JPH02173236A - Rare earth magnetic alloy - Google Patents
Rare earth magnetic alloyInfo
- Publication number
- JPH02173236A JPH02173236A JP32862188A JP32862188A JPH02173236A JP H02173236 A JPH02173236 A JP H02173236A JP 32862188 A JP32862188 A JP 32862188A JP 32862188 A JP32862188 A JP 32862188A JP H02173236 A JPH02173236 A JP H02173236A
- Authority
- JP
- Japan
- Prior art keywords
- rare earth
- maximum energy
- energy product
- coercive force
- alloy
- 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 40
- 150000002910 rare earth metals Chemical class 0.000 title claims abstract description 39
- 229910001004 magnetic alloy Inorganic materials 0.000 title claims abstract description 9
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 44
- 239000000956 alloy Substances 0.000 claims abstract description 44
- 229910052779 Neodymium Inorganic materials 0.000 claims abstract description 12
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 12
- 229910052772 Samarium Inorganic materials 0.000 claims abstract description 10
- 230000005291 magnetic effect Effects 0.000 abstract description 26
- 229910052719 titanium Inorganic materials 0.000 abstract description 12
- 229910052796 boron Inorganic materials 0.000 abstract description 11
- 229910052802 copper Inorganic materials 0.000 abstract description 5
- 229910052742 iron Inorganic materials 0.000 abstract description 5
- 239000000203 mixture Substances 0.000 abstract description 5
- 229910052726 zirconium Inorganic materials 0.000 abstract description 5
- 229910017985 Cu—Zr Inorganic materials 0.000 abstract description 4
- 230000001105 regulatory effect Effects 0.000 abstract 1
- 239000000047 product Substances 0.000 description 45
- 230000007423 decrease Effects 0.000 description 19
- 230000004907 flux Effects 0.000 description 14
- 230000000694 effects Effects 0.000 description 6
- 150000001875 compounds Chemical class 0.000 description 5
- 238000006467 substitution reaction Methods 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 4
- 230000005347 demagnetization Effects 0.000 description 4
- 238000005245 sintering Methods 0.000 description 4
- 229910052777 Praseodymium Inorganic materials 0.000 description 3
- 210000003850 cellular structure Anatomy 0.000 description 3
- 238000010586 diagram Methods 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 230000008901 benefit Effects 0.000 description 2
- 230000008859 change Effects 0.000 description 2
- 229910000938 samarium–cobalt magnet Inorganic materials 0.000 description 2
- 239000004575 stone Substances 0.000 description 2
- 229910001020 Au alloy Inorganic materials 0.000 description 1
- 229910052684 Cerium Inorganic materials 0.000 description 1
- 229910052692 Dysprosium Inorganic materials 0.000 description 1
- 229910052691 Erbium Inorganic materials 0.000 description 1
- 229910017112 Fe—C Inorganic materials 0.000 description 1
- 229910052689 Holmium Inorganic materials 0.000 description 1
- 229910052765 Lutetium Inorganic materials 0.000 description 1
- 241000270295 Serpentes Species 0.000 description 1
- 229910052771 Terbium Inorganic materials 0.000 description 1
- 229910052775 Thulium Inorganic materials 0.000 description 1
- 229910052769 Ytterbium Inorganic materials 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 239000003353 gold alloy Substances 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 230000005415 magnetization Effects 0.000 description 1
- 230000014759 maintenance of location Effects 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 230000001376 precipitating effect Effects 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- -1 rare earth cobalt compounds Chemical class 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- 229910052727 yttrium Inorganic materials 0.000 description 1
Landscapes
- 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、希土類金属を用いた多元素系の希土類磁石合
金に関する。DETAILED DESCRIPTION OF THE INVENTION [Field of Industrial Application] The present invention relates to a multi-element rare earth magnet alloy using rare earth metals.
従来、Ｓｍ−Ｃｏ−Ｆｅ−Ｃｕ−Ｚｒ系の２−１７型磁
石合金（Ｒｚ ＣｏＩ７を主体とする磁石合金、ここに
Ｒは希土類金属を示す）においては３０ＭＧＯｅ程度の
高い最大エネルギー積（（ＢＨ）ｍａｘ）、１０ＫＯｅ
以上の保磁力（ｉＨＣ）を有する磁石合金が商用磁石と
して実用化されている。Conventionally, Sm-Co-Fe-Cu-Zr type 2-17 type magnet alloy (magnet alloy mainly composed of Rz CoI7, where R represents a rare earth metal) has a high maximum energy product ((BH )max), 10KOe
Magnet alloys having the above coercive force (iHC) have been put into practical use as commercial magnets.
しかし、希土類金属のＳｍは高価であり、資源的にも切
迫しており、調達が難しくなっている。However, the rare earth metal Sm is expensive and in short supply as a resource, making it difficult to procure it.
そこで、安価な磁石合金を得るために、従来Ｓｍの一部
を資源的に豊富なＮｄ、Ｃｅ、Ｐｒで置換した希土類磁
石合金が提案されている。このものは、最大エネルギー
積が２４ＭＧＯｅ程度、保持力ｂＨｃが７．６ＫＯｅ
（ｉＨｃ９ＫＯｅ程度）程度であり（特開昭６２−２４
３７３１号公報）。Therefore, in order to obtain an inexpensive magnet alloy, a rare earth magnet alloy has been proposed in which a part of conventional Sm is replaced with resource-rich Nd, Ce, and Pr. This product has a maximum energy product of about 24 MGOe and a holding force bHc of 7.6 KOe.
(about iHc9KOe) (Unexamined Japanese Patent Publication No. 62-24
Publication No. 3731).
前記Ｓｍ−Ｃｏ−Ｆｅ−Ｃｕ−Ｚｒ合金に比べ最大エネ
ルギー積、保持力ともに低い。Both the maximum energy product and the holding force are lower than the Sm-Co-Fe-Cu-Zr alloy.
また８同様の理由から、Ｓｍの一部をＣｅで置換し、Ｚ
ｒ、Ｂを添付した希土類磁石も提案されている。このも
のは、最大エネルギー積が２４ＭＧＯｅ程度、保磁力ｉ
Ｈｃが１３ＫＯｅ程度である（特開昭６３−２８８４４
号公報）が１未だ生産販売されていない。In addition, for the same reason as 8, part of Sm was replaced with Ce, and Z
Rare earth magnets with r and B attached have also been proposed. This product has a maximum energy product of about 24 MGOe and a coercive force i
Hc is about 13KOe (Japanese Patent Application Laid-Open No. 63-28844
No. 1) has not yet been produced and sold.
そして７ このＳｍ−Ｃｅ系の商用磁石としては最大エ
ネルギー積２２ＭＧＯｅ程度、保持力１ＨＣ９ＫＯｅ程
度のものが実用化されているにすぎず、前記Ｓｍ−Ｃｏ
−Ｆｅ−Ｃｕ−Ｚｒ系合金に比べ、最大エネルギー禎、
保持力ともに低い。これは５焼結特性等の製造上の困難
性のためと予想される。7 This Sm-Ce based commercial magnet has only been put into practical use with a maximum energy product of about 22MGOe and a coercive force of about 1HC9KOe.
- Maximum energy compared to Fe-Cu-Zr alloys,
Both holding power is low. This is expected to be due to manufacturing difficulties such as the 5 sintering characteristics.
しかして、希土類（１！Ｌ石合金においては、保持力が
大きく、シかも最大エネルギー積ができるだけ大きいこ
とが望まれる。Therefore, in rare earth (1!L) alloys, it is desired that the coercive force is large and the maximum energy product is as large as possible.
しかしながら、安価な希土類磁石合金を得ようとすると
、前記後二者の公報に示されるごとく。However, when trying to obtain an inexpensive rare earth magnet alloy, as shown in the latter two publications.
最大エネルギー積がセいぜい２４ ＭＧＯｅ程度。The maximum energy product is about 24 MGOe at most.
保持力（ｉＨｃ）が９ＫＯｅ程度のものしか製造するこ
とができない。It is only possible to manufacture a product with a holding power (iHc) of about 9 KOe.
本発明はかかる従来の間■点に鑑み、安価でかつ保磁力
及び最大エネルギー積に優れた希土類磁石合金を提供し
ようとするものである。In view of these drawbacks, the present invention aims to provide a rare earth magnet alloy that is inexpensive and has excellent coercive force and maximum energy product.
本願の発明は２重量比で、Ｓｍ８〜２０％、Ｎｄ６〜２
０％、Ｆｅ１Ｏ〜２５％、Ｃｕ５〜１０％、Ｚｒｌ〜４
％、Ｍｎ０．ｌ〜１％、Ｔｉ０１−１％、８０．００３
〜０．０１５％、残部Ｃｏからなり、かつＳｍ＋Ｎｄが
２２〜２８％であることを特徴とするに土Ｍ磁石合金に
ある。The invention of the present application has a weight ratio of 2, Sm8-20%, Nd6-2
0%, Fe1O~25%, Cu5~10%, Zrl~4
%, Mn0. l~1%, Ti01-1%, 80.003
~0.015%, the balance being Co, and Sm+Nd is 22 to 28%.
本発明は、Ｓｍの−・部をＮｄで置換するのみでなく、
他の添加物の複合添加、更に従来のＳｍＣｏ−Ｆｅ−Ｃ
ｕ系希土類磁石合金における組成等について鋭意研究を
進めた結果なされたものである。The present invention not only replaces the - part of Sm with Nd, but also
Combined addition of other additives, and even conventional SmCo-Fe-C
This was achieved as a result of intensive research into the composition of U-based rare earth magnet alloys.
即ち、磁石合金における最大エネルギー積の理論的上限
の値は（４πＩｓ）”／４で表される。That is, the theoretical upper limit value of the maximum energy product in a magnetic alloy is expressed as (4πIs)''/4.
（ここに４πＩｓは飽和磁束密度である）、また。(where 4πIs is the saturation magnetic flux density), and.
５ＬｒｎａＬの結果（Ｐｒｏｃ １９７２ ＩＮＴ
巳ＲＭＡＧ Ｃｏｎｒ、Ｋｙｏｔｏ、Ｊａｐａｎ （
１９７２）Ａｐｒ、Ｐ５１１）より（第１図参照）、Ｃ
ｅｚ Ｃｏａｔ化合物はＳ ｍｚ Ｃｏ（を化合物に比
較して飽和磁束密度が低いため、ＳｍをＣｅで置換した
希土類磁石合金は、最大エネルギー積が低下することは
避けられない、（第２図参照）、なお、第１図は各種希
土類コバルト化合物Ｒｚ Ｃ０１ｆｆ、ＲＣｏｓ 、Ｒ
１Ｃｏｔの室温における飽和磁束密度を示している。5LrnaL results (Proc 1972 INT
Snake RMAG Conr, Kyoto, Japan (
1972) April, P511) (see Figure 1), C
Since the ez Coat compound has a lower saturation magnetic flux density than the S mz Co compound, it is inevitable that the maximum energy product of rare earth magnet alloys in which Sm is replaced with Ce will decrease (see Figure 2). In addition, Fig. 1 shows various rare earth cobalt compounds Rz C01ff, RCos, R
It shows the saturation magnetic flux density of 1 Cot at room temperature.
第２図はＳｍｘ Ｃｅ＋−ｘ （Ｃｏ ｏ、ｔｚｓＦ
ｅｏ、ｚ。Figure 2 shows Smx Ce+-x (Co o, tzsF
eo, z.
Ｃｕ ｏ、ｏｓｓ Ｚ ｒ ｏ、ｏｚ） ｖ、ｓの希
土類磁石合金において、Ｘの値を変化させたときの、
Ｂｒ （残留磁束密度）、１Ｈｃ（保磁力）、（ＢＨ）
、、。Cu o, oss Z r o, oz) When the value of X is changed in the rare earth magnet alloy of v, s,
Br (residual magnetic flux density), 1Hc (coercive force), (BH)
,,.
（最大エネルギー積）の変化を示したものである（出典
；日本応用磁気学会誌、ＶｏＬ９．Ｎｏｌ。It shows the change in (maximum energy product) (Source: Journal of the Japan Society of Applied Magnetics, Vol. 9. No.
１９８５）。1985).
一方、ＳｍをＮｄ、Ｐｒに置換した場合、ＮｄｌＣｏ１
？化合物、Ｐｒ、Ｃｏ、、化合物はＳｍ、Ｃｏａｔ化合
物に比較して飽和磁化が高いため（第１図参照）１合金
の飽和磁束密度が上昇し、最大エネルギー積の向上が期
待できる。しかし、＋？；Ｉ記従来技術においては、保
磁力の急激な低下（第３図参照）と減磁曲線の角形性の
低下を招くため、大きい最大エネルギー積を得ることが
できない。上記第３図は、 Ｓｍｔｌ、、ｌｌ、Ｎｄ
ｘ （Ｃｏ ｏ、ｂｑ２Ｃｕ＠、＊Ｉ Ｆ ｅｏ、
ｚｔ Ｚ ｒ ｏ、ｏｚｓ） ｓ、ｉｓの希±１［
石合金について、Ｘ値を変化させたときの保磁力の変化
を示している（日本応用磁気学会誌 Ｖ。On the other hand, when Sm is replaced with Nd or Pr, NdlCo1
? Compounds such as Pr, Co, and Compound have higher saturation magnetization than Sm and Coat compounds (see Figure 1), so the saturation magnetic flux density of the alloy increases, and an improvement in the maximum energy product can be expected. But +? In the prior art described in I, a large maximum energy product cannot be obtained because the coercive force suddenly decreases (see FIG. 3) and the squareness of the demagnetization curve decreases. The above figure 3 shows Smtl, ll, Nd
x (Co o, bq2Cu@, *IF eo,
zt Z r o, ozs) s, is rare ± 1 [
It shows the change in coercive force when the X value is changed for stone alloys (Journal of the Japan Society of Applied Magnetics V.
Ｌｌｌ、Ｎｏ２．１９８７）。Lll, No. 2.1987).
本発明はかかる知見に基づき、Ｓｍの一部をＮｄに置換
したＮｄ置換型希土類磁石合金に着目して研究を進めた
結果、Ｍｎ−Ｔｉ−８の複合添加を行うこと、及び合金
中の各成分、即ちＦｅ、Ｃｕ、Ｚｒ及びＳｍ、Ｎｄを特
定範囲とすることにより２本発明に到達したものである
。Based on this knowledge, the present invention focused on a Nd-substituted rare earth magnet alloy in which a part of Sm was replaced with Nd. The present invention has been achieved by setting the components, namely Fe, Cu, Zr, Sm, and Nd, to specific ranges.
次に、第２発明は、上記第１発明において、更にＳｍ及
びＮｄを除く希土類金属Ｒ（Ｌａ、 ＣｅＰｒ、Ｐｍ、
Ｅｎ、Ｃｄ、Ｔｂ、Ｄｙ、Ｈｏ、Ｅｒ、 Ｔｍ、 Ｙｂ
、 Ｌｕ、 Ｙ）の１種又は２種以上が５％以下含有
されており、かつＳｍ＋Ｎｄ＋Ｒが２２〜２８％である
ことを特徴とする希土類磁石合金である。これにより２
第１発明と同等のｔｎ磁気特性得られる。Next, a second invention is a rare earth metal R (La, CePr, Pm,
En, Cd, Tb, Dy, Ho, Er, Tm, Yb
, Lu, Y) in an amount of 5% or less, and Sm+Nd+R is 22 to 28%. This results in 2
tn magnetic properties equivalent to those of the first invention can be obtained.
次に 上記発明における成分限定理由につき。Next, regarding the reason for limiting the ingredients in the above invention.
説明する。explain.
Ｓｍ：８〜２０％
Ｓｍは、Ｎｄと共に１本発明の希土類磁石合金の主体を
なして、最大エネルギー積と保磁力の特性を左右する成
分であるが、８％未満では十分な最大エネルギー積、保
磁力が得られない、一方２０％を越えるとコスト高とな
り、また資源的なメリットがない。Sm: 8-20% Sm, together with Nd, forms the main component of the rare earth magnet alloy of the present invention and is a component that influences the characteristics of maximum energy product and coercive force, but if it is less than 8%, the maximum energy product is insufficient, On the other hand, if the coercive force exceeds 20%, the cost will be high and there will be no advantage in terms of resources.
Ｎｄ：６〜２０％
６％未満では、コスト、資源的なメリットがない、一方
、２０％を越えると、最大エネルギー積保磁力が急激に
低下する。Nd: 6 to 20% If it is less than 6%, there is no advantage in terms of cost or resources. On the other hand, if it exceeds 20%, the maximum energy product coercive force will decrease rapidly.
Ｆｅ：１０〜２５％
１０％未満では十分な残留磁束密度、最大エネルギー積
が得られない。一方、２５％を越えると十分な保磁力が
得られない。Fe: 10-25% If it is less than 10%, sufficient residual magnetic flux density and maximum energy product cannot be obtained. On the other hand, if it exceeds 25%, sufficient coercive force cannot be obtained.
Ｃｕ：５〜１０％ ５％未満では、十分な保磁力が得られない。Cu: 5-10% If it is less than 5%, sufficient coercive force cannot be obtained.
方、１０％を越えると残留磁束密度が低下する。On the other hand, if it exceeds 10%, the residual magnetic flux density decreases.
Ｚｒ：１〜４％ １％未満では、十分な保磁力が得られない。Zr: 1-4% If it is less than 1%, sufficient coercive force cannot be obtained.
方、４％を越えると残留磁束密度の低下、最大エネルギ
ー積の低下を招く。On the other hand, if it exceeds 4%, the residual magnetic flux density and the maximum energy product will decrease.
Ｍｎ：０．ｌ−１％
Ｍｎは 希土［（５５石金合金溶体化処理時に＆ＩＩＨ
１の均一性を政庁する効果を発揮する。これにより十分
量のＺｒ、Ｔｉを基地中に固溶させることができる。そ
して、Ｍｎは、Ｔｉ、Ｂと共に複合添加することによっ
て、初めて、その添加効果を発揮するもので、単独添加
による磁気特性への寄与は極めて小さい。Mn: 0. l-1% Mn is rare earth [(During solution treatment of 55-stone gold alloy
It will have the effect of ensuring uniformity in government offices. This allows a sufficient amount of Zr and Ti to be solid-dissolved in the base. Mn exhibits its additive effect only when added in combination with Ti and B, and its contribution to magnetic properties when added alone is extremely small.
しかして、０．１％未満では磁気特性向−ヒの効果が少
なく、一方１％を越えると最大エネルギー積が低下する
。Therefore, if it is less than 0.1%, the effect of improving magnetic properties will be small, while if it exceeds 1%, the maximum energy product will decrease.
Ｔｉ：０．ｌ＝１％
Ｔｉは （Ｓｍ Ｎｄ）ｚ （Ｃｏ、 Ｆｅ、 Ｃｕ
）ｖ相（以下、２−７相ともいう）の析出量を増加させ
、保磁力の向上に寄与すると考えられる。Ti: 0. l=1% Ti is (Sm Nd)z (Co, Fe, Cu
) It is thought that this increases the amount of precipitated v-phase (hereinafter also referred to as 2-7 phase) and contributes to improving the coercive force.
しかし、単独では、減磁曲線の角形性が悪く、最大エネ
ルギー積が低下してしまう。However, when used alone, the squareness of the demagnetization curve is poor and the maximum energy product decreases.
しかして、０．１％未満では磁気特性向上の効果が少な
く、一方１％を越えると最大エネルギー積が低下する。Therefore, if it is less than 0.1%, the effect of improving magnetic properties will be small, while if it exceeds 1%, the maximum energy product will decrease.
Ｂ：０．００３〜０．０１５％
Ｂは３粒界、亜粒界へ２粗大な前記２−７相が不均一に
析出することを防止し、微細な２−７相を組織全体に均
一に析出させる。そのため、減磁曲線の角形性が改善さ
れ、最大エネルギー積は向上する。しかし、単独添加で
は最大エネルギー積。B: 0.003 to 0.015% B prevents the coarse 2-7 phase from precipitating unevenly at grain boundaries and sub-grain boundaries, and makes the fine 2-7 phase uniform throughout the structure. Let it precipitate. Therefore, the squareness of the demagnetization curve is improved and the maximum energy product is improved. However, the maximum energy product when added alone.
保磁力が大幅に低下する。Coercive force decreases significantly.
しかして、０．００３％未満では磁気特性１組織の改善
効果が少なく、０．０１５％を越えると保磁力が大幅に
低下する。However, if it is less than 0.003%, the effect of improving the magnetic properties 1 structure is small, and if it exceeds 0.015%, the coercive force will be significantly reduced.
前記Ｒとして示したＳｍ、Ｎｄ以外の希土類金属：５％
以下
第２発明において、Ｓｍ、Ｎｄ以外の希土類金属の１種
又は２種以上を用いるのは、これにより希土類磁石合金
のコストを低下させるためである。Rare earth metals other than Sm and Nd shown as R above: 5%
In the second invention, one or more rare earth metals other than Sm and Nd are used in order to reduce the cost of the rare earth magnet alloy.
しかし、５％を越えると保磁力、最大エネルギー積が低
下する。However, if it exceeds 5%, the coercive force and the maximum energy product decrease.
全希土類金属量＝２２〜２８％
この量が２２％未満では希土類磁石として要求される最
大エネルギー積、保持力が得られない。Total amount of rare earth metals = 22 to 28% If this amount is less than 22%, the maximum energy product and coercive force required for a rare earth magnet cannot be obtained.
また、２８％を越えて含有させると残留４５３束密度量
大エネルギー積が低下する。Moreover, when the content exceeds 28%, the residual 453 flux density mass energy product decreases.
本発明においては、高価で資源的切迫状態にあるＳｍの
一部をＮｄに代え、かつＭｎ、 Ｔｉ、 Ｂの複合添
加を行っている。そのため、安価で、かつ保磁力及び最
大エネルギー積に優れた希土類磁石合金を提供すること
ができる。In the present invention, a part of Sm, which is expensive and under resource pressure, is replaced with Nd, and Mn, Ti, and B are added in combination. Therefore, it is possible to provide a rare earth magnet alloy that is inexpensive and has excellent coercive force and maximum energy product.
本発明の希土類磁石合金が、このように優れた効果を有
するのは９次の理由によるものと考えられる。The reason why the rare earth magnet alloy of the present invention has such excellent effects is considered to be due to the following reason.
即ち、前記従来技術で示したＳｍ−Ｃｏ−ＦｅＣｕ−Ｚ
ｒ系希土類磁石合金では、溶体化処理後ひき続き時効処
理を行うことにより、 Ｓｍｚ Ｃ０１’ｌ 相（
２−１７相）がＳｍＣｏ、相（１−５相）で囲まれた微
細セル状構造を形成し、大きな保磁力を発揮していた。That is, Sm-Co-FeCu-Z shown in the prior art
In r-based rare earth magnet alloys, the Smz C01'l phase (
The SmCo phase (2-17 phase) formed a fine cellular structure surrounded by the SmCo phase (1-5 phase), exhibiting a large coercive force.
また、前記従来のＮｄ置換型磁石合金では、上記セル状
構造を形成しても十分な保磁力が得られなかった。その
理由は１次のように推察される。Further, in the conventional Nd substitution type magnet alloy, even if the above-mentioned cellular structure was formed, sufficient coercive force could not be obtained. The reason is presumed to be as follows.
即ち、上記２−１７相と１−５相の２相構造の保磁力は
、Ｌｉｖｉｎｇｓｔｏｎらの解説（Ｊ、 Ａｐｐｌ、Ｐ
ｈｙｓ、４Ｂ （１９７７）、１３５０〕によると、２
−１７相と１−５相の磁壁エネルギーの差に比例する。That is, the coercive force of the two-phase structure of the 2-17 phase and 1-5 phase is based on the explanation by Livingston et al. (J, Appl, P
hys, 4B (1977), 1350], 2
It is proportional to the difference in domain wall energy between the -17 phase and the 1-5 phase.
そして、ＳｍをＮｄで置換すると２−１７相、１−５相
共に磁壁エネルギーが低下し、しかもその差が低下する
ため、保磁力が低下する。この保磁力の低下と別に付随
した減磁曲線の角形性の低下により、最大エネルギー積
が低下する。When Sm is replaced with Nd, the domain wall energy of both the 2-17 phase and the 1-5 phase decreases, and the difference between them decreases, resulting in a decrease in coercive force. This decrease in coercive force and the accompanying decrease in the squareness of the demagnetization curve result in a decrease in the maximum energy product.
これに対し１本発明のＮｄ置換型磁石合金においては、
前記従来のＮｄ置換型磁石合金に比して保磁力、最大エ
ネルギー積ともに大きく向上する。On the other hand, in the Nd substitution type magnet alloy of the present invention,
Both the coercive force and the maximum energy product are greatly improved compared to the conventional Nd substitution type magnet alloy.
このメカニズムの詳細は不明であるが８次のように推察
される。即ち１本発明の磁石合金では、上記微細セル状
組織に重畳して、Ｚｒ、Ｔｉリッチな（Ｓｍ、Ｎｄ）ｚ
（Ｃｏ、Ｆｅ、Ｃｕ）７相の微細でしかも均一な析
出を実現することにより磁壁をより強固にピン止めする
。このため、保磁力のアップと角形性を向上させ、これ
により最大エネルギー積を大幅に向上することができる
。Although the details of this mechanism are unknown, it is presumed to be of the 8th order. That is, in the magnetic alloy of the present invention, Zr and Ti-rich (Sm, Nd)z are superimposed on the fine cellular structure.
By realizing fine and uniform precipitation of seven phases (Co, Fe, Cu), the domain wall is more firmly pinned. Therefore, it is possible to increase the coercive force and improve the squareness, thereby significantly increasing the maximum energy product.
本発明にかかる種々の希土類磁石合金を製造しそれらに
つき、磁気特性を測定した。Various rare earth magnet alloys according to the present invention were manufactured and their magnetic properties were measured.
即ち、所定の割合の金属原料を第１表、第２表に示す割
合で混合５溶解し、得られた磁石合金を平均粒径２〜５
μｍに粉砕し、ｌ０ＫＧの磁場中で磁場プレス成形を行
ない、１１５０〜１２００°Ｃ１２〜４時間で焼結後、
焼結温度より２０〜４０°Ｃ低い温度にて、２〜６時間
時間化処理を行なった０次いで、７５０〜９００ ’Ｃ
で時効処理を施し、０．５〜５°Ｃ／ｍｉｎで４００°
Ｃまで徐冷後急冷を行なった。なお、製造条件の幅は９
合金組成により磁気特性の最適な条件が異なることによ
る。That is, a predetermined proportion of metal raw materials are mixed and melted at the proportions shown in Tables 1 and 2, and the obtained magnetic alloy is mixed with an average particle size of 2 to 5.
After grinding to μm, magnetic press forming in a 10KG magnetic field, and sintering at 1150-1200°C for 12-4 hours,
Temperature treatment was carried out for 2 to 6 hours at a temperature 20 to 40 °C lower than the sintering temperature, then 750 to 900'C.
Aging treatment is performed at 400° at 0.5 to 5°C/min.
After slow cooling to C, rapid cooling was performed. In addition, the range of manufacturing conditions is 9
This is because the optimal conditions for magnetic properties differ depending on the alloy composition.
得られた磁石合金の磁気特性、即ち保磁力（ｉＨｃ （
ＫＯｅ））、残留磁束密度（Ｂｒ（ＫＧ）〕、最大エネ
ルギー積（ＢＨｍａ ｘ （ＭＧＯｅ））につき、第１
表、第２表に示す。なお、同表はＣｏ１（残部）の表示
を省略しである。The magnetic properties of the obtained magnet alloy, namely coercive force (iHc (
KOe)), residual magnetic flux density (Br(KG)), and maximum energy product (BHmax(MGOe)).
It is shown in Table 2. Note that the table omits the display of Co1 (remainder).
第１表において、Ｎｏ！−１１は第１発明、Ｎｏ１２及
び１３は第２発明に関する磁石合金である。In Table 1, No! -11 is a magnet alloy related to the first invention, and Nos. 12 and 13 are magnet alloys related to the second invention.
また、第２表には、比較のために、ＮｏＣ１〜Ｃ２０に
比較磁石合金を、ＮｏＣ２１には前記従来技術（特開昭
６２−２４３７３１号公報の実施例１）を示した。For comparison, Table 2 shows comparative magnet alloys for NoC1 to C20, and the prior art (Example 1 of JP-A-62-243731) for NoC21.
第１表、第２表より知られるごとく５本発明によれば、
保磁力１０ＫＯｅ以上、残留磁束密度１０，５ＫＣ，以
上、最大エネルギー積２８ＭＧＯｅ程度の希土類磁石合
金を得ることができる。As is known from Tables 1 and 2, according to the present invention,
A rare earth magnet alloy having a coercive force of 10 KOe or more, a residual magnetic flux density of 10.5 KC or more, and a maximum energy product of about 28 MGOe can be obtained.
また、Ｍｎ、Ｂの添加により焼結温度、溶体化温度の最
適領域が拡がる。これにより工業的生産において、上記
工程での温度バラツキによる品質のバラツキが低減する
。さらに、Ｎｄｉ換合金合金、研削性が改善され、ワレ
、カケ等の発生率が低くなるため製品の歩留が向上する
。Furthermore, the addition of Mn and B expands the optimum range of sintering temperature and solution temperature. This reduces quality variations due to temperature variations in the above steps in industrial production. Furthermore, the grindability of the Ndi exchange alloy is improved, and the incidence of cracks, chips, etc. is reduced, resulting in improved product yield.
これに比して、比較例の希土類磁石合金においては、Ｃ
ＩはＭｎ、Ｔｉ、Ｂ無添加の場合であり。In contrast, in the rare earth magnet alloy of the comparative example, C
I is the case where Mn, Ti, and B are not added.
本発明に比べ保磁力、最大エネルギー積ともに低い、Ｃ
２〜Ｃ４はＭｎ、Ｔｉ、Ｂのうち２種を添加した合金で
あるが、Ｔｉ添加のもので保ｉｆｆ力の改善は見られる
ものの、最大エネルギー積は本発明合金に比べ低い。C which has lower coercive force and maximum energy product than the present invention.
2 to C4 are alloys to which two of Mn, Ti, and B are added, and although the retention force is improved by adding Ti, the maximum energy product is lower than that of the alloy of the present invention.
Ｃ５〜Ｃ１２は、Ｍｎ、Ｔｉ、Ｂ、ＡＮ、Ｃｒ。C5 to C12 are Mn, Ti, B, AN, and Cr.
Ｖ、Ｍｏ、Ｎｂを、１種添加した場合で、いずれも保磁
力、最大エネルギー積ともに低い。When one type of V, Mo, or Nb is added, both the coercive force and the maximum energy product are low.
Ｃ５〜Ｃ１２は、成分系は同一があるが、それぞれＳｍ
、Ｎｄ、Ｍｎ、Ｔｉ、Ｂの含有量が本発明外の合金の比
較例である。Ｃ１５では、保磁力は優れているが、最大
エネルギー積が低い。C5 to C12 have the same component system, but each has Sm
, Nd, Mn, Ti, and B are comparative examples of alloys other than those of the present invention. C15 has an excellent coercive force but a low maximum energy product.
その他のＣ１３，１４，１６〜１８は、保磁力。The other C13, 14, 16 to 18 are coercive forces.
最大エネルギー積ともに大幅に低下する。Both the maximum energy product decreases significantly.
また、Ｃ１９，Ｃ２０は、全希土類金属量が本発明外の
合金の比較例である。Ｃ１９では保磁万力は優れている
で、最大エネルギー積は低い。Ｃ２０は保磁力最大エネ
ルギー積とも低い。Further, C19 and C20 are comparative examples of alloys in which the total amount of rare earth metals is outside the scope of the present invention. C19 has excellent coercive force and low maximum energy product. C20 has a low coercive force maximum energy product.
更に、従来の希土類磁石合金（ＮｏＣ２］、）は。Furthermore, the conventional rare earth magnet alloy (NoC2).
残留磁束密度は若干低い程度であるが、最大エネルギー
積、保磁力ともに低い。Although the residual magnetic flux density is slightly low, both the maximum energy product and coercive force are low.
第１図は希土類金属と飽和磁束密度との関係を示す線図
５第２図は従来のＣｅ置換型磁石合金における３ｍ世と
最大エネルギー積、保磁力、残留磁束密度の関係を示す
線図、第３図は従来のＮｄ置換型磁石合金におけるＮｄ
ｉと保磁力の関係を示す線図である。Figure 1 is a diagram showing the relationship between rare earth metals and saturation magnetic flux density. Figure 2 is a diagram showing the relationship between 3m generation, maximum energy product, coercive force, and residual magnetic flux density in conventional Ce substitution type magnet alloys. Figure 3 shows Nd in a conventional Nd substitution type magnet alloy.
It is a diagram showing the relationship between i and coercive force.
Claims (2)
ｅ１０〜２５％、Ｃｕ５〜１０％、Ｚｒ１〜４％、Ｍｎ
０．１〜１％、Ｔｉ０．１〜１％、Ｂ０．００３〜０．
０１５％、残部Ｃｏからなり、かつＳｍ＋Ｎｄが２２〜
２８％であることを特徴とする希土類磁石合金。(1) Weight ratio: Sm8-20%, Nd6-20%, F
e10-25%, Cu5-10%, Zr1-4%, Mn
0.1-1%, Ti0.1-1%, B0.003-0.
015%, the balance is Co, and Sm+Nd is 22~
A rare earth magnetic alloy characterized by having a content of 28%.
ｅ１０〜２５％、Ｃｕ５〜１０％、Ｚｒ１〜４％、Ｍｎ
０．１〜１％、Ｔｉ０．１〜１％、Ｂ０．００３〜０．
０１５％、残部Ｃｏからなり、かつＳｍ及びＮｄを除く
希土類金属Ｒの１種または２種以上を５％以下含有し、
更にＳｍ＋Ｎｄ＋Ｒが２２〜２８％であることを特徴と
する希土類磁石合金。(2) Weight ratio: Sm8-20%, Nd6-20%, F
e10-25%, Cu5-10%, Zr1-4%, Mn
0.1-1%, Ti0.1-1%, B0.003-0.
015%, the balance being Co, and containing 5% or less of one or more rare earth metals R excluding Sm and Nd,
A rare earth magnet alloy further characterized in that Sm+Nd+R is 22 to 28%.
Priority Applications (5)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP32862188A JPH02173236A (en) | 1988-12-26 | 1988-12-26 | Rare earth magnetic alloy |
| KR1019890018900A KR900010031A (en) | 1988-12-26 | 1989-12-19 | Rare Earth Magnet Alloy |
| DE3942624A DE3942624A1 (en) | 1988-12-26 | 1989-12-22 | RARE EARTH MAGNETIC ALLOY |
| GB8929088A GB2226330B (en) | 1988-12-26 | 1989-12-22 | Rare earth magnet alloy |
| US07/457,041 US5017247A (en) | 1988-12-26 | 1989-12-26 | Rare earth magnet alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP32862188A JPH02173236A (en) | 1988-12-26 | 1988-12-26 | Rare earth magnetic alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH02173236A true JPH02173236A (en) | 1990-07-04 |
Family
ID=18212311
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP32862188A Pending JPH02173236A (en) | 1988-12-26 | 1988-12-26 | Rare earth magnetic alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH02173236A (en) |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61213340A (en) * | 1985-03-15 | 1986-09-22 | Daido Steel Co Ltd | Rare earth magnet manufacturing method |
| JPS62192568A (en) * | 1986-02-18 | 1987-08-24 | Daido Steel Co Ltd | Manufacturing method of rare earth cobalt magnet |
| JPS62243731A (en) * | 1986-04-15 | 1987-10-24 | Tohoku Metal Ind Ltd | Permanent magnet alloy and its manufacture |
-
1988
- 1988-12-26 JP JP32862188A patent/JPH02173236A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61213340A (en) * | 1985-03-15 | 1986-09-22 | Daido Steel Co Ltd | Rare earth magnet manufacturing method |
| JPS62192568A (en) * | 1986-02-18 | 1987-08-24 | Daido Steel Co Ltd | Manufacturing method of rare earth cobalt magnet |
| JPS62243731A (en) * | 1986-04-15 | 1987-10-24 | Tohoku Metal Ind Ltd | Permanent magnet alloy and its manufacture |
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