Mat, Letters 4.1986.3
77-380).
ところがＲが重希土類元素の場合には、Ｆｅのモーメン
トとＲのモーメントが反平行に結合するため軽希土類元
素の場合とくらべて飽和磁化が小さくなってしまう。し
たがって、Ｒは軽希土類元素を主成分にすることが望ま
しい。しかしＲが軽希土類元素の場合、Ｒ２Ｆｅ１４Ｃ
化合物が生成しにくいので、高保磁力を容易に得ること
ができない、Ｂｕｓｃｈｏｗ他は、Ｒ２Ｆｅ１４Ｇを生
成させるための熱処理条件を報告している（Ｋ、 Ｈ。However, when R is a heavy rare earth element, the moment of Fe and the moment of R are coupled in an antiparallel manner, so that the saturation magnetization becomes smaller than when R is a light rare earth element. Therefore, it is desirable that R contains a light rare earth element as a main component. However, when R is a light rare earth element, R2Fe14C
Buschow et al. reported heat treatment conditions for producing R2Fe14G (K, H.
Ｂｕｓｃｈｏｗ他： Ｊ、Ｌｅｓ ｓ−ＣｏｍｍｏｎＭ
ｅｔ、１４２．１９８８．３４９〜３５７頁及び特開平
２−４９４０号公報）。Buschow et al.: J, Les s-Common M
et, 142.1988. pp. 349-357 and JP-A-2-4940).
更に、Ｂｕｓｃｈｏｗ他は、Ｒ２Ｆｅ１４ＣのＦｅの一
部をＭｎで置換することにより、Ｒ２（Ｆｅ、Ｍｎ）１
４Ｃ化合物を安定化できることを示した（例えばに、Ｈ
，Ｊ、Ｂ、ｕｓｃｈｏｗ他：Ｊ。Furthermore, Buschow et al. replaced a part of Fe in R2Fe14C with Mn to form R2(Fe,Mn)1
It was shown that 4C compounds can be stabilized (for example, H
, J., B., uschow et al.: J.
ｄｅ、Ｐｈｙｓ、４９．１９８８、Ｃ８−５９３〜５９
４頁、特開平２−８３４５号公報）。de, Phys, 49.1988, C8-593-59
4 pages, JP-A-2-8345).
［＠明が解決しようにする課題］
しかし、前記の熱処理条件を規定した発明では、約８３
０℃以下の温度ではＲ２Ｆｅ１４Ｃが生成する反応速度
はたいへん遅く、また、希土類元素の種類によって決ま
るある温度（例えばＲがＮｄの場合は８９０℃）以上で
は、Ｒ２Ｆｅ１４Ｇが分解してしまうので、Ｒ２Ｆｅ１
４Ｇが生成する温度範囲はたいへん狭い。その上に、長
時間の熱処理（例えばＲがＮｄの場合は５００時間）を
必要にするので、実用上問題が大きい。また、長時間の
熱処理は粒成長をまねき、高保磁力化を図るさまたげに
なる。[Problem that @Ming is trying to solve] However, in the invention that specifies the heat treatment conditions mentioned above, about 83
At temperatures below 0°C, the reaction rate for producing R2Fe14C is very slow, and at temperatures above a certain temperature determined by the type of rare earth element (e.g. 890°C when R is Nd), R2Fe14G decomposes.
4G produces a very narrow temperature range. Moreover, it requires a long heat treatment (for example, 500 hours when R is Nd), which is a big problem in practice. In addition, long-term heat treatment causes grain growth, which hinders efforts to increase coercive force.
またＲＦｅＣ：系にＭｎを添加する発明では、Ｍｎの導
入によってＲ２（Ｆｅ、Ｍｎ）１４Ｇを安定に生成させ
ることができても、保磁力の発生に必要な金属組織が実
現されないため、高保磁力を得ることができないと同時
にＭｎのモーメントはＦｅのモーメントと反強磁性的に
結合し、磁化が減少してしまうので、多量のＭｎを添加
することは望ましくない。Furthermore, in the invention of adding Mn to the RFeC: system, even if it is possible to stably generate R2(Fe, Mn)14G by introducing Mn, the metal structure necessary for generating coercive force cannot be achieved, resulting in a high coercive force. It is not desirable to add a large amount of Mn because the moment of Mn is antiferromagnetically coupled with the moment of Fe and the magnetization decreases.
従って本発明の目的は、このような欠点を解消し、Ｒ２
Ｆｅ１４Ｃ系合金のバルク材において高エネルギー積を
得ることを可能にしたものである。Therefore, an object of the present invention is to eliminate such drawbacks and to improve R2
This makes it possible to obtain a high energy product in the bulk material of Fe14C alloy.
具体的には本発明は、液体急冷法を用いて非晶質Ｒ−Ｆ
ｅ−Ｍ−Ｃ系合金薄帯を作成し、これに適切な熱処理を
施すことにより、大きな飽和磁化を有するＲ２ （Ｆｅ
、Ｍ）１４Ｃ化合物を短時間のうちに生成させると同時
に、保磁ノＪを発生するような金属組織を実現し、Ｒ２
Ｆｅ１４Ｃ系合金による高エネルギー積永久磁石を実現
する方法を提供することである。Specifically, the present invention uses a liquid quenching method to produce amorphous R-F.
By creating an e-M-C alloy ribbon and subjecting it to appropriate heat treatment, R2 (Fe
, M) 14C compound is generated in a short time, and at the same time, a metal structure that generates coercive J is realized, and R2
The object of the present invention is to provide a method for realizing a high-energy product permanent magnet using an Fe14C alloy.
［課題を解決するための手段］
本発明は、組成式： （Ｒ’ １００−ａ Ｒａ ）
ｘＦ ｅ ＋。。−ｘ−ｙ−ｚＭｙＣｚ
（ただし、
Ｒは軽希土類元素の１種または２種以
上、Ｒ′は重希土類元素の１種または２種以上、ＭはＡ
Ｉ＋ Ｓ ｘ＋ Ｐ＋ Ｃ： ｒｌ ｖ、 Ｔ １１
Ｍｎ、 Ｇａ、Ｇｅ、Ｉｎ、Ｓｎ、Ｎｉ、Ｎの少なく
とも１種以上であり、原子百分率で
Ｘは１０〜１５％
ｙは １〜１２％
２は ４〜１０％
ａは ５０％以上
で表されることを特徴にする希土類永久磁石である。[Means for Solving the Problems] The present invention has the following compositional formula: (R' 100-a Ra )
xF e +. . -x-y-zMyCz (However, R is one or more light rare earth elements, R' is one or more heavy rare earth elements, M is A
I+ S x+ P+ C: rl v, T 11
At least one of Mn, Ga, Ge, In, Sn, Ni, and N, represented by an atomic percentage of X of 10 to 15%, y of 1 to 12%, 2 of 4 to 10%, and a of 50% or more. It is a rare earth permanent magnet characterized by
本発明はまた、前記組成の合金溶湯な超急冷法によって
薄帯とし、前記薄帯を熱処理することを特徴にする希土
類永久磁石の製造方法である。熱処理は７００〜９００
℃で行うことが好ましい。The present invention also provides a method for producing a rare earth permanent magnet, which comprises forming a molten alloy having the composition into a thin ribbon by an ultra-quenching method, and heat-treating the thin ribbon. Heat treatment is 700-900
Preferably, the reaction is carried out at ℃.
以下これについて詳しく説明する。本発明の永久磁石は
（Ｒ，Ｒ’ ） −Ｆ ｅ−Ｍ−Ｃの４元系合金であっ
て、ＲはＣｅ、Ｐｒ、Ｎｄ、Ｓｍ、Ｅｕからなる軽希土
類元素の中から選んだ少なくとも１種または２種以上の
組み合わせ、Ｒ′はＧｄ、Ｔｂ、Ｄｙ、Ｈｏ、Ｅｒ、Ｔ
ｍ、Ｌｕからなる重希土類元素の１種または２種以上の
組み合わせである。、ＭはＡｌ、Ｓｉ、Ｐ、Ｃｒ、Ｖ、
Ｔｉ、Ｍｎ、Ｇａ、Ｇｅ、Ｉｎ、Ｓｎ、Ｎｉ、Ｎの各々
１種以上であり、Ｒ２（Ｆｅ、Ｍ）１４Ｃ化合物を含ん
だものである。This will be explained in detail below. The permanent magnet of the present invention is a quaternary alloy of (R,R')-Fe-MC, where R is at least one selected from light rare earth elements consisting of Ce, Pr, Nd, Sm, and Eu. One type or a combination of two or more types, R' is Gd, Tb, Dy, Ho, Er, T
It is one kind or a combination of two or more kinds of heavy rare earth elements consisting of m and Lu. , M is Al, Si, P, Cr, V,
It is one or more of each of Ti, Mn, Ga, Ge, In, Sn, Ni, and N, and contains an R2(Fe, M)14C compound.
また、上記一般式において、軽希土類元素ＲはｌＯから
１５原子％の範囲とした。Ｒの量が少なすぎると残留磁
束密度（Ｂｒ）は向上するものの、保磁力が極端に減少
するため最大エネルギー積（（ＢＨ）ｗａｘ）は減少す
る。したがってＲ量は１０原子％以上とした。Ｒの量が
多すぎると、残留磁束密度（Ｂｒ）が減少し、この場合
も最大エネルギー積（（ＢＨ） ｍａｘ）が減少するの
で、Ｒ量は１５原子％以下とした。また重希土類元素の
量が保磁力が大きくなるが、磁化が減少するので軽希土
類元素の量を越えないことが望ましい。よってａは５０
％以上とした。Furthermore, in the above general formula, the light rare earth element R is in the range of 10 to 15 at %. If the amount of R is too small, the residual magnetic flux density (Br) will improve, but the coercive force will be extremely reduced, so the maximum energy product ((BH)wax) will decrease. Therefore, the amount of R was set to 10 atomic % or more. If the amount of R is too large, the residual magnetic flux density (Br) will decrease and the maximum energy product ((BH) max) will also decrease in this case, so the amount of R was set to 15 atomic % or less. Further, although the amount of heavy rare earth elements increases the coercive force, it decreases magnetization, so it is desirable that the amount of heavy rare earth elements does not exceed the amount of light rare earth elements. Therefore a is 50
% or more.
元素ＭはＲ２（Ｆｅ、Ｍ）１４Ｃ化合物を安定に生成す
る作用があり、重希土類元素と添加元素Ｍを同時に添加
することによって（Ｒ，Ｒ量 ）２（Ｆｅ、Ｍ）１４Ｃ
：化合物の安定生成がより促進される。しかし、Ｍの量
が少なすぎたり多すぎたりすると、 （Ｒ，Ｒ量 ）
２ （Ｆ ｅ、 Ｍ） １４Ｃ：化合物が安定に生成せ
ず、このため高保磁力が得られない、よってＭ量は１〜
１２原子％でなければならない。Element M has the effect of stably generating R2(Fe,M)14C compounds, and by adding heavy rare earth elements and additive element M at the same time (R, R amount)2(Fe,M)14C
: Stable production of the compound is further promoted. However, if the amount of M is too small or too large, (R, R amount)
2 (Fe, M) 14C: The compound does not form stably, and therefore a high coercive force cannot be obtained. Therefore, the amount of M is 1 to 1.
Must be 12 atomic percent.
また、Ｃ量が多すぎると、残留磁束密度（Ｂｒ）、およ
び保磁力が減少し大きな最大エネルギー積（（Ｂ Ｈ）
ｗａｘ）が得られない。Ｃ量が少なすぎるとＲ２（Ｆ
ｅ、Ｍ）１４Ｃ化合物が生成しないので、高保磁力が得
られない。したがってＣ量を４〜１０原子％とした。In addition, if the amount of C is too large, the residual magnetic flux density (Br) and coercive force decrease, resulting in a large maximum energy product ((B H)
wax) cannot be obtained. If the amount of C is too small, R2(F
e, M) Since no 14C compound is generated, high coercive force cannot be obtained. Therefore, the amount of C was set to 4 to 10 at%.
なお、この発明では特性を維持しながら、キュリー温度
の上昇と耐食性を改善するのに、Ｃ０１Ｎｉの各々１種
以上をＦｅに対して５０％まで置換することができる。In the present invention, one or more of each of C01Ni can be substituted up to 50% of Fe in order to improve the Curie temperature increase and corrosion resistance while maintaining the characteristics.
本発明の磁石の形態としては合金薄帯を粉砕して磁粉を
得た後、有機バインダー等で固めたいわゆるボンド磁石
、あるいは、前記磁粉をホットプレスで固めた圧密磁石
、更に温間で組成加工した温間加工磁石、あるいはそれ
を再粉砕して磁粉とした後にバインダで固めた磁気異方
性ボンド磁石にすることができる。なお、本発明で合金
薄帯とは、超急冷法で得られた連続帯状のものに限られ
るものではなくフレーク状のものも含むものである。あ
るいは、例えばアトマイズ法によって直接に磁粉を得る
ことも本発明の範囲を逸脱するもので１１ない。The form of the magnet of the present invention is a so-called bonded magnet in which magnetic powder is obtained by crushing an alloy ribbon and then hardened with an organic binder, etc., or a consolidated magnet in which the magnetic powder is hardened by hot pressing, and further processed into a composition by warm processing. It can be made into a warm-processed magnet, or a magnetically anisotropic bonded magnet made by re-pulverizing it into magnetic powder and solidifying it with a binder. In the present invention, the alloy ribbon is not limited to a continuous ribbon obtained by an ultra-quenching method, but also includes a flake. Alternatively, it is not beyond the scope of the present invention to obtain magnetic powder directly, for example, by an atomization method.
また、得られた微細結晶粒を有する磁粉を低温度で粒成
長しないように工夫すれば焼結磁石を得ることもできる
。Furthermore, if the obtained magnetic powder having fine crystal grains is devised to prevent grain growth at a low temperature, a sintered magnet can be obtained.
以下、実施例によって本発明を具体的に説明する。Hereinafter, the present invention will be specifically explained with reference to Examples.
［実施例］
（実施例−１）
合金組成はＤ ｙ４．７Ｐ ｒ７．Ｉ Ｆ ｅ８２．３
Ｇ５．９ （原子百分率）である。純度９９．９％のＤ
ｙ、Ｐｒ、ＦｅおよびＦｅ５Ｇを用いて、上記組成のイ
ンゴットをアーク溶解で作成した。このインゴットをア
ルゴンガス雰囲気中で高周波溶解したのち、０．５ｋｇ
／ｃｍ２のアルゴンガスを溶湯に加圧して内径０．５ｍ
ｍの石英ノズルから、約４２ｍ／Ｓの周速で回転する直
径１６０ｍｍの銅製の回転ロール上に噴射し、急速に冷
却凝固させて薄帯を作成した。このようにして得た薄帯
を熱処理し、振動試料型磁力針を用いて、最大磁場１８
ｋＯｅの範囲で磁気特性を測定した。これらの試料の保
磁力と熱処理温度との関係を調べたところ、第１図に示
すように、７００℃以上の温度でで熱処理したときに、
最も高い保磁カフｋＯｅを示すことがわかった。熱処理
時間を１時間から３０時間まで延長した場合にも、保磁
力の変化は認められなかった。また、Ｄｙを添加してい
ないＰｒ１１．８Ｆｅ８２．３Ｇ５．９合金の場合の保
磁力の変化を同図に示したが、保磁力は小さくＤｙの添
加が保磁力の発生に効果があることがわかる。一方、は
じめに作成したインゴットから切り出した試料を７００
℃で熱処理したが、その保磁力は約２０００ｅで小さか
った。このことから、本発明はＲ−Ｆ ｅ−Ｃ系合金の
高保磁力化を実現できる方法であるこ之が確認できた。[Example] (Example-1) The alloy composition was Dy4.7P r7. I F e82.3
G5.9 (atomic percentage). D with 99.9% purity
An ingot having the above composition was prepared by arc melting using Y, Pr, Fe, and Fe5G. After high frequency melting of this ingot in an argon gas atmosphere, 0.5 kg
/cm2 of argon gas was pressurized to the molten metal to create an inner diameter of 0.5m.
The mixture was injected from a quartz nozzle of 300 mm onto a copper rotating roll with a diameter of 160 mm rotating at a circumferential speed of about 42 m/s, and rapidly cooled and solidified to create a ribbon. The ribbon obtained in this way was heat-treated, and a maximum magnetic field of 18
Magnetic properties were measured in the kOe range. When we investigated the relationship between coercive force and heat treatment temperature for these samples, we found that when heat treated at a temperature of 700°C or higher, as shown in Figure 1,
It was found that it exhibited the highest coercive cuff kOe. Even when the heat treatment time was extended from 1 hour to 30 hours, no change in coercive force was observed. The figure also shows the change in coercive force in the case of the Pr11.8Fe82.3G5.9 alloy to which Dy is not added, and it can be seen that the coercive force is small and the addition of Dy is effective in generating coercive force. . On the other hand, the sample cut from the ingot prepared at the beginning was
Although it was heat-treated at ℃, its coercive force was small at about 2000e. From this, it was confirmed that the present invention is a method that can realize a high coercive force of an R-Fe-C alloy.
（実施例−２）
合金組成はＧｄ４．７Ｎｄ７．ｌＦｅ７６．４Ａ１５．
９Ｇ、９（原子百分率）であり、製造方法は（実施例−
１）と同じである。この試料は、第２図に示すＪうに、
９００℃の熱処理で最も高い保磁力８ｋＣｅを示す。ま
た、インゴットから切り出した試りは、９００℃の熱処
理を行っても、２０００ｅｆｉ度であり、本発明の有効
性を確認できた。(Example-2) The alloy composition is Gd4.7Nd7. lFe76.4A15.
9G, 9 (atomic percentage), and the manufacturing method is (Example-
Same as 1). This sample is as shown in Figure 2.
It shows the highest coercive force of 8 kCe after heat treatment at 900°C. In addition, even when the sample cut out from the ingot was subjected to heat treatment at 900° C., the efi was 2000 degrees, confirming the effectiveness of the present invention.
（実施例−３）
合金組成はＤｙ４．７Ｐ ｒ７．ｌＦｅ６６、ｌ’ｌ；
ｏｌｏ、Ｏｓｉ ２．９Ｍ ｎ３．ＯＧ５．９ （原子
百分率）であり、製造方法は（実施例−１）と同じであ
る。この試料は、第３図に示すように、９００℃の熱処
理で最も高い保磁力６ｋＯｅを示す。また、インゴット
から切り出した試料は、９００℃の熱処理を行っても、
２０００ｅ程度であり、本発明の有効性を確認できた。(Example-3) The alloy composition was Dy4.7P r7. lFe66, l'l;
olo, Osi 2.9M n3. OG5.9 (atomic percentage), and the manufacturing method is the same as (Example-1). As shown in FIG. 3, this sample exhibits the highest coercive force of 6 kOe after heat treatment at 900°C. In addition, even if the sample cut from the ingot was heat-treated at 900°C,
It was approximately 2000e, confirming the effectiveness of the present invention.
実施例１〜３の結果から、熱処理温度は７００〜９００
℃が適当である。From the results of Examples 1 to 3, the heat treatment temperature was 700 to 900.
°C is appropriate.
（実施例−４）
実施例−１と同様にして第１表に示す種々の添加元素Ｍ
についても本発明の効果を確認した。(Example-4) Various additive elements M shown in Table 1 were added in the same manner as in Example-1.
The effects of the present invention were also confirmed for these cases.
［発明の効果〕
本発明によれば、Ｒ−Ｆｅ−Ｃ系に元素Ｍを所定量加え
、液体急冷法で非晶質薄帯を作成し、これを適切な温度
で熱処理することにより、Ｒ２（Ｆｅ、Ｍ）１００化合
物を安定に生成させると同時に保磁力の発生に適した金
属組織を実現することができ、高い保磁力ひいては大き
な最大エネルギー積（（Ｂ Ｈ） ｗａｘ）を有する永
久磁石が得られる。[Effects of the Invention] According to the present invention, by adding a predetermined amount of element M to the R-Fe-C system, creating an amorphous ribbon using a liquid quenching method, and heat-treating this at an appropriate temperature, R2 It is possible to stably generate a (Fe, M)100 compound and at the same time realize a metal structure suitable for generating coercive force, and a permanent magnet with a high coercive force and a large maximum energy product ((B H) wax) can be created. can get.
第１図〜第３図は本発明に係る希土類磁石の熱処理温度
と保磁力の関係を示す図である。
第
図
液体急冷後
熱処理温度
（Ｃ）
第
図
液体急玲後
熱処理温度（°Ｃ）
第
図1 to 3 are diagrams showing the relationship between heat treatment temperature and coercive force of rare earth magnets according to the present invention. Fig. Heat treatment temperature after liquid quenching (C) Fig. Heat treatment temperature after liquid quenching (°C) Fig.
Claims (3)
ｘＦｅ＿１＿０＿０＿−＿ｘ＿−＿ｙ＿−＿ｚＭ＿ｙＣ
＿ｚ（ただし、Ｒは軽希土類元素の１種または２種以上
、Ｒ’は重希土類元素の１種または２種以上、ＭはＡｌ
、Ｓｉ、Ｐ、Ｃｒ、Ｖ、Ｔｉ、Ｍｎ、Ｇａ、Ｇｅ、Ｉｎ
、Ｓｎ、Ｎｉ、Ｎの少なくとも１種以上であり、原子百
分率で ｘは１０〜１５％ ｙは１〜１２％ ｚは４〜１０％ ａは５０％以上 で表されることを特徴にする希土類永久磁石。(1) Composition formula: (R'_1_0_0_-_aR_a)_
xFe_1_0_0_-_x_-_y_-_zM_yC
__z (However, R is one or more types of light rare earth elements, R' is one or more types of heavy rare earth elements, M is Al
, Si, P, Cr, V, Ti, Mn, Ga, Ge, In
, Sn, Ni, and N, and is characterized in that x is 10 to 15%, y is 1 to 12%, z is 4 to 10%, and a is 50% or more in atomic percentage. permanent magnet.
って薄帯とし、前記薄帯を熱処理することを特徴にする
希土類永久磁石の製造方法。(2) A method for producing a rare earth permanent magnet, which comprises forming a molten alloy having the composition according to claim 1 into a ribbon by an ultra-quench cooling method, and heat-treating the ribbon.
る請求項２に記載の希土類磁石の製造方法。(3) The method for manufacturing a rare earth magnet according to claim 2, wherein the heat treatment is performed at a temperature of 700 to 900°C.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2277065A JPH04152503A (en) | 1990-10-16 | 1990-10-16 | Rare earth permanent magnet |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2277065A JPH04152503A (en) | 1990-10-16 | 1990-10-16 | Rare earth permanent magnet |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH04152503A true JPH04152503A (en) | 1992-05-26 |
Family
ID=17578299
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2277065A Pending JPH04152503A (en) | 1990-10-16 | 1990-10-16 | Rare earth permanent magnet |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH04152503A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6319336B1 (en) | 1998-07-29 | 2001-11-20 | Dowa Mining Co., Ltd. | Permanent magnet alloy having improved heat resistance and process for production thereof |
-
1990
- 1990-10-16 JP JP2277065A patent/JPH04152503A/en active Pending
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6319336B1 (en) | 1998-07-29 | 2001-11-20 | Dowa Mining Co., Ltd. | Permanent magnet alloy having improved heat resistance and process for production thereof |
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