JPS60144906A - Permanent magnet material - Google Patents
Permanent magnet materialInfo
- Publication number
- JPS60144906A JPS60144906A JP59000261A JP26184A JPS60144906A JP S60144906 A JPS60144906 A JP S60144906A JP 59000261 A JP59000261 A JP 59000261A JP 26184 A JP26184 A JP 26184A JP S60144906 A JPS60144906 A JP S60144906A
- Authority
- JP
- Japan
- Prior art keywords
- magnetic flux
- flux density
- residual magnetic
- permanent magnet
- maximum energy
- 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
Classifications
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/032—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials
- H01F1/04—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials metals or alloys
- H01F1/047—Alloys characterised by their composition
- H01F1/053—Alloys characterised by their composition containing rare earth metals
- H01F1/055—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5
- H01F1/0555—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 pressed, sintered or bonded together
- H01F1/0557—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 pressed, sintered or bonded together sintered
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）
この発明は、家庭電化製品、音響製品、時計部品、自動
車部品、精密機器等々の永久磁石を用いる広範囲な用途
に使用することができる永久磁石材料に関し、とくに希
土類元素（Ｒ）と鉄（Ｆ ’ｅ ）とを主体とする永久
磁石材料に関するものである。Detailed Description of the Invention (Field of Industrial Application) This invention provides a permanent magnet that can be used in a wide range of applications such as home appliances, audio products, watch parts, automobile parts, precision instruments, etc. The present invention relates to materials, and particularly to permanent magnet materials mainly composed of rare earth elements (R) and iron (F'e).
（従来技術）
近年、永久磁石材料における最大エネルギ積（（ＢＨ）
ｗａｘ ）の向上はかってのアルニコ系磁石材料等の
それに比べて著しいものがあり、とくに家庭電化製品、
音響製品、時計部品、自動車部品、精密機器等々の小型
軽量化および高性能化等に大きく貢献している。(Prior art) In recent years, the maximum energy product ((BH)
wax ) has been significantly improved compared to that of previous alnico magnet materials, especially for home appliances,
It has greatly contributed to making audio products, watch parts, automobile parts, precision equipment smaller, lighter, and higher in performance.
従来、このような優れた特性の永久磁石材料としては希
土類−コバルト系磁石が代表的なものであり、その最大
エネルギ積（（Ｂ Ｈ） ｆｆ１ａｘ ）は１８〜２８
ＭＧ・Ｏｅ程度のかなり高い値を示している。しかし、
最大エネルギ積（（ＢＨ）ｍａｘ ）をさらに向上させ
るための研究はいぜんとして続けられ、一部では他の希
土類磁石の開発も進んでおり、なかには希土類−鉄系磁
石材料についての開発も行われている。この希土類−鉄
系磁石材料としてはＮｄ−Ｆｅ−、Ｂ系のものもあるが
、この系の永久磁石材料では残留磁束密度（Ｂ ｒ）の
温度係数があまり良くないという問題点があった。Conventionally, rare earth-cobalt magnets have been typical as permanent magnet materials with such excellent properties, and their maximum energy product ((B H) ff1ax) is 18 to 28.
It shows a fairly high value on the order of MG.Oe. but,
Research to further improve the maximum energy product ((BH)max) is continuing, and the development of other rare earth magnets is also progressing, and some rare earth-iron magnet materials are also being developed. . This rare earth-iron based magnet material includes Nd-Fe- and B based permanent magnet materials, but this type of permanent magnet material has a problem in that the temperature coefficient of residual magnetic flux density (Br) is not very good.
（発明の目的）
この発明は上述した従来の問題点に着目してなされたも
ので、残留磁束密度（Ｂｒ）および保磁力Ｃ５Ｈｃ 、
■Ｈｃ）が優れていると共に、とくに最大エネルギ積
（（Ｂ Ｈ） ｗａｘ ）が大きな値を示し、しかも残
留磁束密度（Ｂｒ）の温度係数が良好である希土類−鉄
系永久磁石材料を提供することを目的としている。(Objective of the Invention) This invention was made by focusing on the above-mentioned conventional problems.
■ To provide a rare earth-iron permanent magnet material that has an excellent Hc), a particularly large maximum energy product ((B H) wax), and a good temperature coefficient of residual magnetic flux density (Br). The purpose is to
（発明の構成）
この発明による永久磁石材料は、一般式、Ｒ□ 、−β
、Ｆｅ、ＭβＸ、で表わされ、Ｒが希土類元素の１種
または２種以上、ＭがＴｉ。(Structure of the Invention) The permanent magnet material according to the present invention has the general formula R□, -β
, Fe, MβX, where R is one or more rare earth elements, and M is Ti.
Ｚｒ、Ｈｆ、Ｖ、Ｎｂ、Ｔａ、Ｃｒ、Ｍｏ、Ｗの１種マ
タは２種以上、ＸがＢ、Ｃ，Ｎ、Ｓｔ 、Ｐの１種また
は２種以上であり、
０．６０≦α≦０．８５．
０．０１≦β≦０．１０、
γ＜０．１５
であることを特徴としている。One type of Zr, Hf, V, Nb, Ta, Cr, Mo, and W are two or more types, X is one or two or more types of B, C, N, St, and P, and 0.60≦α ≦0.85. It is characterized in that 0.01≦β≦0.10 and γ<0.15.
この発明による永久磁石材料は、上記のように、一般式
、Ｒ１−ｏ−β−ｙＦｅｏＭβｘｙで表わされるが、式
中のＲは希土類元素の１種または２種以上であることを
示し、Ｎｄをはじめとし、Ｓｃ、Ｙ、Ｌａ、Ｃｅ、Ｐｒ
、Ｐｍ、Ｓｍ。As mentioned above, the permanent magnet material according to the present invention is represented by the general formula R1-o-β-yFeoMβxy, where R represents one or more rare earth elements, and Nd Introduction, Sc, Y, La, Ce, Pr
, Pm, Sm.
Ｅｕ、Ｇｄ、Ｔｂ、Ｄｙ、Ｈｏ、Ｅｒ、Ｔｍ。Eu, Gd, Tb, Dy, Ho, Er, Tm.
Ｙｂ、Ｌｕのうちの１種または２種以上が用いられる。One or more of Yb and Lu are used.
また、上記一般式において、Ｆｅ（鉄）は、０．６０≦
α≦０．８５の範囲としている。ここで、Ｆｅの量が多
すぎると、残留磁束密度（Ｂｒ）は向上するものの、保
磁力（ＢＨＣ。In addition, in the above general formula, Fe (iron) is 0.60≦
The range is α≦0.85. Here, if the amount of Fe is too large, the residual magnetic flux density (Br) will improve, but the coercive force (BHC) will increase.
工Ｈｃ）が極端に減少するため、すぐれた最大エネルギ
積（（ＢＨ） ｍａりは得られなくなるので、α≦０．
８５とした。一方、Ｆｅの量が少なすぎると残留磁束密
度（Ｂｒ）が低くなり、最大エネルギ積（’（Ｂ Ｈ）
ｍａｗ ）が減少するので、０．６０≦αとした。Since the maximum energy product ((BH) ma) decreases extremely, it becomes impossible to obtain an excellent maximum energy product ((BH) ma), so α≦0.
It was set at 85. On the other hand, if the amount of Fe is too small, the residual magnetic flux density (Br) will be low, and the maximum energy product ('(B H)
maw ) decreases, so 0.60≦α is set.
さらに、上記一般式において、ＭはＴｉ。Furthermore, in the above general formula, M is Ti.
Ｚｒ、Ｈｆ、Ｖ、Ｎｂ、Ｔａ、Ｃｒ、Ｍｏ、Ｗの１種ま
たは２種以上であり、０．０１≦β≦ｏ、ｉｏの範囲と
している。また、ＸはＢ、Ｃ。It is one or more of Zr, Hf, V, Nb, Ta, Cr, Mo, and W, and is in the range of 0.01≦β≦o, io. Also, X is B, C.
Ｎ、Ｓｉ、Ｐの１種または２種以上であり、γく０．１
５の範囲としている。ここで、上記Ｍは上記Ｘ元素と複
合添加することによりＭの一部が硼化物、炭化物、窒化
物、珪化物、燐化物となり、保磁力（Ｂ Ｈｃ 、 ｚ
Ｈａ）の向上および残留磁束密度（Ｂｒ）の温度係数
の向上に著しい効果をもたらす。しかし、Ｍの量が少な
すぎると残留磁束密度（Ｂｒ）の温度係数の向上は望め
ないため、０．０１≦βとし、Ｍの量が多すぎると前記
硼化物、炭化物、窒化物、珪化物、燐化物等の形成量が
多くなり、磁気特性が劣化するので、β≦０．１０とし
た。また、上記Ｘ元素は希土類−鉄系磁石、たとえばＮ
ｄ−Ｆｅ系磁石のキュリ一点を常温程度から３００℃以
上に昇温させる効果を有するものであるが、Ｘの量が多
すぎると保磁力（ＢＨＣ、ｒＨｃ）および残留磁束密度
（Ｂ ｒ）が減少し、すぐれた最大エネルギ積（（ＢＨ
）ＷａＸ ）が得られなくなるのでγ＜０．１５とした
。One or more of N, Si, and P, and γ is 0.1
The range is 5. Here, by adding M in combination with the above element
This has a significant effect on improving the temperature coefficient of residual magnetic flux density (Br) and the residual magnetic flux density (Br). However, if the amount of M is too small, no improvement in the temperature coefficient of residual magnetic flux density (Br) can be expected, so it is set to 0.01≦β, and if the amount of M is too large, the borides, carbides, nitrides, and silicides Since the amount of formation of , phosphides, etc. increases and the magnetic properties deteriorate, β≦0.10 is set. In addition, the above X element is a rare earth-iron magnet, for example, N
It has the effect of raising the temperature of the Curie point of a d-Fe magnet from room temperature to over 300℃, but if the amount of X is too large, the coercive force (BHC, rHc) and residual magnetic flux density (Br) will decrease. reduced and excellent maximum energy product ((BH
) WaX ) could no longer be obtained, so γ<0.15 was set.
（実施例１）
ＦｅＴｉＢ なる組成
ＮｄＯ，１？−β ０．７５ β ０，０８の合金をア
ルゴン雰囲気中に調整したボタン溶解炉を用いて溶製し
た。次いで、溶製合金を乳鉢内で粗粉砕した後、ジェッ
トミルにて平均粒径５ｐｍ程度まで微粉砕した。(Example 1) FeTiB composition NdO, 1? -β 0.75 β 0.08 alloy was melted using a button melting furnace adjusted to an argon atmosphere. Next, the molten alloy was roughly pulverized in a mortar, and then finely pulverized in a jet mill to an average particle size of about 5 pm.
次に、得られた粉末を１５ＫＯｅの磁場中で約２ ｔｏ
ｎｆ／ ｃｍ２の圧力をかけてプレス成形したのち、得
られた成形体をアルゴン雰囲気中において１０００℃で
１時間の条件で焼結を行い、寥温ま−で急冷した後さら
に所定の熱処理を施した。Next, the obtained powder was heated in a magnetic field of 15 KOe for about 2 to
After press molding under a pressure of nf/cm2, the obtained molded body was sintered at 1000°C for 1 hour in an argon atmosphere, rapidly cooled to the bath temperature, and then further subjected to prescribed heat treatment. .
次いで、得られた磁石材料の残留磁束密度（Ｂｒ）、保
磁力（ＢＨＣ、ＩＨＣ）、最大エネルギ積（（Ｂ Ｈ）
ｌｌ１ａｘ ）および残留磁束密度（Ｂｒ）の温度係
数を調べたところ、第１表および第１図に示す結果とな
った。Next, the residual magnetic flux density (Br), coercive force (BHC, IHC), and maximum energy product ((B H) of the obtained magnet material are
When the temperature coefficients of ll1ax) and residual magnetic flux density (Br) were investigated, the results were shown in Table 1 and FIG.
第１表および第１図に示すように、Ｔｉ量が０．０１≦
βで保磁力（ＢＨＣ、ＩＨＣ）および最大エネルギ積（
（Ｂ Ｈ） １１ａｘ ）が向上すると共に、とくに残
留磁束密度（Ｂ ｒ）の温度係数が小さくなることが明
らかである。しかし、Ｔｉ量が多くなりすぎると保磁力
（ＢＨＣ，ＩＨＣ）および最大エネルギー積（（ＢＨ）
１１ａｘ ）が著しく低下するので、β≦０．１０と
するのが良いことが確かめられた。As shown in Table 1 and Figure 1, the amount of Ti is 0.01≦
β is the coercive force (BHC, IHC) and the maximum energy product (
It is clear that (B H) 11ax) is improved and, in particular, the temperature coefficient of residual magnetic flux density (B r) is reduced. However, if the amount of Ti becomes too large, the coercive force (BHC, IHC) and the maximum energy product ((BH)
11ax) is significantly reduced, it was confirmed that it is better to set β≦0.10.
（実施例２）
Ｎｄ Ｆｅ ＶＢ Ｓｔな
０．１７−β ０．７５ β ０．０３ ０．．０５る
組成の合金をアルゴン雰囲気中に調整し〜たボタン溶解
炉を用いて溶製した。次いで、溶製合金を乳鉢内で粗粉
砕した後、ジェットミルにて平均粒径５７ｈｍ程度まで
微粉砕した。(Example 2) Nd Fe VB St 0.17-β 0.75 β 0.03 0. ．． An alloy having a composition of 0.05 was melted using a button melting furnace adjusted to an argon atmosphere. Next, the molten alloy was roughly pulverized in a mortar, and then finely pulverized in a jet mill to an average particle size of about 57 hm.
次に、得られた粉末を１５ＫＯｅの磁場中で約２ｔｏｎ
ｆ／ｃｍ２の圧力をかけてプレス成形したのち、得られ
た成形体をアルゴン雰囲気中においてａｏｏ’ｃで１時
間の条件で焼結を行い、室温まで急冷した後さらに所定
の熱処理を施した。Next, the obtained powder was heated to approximately 2 tons in a magnetic field of 15 KOe.
After press molding under a pressure of f/cm2, the obtained molded body was sintered in an argon atmosphere at AOO'C for 1 hour, rapidly cooled to room temperature, and then further subjected to a prescribed heat treatment.
次いで、得られた磁石材料の残留磁束密度（Ｂｒ）、保
磁力（ＢＨＣ、ＩＨＣ）、最大エネルギ積（（ＢＨ）
ｍａｘ ）および残留磁束密度（Ｂｒ）の温度係数を調
べたところ、第２表および第２図に示す結果となった。Next, the residual magnetic flux density (Br), coercive force (BHC, IHC), and maximum energy product ((BH) of the obtained magnet material are
max) and the residual magnetic flux density (Br), the results are shown in Table 2 and Figure 2.
第２表および第２図に示すように、Ｖ量が０．０１≦β
で保磁力（ＢＨＣ，ＩＨＣ）および最大エネルギ積（（
ＢＨ） ｗａｘ ）が向上すると共に、とくに残留磁束
密度（Ｂｒ’）の温度係数が小さくなることが明らかで
ある。しかし、Ｖ量が多くなりすぎると磁気特性が著し
く低下するので、β≦０．ｌＯとするのが良いことが確
かめられた。As shown in Table 2 and Figure 2, the amount of V is 0.01≦β
coercive force (BHC, IHC) and maximum energy product ((
It is clear that the temperature coefficient of the residual magnetic flux density (Br') in particular decreases as the BH)wax) improves. However, if the amount of V becomes too large, the magnetic properties will deteriorate significantly, so β≦0. It was confirmed that it is good to set it to lO.
（実施例３）
Ｎｄｏ、１７−β Ｆｅｏ、７５ＣｒβＮｏ、ｏ８なる
組成の合金をアルゴン雰囲気中に調整したボタン溶解炉
を用いて溶製した。次いで、溶製合金を乳鉢内で粗粉砕
した後、ジェットミルにて平均粒径５ｇｍ程度まで微粉
砕した。(Example 3) An alloy having a composition of Ndo, 17-β Feo, 75CrβNo, and o8 was melted using a button melting furnace adjusted to an argon atmosphere. Next, the molten alloy was roughly pulverized in a mortar, and then finely pulverized in a jet mill to an average particle size of about 5 gm.
次に、得られた粉末を１５ＫＯｅの磁場中で約２ ｔｏ
ｎｆ ／ ｃｎ＋２の圧力をかけてプレス成形したのち
、得られた成形体をアルゴン雰囲気中において８００°
Ｃで１時間の条件で焼結を行い、室温まで急冷した後さ
らに所定の熱処理を施した。Next, the obtained powder was heated in a magnetic field of 15 KOe for about 2 to
After press molding under a pressure of nf/cn+2, the obtained molded body was heated at 800° in an argon atmosphere.
Sintering was performed at C for 1 hour, and after rapidly cooling to room temperature, a predetermined heat treatment was performed.
（Ｂｒ）、保磁力（ＢＨＣ、ＩＨＣ）、最大エネルギ積
（（ＢＨ） ｆｌｌａｘ ）および残留磁束密度（Ｂｒ
）の温度係数を調べたところ、第３表および第３図に示
す結果となった。(Br), coercive force (BHC, IHC), maximum energy product ((BH) flax ) and residual magnetic flux density (Br
), the results are shown in Table 3 and Figure 3.
第３表および第３図に示すように、Ｃｒ量が０．０１≦
βで保磁力（Ｂ Ｈｃ ＊ Ｉ ＨＣ）および最大エネ
ルギ積（（ＢＨ） ｗａｘ ）が向上すると共に、とく
に残留磁束密度（Ｂ ｒ）の温度係数が著しく小さくな
ることが明らかである。しかし、Ｃｒ量が多くなりすぎ
ると磁気特性が著しく低下するので、β≦０．１０とす
るのが良いことが確かめられた。As shown in Table 3 and Figure 3, the amount of Cr is 0.01≦
It is clear that the coercive force (B Hc * I HC) and the maximum energy product ((BH) wax) are improved with β, and in particular, the temperature coefficient of the residual magnetic flux density (B r) is significantly reduced. However, if the amount of Cr becomes too large, the magnetic properties will deteriorate significantly, so it was confirmed that it is better to set β≦0.10.
（実施例４）
ＮｄＯ，１６ＦｅＯ，？５ＭＯ，０３Ｓ’ ０．０８な
る組成の合金をアルゴン雰囲気中に調整したボタン溶解
炉を用いて溶製した。次いで、溶製合金を乳鉢内で粗粉
砕した後、ジェットミルにて平均粒径５４ｍ程度まで微
粉砕した。(Example 4) NdO, 16FeO,? An alloy having a composition of 5MO, 03S' 0.08 was melted using a button melting furnace adjusted to an argon atmosphere. Next, the molten alloy was roughly pulverized in a mortar, and then finely pulverized in a jet mill to an average particle size of about 54 m.
次に、得られた粉末を１５ＫＯｅの磁場中で約２ ｔｏ
ｎｆ／ ａｍ２の圧力をかけてプレス成形したのち、得
られた成形体をアルゴン雰囲気中において８００℃で１
時間の条件で焼結を行い、室温まで急冷した後さらに所
定の熱処理を施した。Next, the obtained powder was heated in a magnetic field of 15 KOe for about 2 to
After press molding under a pressure of nf/am2, the obtained molded body was heated at 800°C in an argon atmosphere for 1
Sintering was carried out under the conditions of a certain amount of time, and after being rapidly cooled to room temperature, a predetermined heat treatment was performed.
次いで、得られた磁石材料の残留磁束密度（Ｂｒ）、保
磁力（Ｂｌ（ｃ 、ｚＨｃ）、最大エネルギ積（（Ｂ
Ｈ） ｍａｗ ）および残留磁束密度（Ｂｒ）の温度係
数を調べたところ、第４表に示す結果となった。−
第４表に示すように、Ｍが前記Ｔｉ 、Ｖ、Ｃｒのほか
、Ｚｒ、Ｈｆ、Ｎｂ、Ｔａ、Ｍｏ、Ｗであっても保磁力
（ｎＨｃ、ｚＨｃ）および最大エネルギ積（（Ｂ Ｈ）
ｗａｘ ）に優れていると共に、とくに残留磁束密度
（Ｂ ｒ）の温度係数が小さくなることが明らかである
。Next, the residual magnetic flux density (Br), coercive force (Bl (c, zHc), maximum energy product ((B
When the temperature coefficients of H) maw ) and residual magnetic flux density (Br) were investigated, the results are shown in Table 4. - As shown in Table 4, even if M is not only Ti, V, and Cr but also Zr, Hf, Nb, Ta, Mo, and W, the coercive force (nHc, zHc) and maximum energy product ((B H )
It is clear that the temperature coefficient of residual magnetic flux density (Br) is particularly small.
（実施例５）
Ｎｄ０．１７ ＦｅＯ，７５Ｍ０．０２ ＣＯ，０２Ｎ
Ｏ，０４なる組成の合金をアルゴン雰囲気中に調整した
ボタン溶解炉を用いて溶製した。次いで、溶製合金を乳
鉢内で粗粉砕した後、ジェットミルにて平均粒径５Ｊｉ
、ｍ程度まで微粉砕した。(Example 5) Nd0.17 FeO,75M0.02 CO,02N
An alloy having a composition of O.04 was melted using a button melting furnace adjusted to an argon atmosphere. Next, the molten alloy was roughly pulverized in a mortar, and then a jet mill was used to reduce the average particle size to 5Ji.
It was finely ground to about .
次に、得られた粉末を１５ＫＯｅの磁場中で約２ ｔｏ
ｎｆ／ ｃｍ２の圧力をかけてプレス成形したのち、得
られた成形体をアルゴン雰囲気中において８００°Ｃで
１時間の条件で焼結を行い、室温まで急冷した後さらに
所定の熱処理を施した。Next, the obtained powder was heated in a magnetic field of 15 KOe for about 2 to
After press molding under a pressure of nf/cm2, the obtained molded body was sintered at 800°C for 1 hour in an argon atmosphere, and after being rapidly cooled to room temperature, it was further subjected to a prescribed heat treatment.
次いで、得られた磁石材料の残留磁束密度（Ｂｒ）、保
磁力（ＢＨＣ、ｒＨｃ）、最大エネルギｌｔｒ （（Ｂ
Ｈ）ｓａｗ ）およｒｘ−＊ｗｍ宙ｓｇ（Ｂｒ）の温度
係数を調べたところ、第５表に示す結果となった。Next, the residual magnetic flux density (Br), coercive force (BHC, rHc), and maximum energy ltr ((B
When the temperature coefficients of H) saw) and rx-*wm air sg (Br) were investigated, the results are shown in Table 5.
第５表に示すように、実施例４におけるＳｔの代わりに
Ｃ，Ｎを添加したときでも保磁力（ＢＨＣ，ＩＨＣ）お
よび最大エネルギ積（（ＢＨ） ｍａｘ ）に優れてい
ると共に、とくに残留磁束密度（Ｂ ｒ）の温度係数が
小さくなることが明らかである。As shown in Table 5, even when C and N were added in place of St in Example 4, the coercive force (BHC, IHC) and maximum energy product ((BH) max) were excellent, and the residual magnetic flux was particularly good. It is clear that the temperature coefficient of density (Br) becomes smaller.
（発明の効果）
以上説明してきたように、この発明による永久磁石材料
は、一般式
％式％
が希土類元素の１種または２種以上、Ｆ６が鉄、ＭがＴ
ｉ、Ｚｒ、Ｈｆ、Ｖ、Ｎｂ、Ｔａ、Ｃｒ。(Effects of the Invention) As explained above, in the permanent magnet material according to the present invention, the general formula % is one or more rare earth elements, F6 is iron, and M is T.
i, Zr, Hf, V, Nb, Ta, Cr.
ＭＯ，Ｗ（７）Ｌ種マタは２種以上、ＸがＢ、Ｃ。MO, W (7) L type mata is 2 or more types, X is B, C.
Ｎ、Ｓｔ、Ｐの１種または２種以上であり、０．６０≦
α≦０．８５．
０．０１≦β≦０．１０、
γ＜０．１５
であるようにしたから、残留磁束密度（Ｂｒ）および保
磁力（ＲＨＣ，ＩＨＣ）に優れていると共に、とくに最
大エネルギ積（（Ｂ’Ｈ） ｍａｗ ）が大きな値を示
し、しかも残留磁束密度（Ｂｒ）の温度係数が著しく良
好であり、家庭電化製品 音響製品、時計部品、自動車
部品、精密機器等々の小型軽量化を永久磁石の面から実
現することが可能であると共に、特に温度による残留磁
束密度（Ｂ ｒ）への影響が著しく小さいため高性能を
発揮することが可能であるという非常に優れた効果をも
たらしうるものである。One or more of N, St, and P, and 0.60≦
α≦0.85. Since 0.01≦β≦0.10 and γ<0.15 are satisfied, it is excellent in residual magnetic flux density (Br) and coercive force (RHC, IHC), and especially has a maximum energy product ((B' H) maw ) shows a large value, and the temperature coefficient of residual magnetic flux density (Br) is extremely good. In addition, since the influence of temperature on the residual magnetic flux density (Br) is extremely small, it is possible to achieve a very excellent effect in that it is possible to exhibit high performance.
第１図、第２図および８３図はこの発明の実施例１，２
．３においてそれぞれＭ含有量（β値）による保磁力、
最大エネルギー積および残留磁束密度の温度係数への影
響を調べた結果を示すグラフである。
特許出願人 大同特殊鋼株式会社
代理人弁理士 小 塩 豊1, 2 and 83 are embodiments 1 and 2 of this invention.
．． In 3, the coercive force depending on the M content (β value),
7 is a graph showing the results of investigating the influence of maximum energy product and residual magnetic flux density on temperature coefficient. Patent applicant: Daido Steel Co., Ltd. Representative patent attorney: Yutaka Oshio
Claims (1)
れ、Ｒ１が希土類元素の１種または２種以上、ＭがＴｉ
、Ｚｒ、Ｈｆ、Ｖ、Ｎｂ、Ｔａ、Ｃｒ。 Ｍｏ、Ｗの１種マタは２種以上、ＸがＢ、Ｃ。 Ｎ、Ｓ’ｉ、Ｐの１種または２′、！以上であり、０．
６０≦α≦０．８５、。 ０．０１≦β≦０．１０、 γ＜０．１５ であることを特徴とする永久磁石材料。Formula (1) is represented by R□-ct-β-aFe, Mβxa, where R1 is one or more rare earth elements, and M is Ti.
, Zr, Hf, V, Nb, Ta, Cr. 1 type of Mo, W is 2 or more types, X is B, C. One of N, S'i, P or 2',! That's all, 0.
60≦α≦0.85. A permanent magnetic material characterized in that 0.01≦β≦0.10 and γ<0.15.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP59000261A JPS60144906A (en) | 1984-01-06 | 1984-01-06 | Permanent magnet material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP59000261A JPS60144906A (en) | 1984-01-06 | 1984-01-06 | Permanent magnet material |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS60144906A true JPS60144906A (en) | 1985-07-31 |
Family
ID=11468969
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP59000261A Pending JPS60144906A (en) | 1984-01-06 | 1984-01-06 | Permanent magnet material |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS60144906A (en) |
Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH01219142A (en) * | 1988-02-26 | 1989-09-01 | Sumitomo Special Metals Co Ltd | Rare earth magnetic material excellent in corrosion resistance |
| JPH0257663A (en) * | 1987-09-18 | 1990-02-27 | Asahi Chem Ind Co Ltd | Magnetic anisotropy material and its manufacture |
| JPH03153852A (en) * | 1989-11-13 | 1991-07-01 | Asahi Chem Ind Co Ltd | Magnetic material, magnet composed of the same, and their production |
| US5041171A (en) * | 1986-07-18 | 1991-08-20 | U.S. Philips Corporation | Hard magnetic material |
| US5049208A (en) * | 1987-07-30 | 1991-09-17 | Tdk Corporation | Permanent magnets |
| US5085716A (en) * | 1990-02-20 | 1992-02-04 | General Motors Corporation | Hot worked rare earth-iron-carbon magnets |
| US5135584A (en) * | 1990-09-20 | 1992-08-04 | Mitsubishi Steel Mfg. Co., Ltd. | Permanent magnet powders |
| US5186766A (en) * | 1988-09-14 | 1993-02-16 | Asahi Kasei Kogyo Kabushiki Kaisha | Magnetic materials containing rare earth element iron nitrogen and hydrogen |
| US5217541A (en) * | 1990-05-03 | 1993-06-08 | High End Metals Corp. | Permanent magnet and the method for producing the same |
| US5403407A (en) * | 1993-04-08 | 1995-04-04 | University Of Delaware | Permanent magnets made from iron alloys |
| JP2009249682A (en) * | 2008-04-04 | 2009-10-29 | Nec Tokin Corp | Hard magnetic alloy and method for producing the same |
| US11289249B2 (en) | 2017-08-30 | 2022-03-29 | Kabushiki Kaisha Toshiba | Permanent magnet, rotary electrical machine, and vehicle |
-
1984
- 1984-01-06 JP JP59000261A patent/JPS60144906A/en active Pending
Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5041171A (en) * | 1986-07-18 | 1991-08-20 | U.S. Philips Corporation | Hard magnetic material |
| US5049208A (en) * | 1987-07-30 | 1991-09-17 | Tdk Corporation | Permanent magnets |
| JPH0257663A (en) * | 1987-09-18 | 1990-02-27 | Asahi Chem Ind Co Ltd | Magnetic anisotropy material and its manufacture |
| JPH01219142A (en) * | 1988-02-26 | 1989-09-01 | Sumitomo Special Metals Co Ltd | Rare earth magnetic material excellent in corrosion resistance |
| US5186766A (en) * | 1988-09-14 | 1993-02-16 | Asahi Kasei Kogyo Kabushiki Kaisha | Magnetic materials containing rare earth element iron nitrogen and hydrogen |
| JPH03153852A (en) * | 1989-11-13 | 1991-07-01 | Asahi Chem Ind Co Ltd | Magnetic material, magnet composed of the same, and their production |
| US5085716A (en) * | 1990-02-20 | 1992-02-04 | General Motors Corporation | Hot worked rare earth-iron-carbon magnets |
| US5217541A (en) * | 1990-05-03 | 1993-06-08 | High End Metals Corp. | Permanent magnet and the method for producing the same |
| US5135584A (en) * | 1990-09-20 | 1992-08-04 | Mitsubishi Steel Mfg. Co., Ltd. | Permanent magnet powders |
| US5403407A (en) * | 1993-04-08 | 1995-04-04 | University Of Delaware | Permanent magnets made from iron alloys |
| JP2009249682A (en) * | 2008-04-04 | 2009-10-29 | Nec Tokin Corp | Hard magnetic alloy and method for producing the same |
| US11289249B2 (en) | 2017-08-30 | 2022-03-29 | Kabushiki Kaisha Toshiba | Permanent magnet, rotary electrical machine, and vehicle |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JPS60254708A (en) | Manufacture of permanent magnet | |
| JPS60144909A (en) | Manufacture of permanent magnet material | |
| JPS60144906A (en) | Permanent magnet material | |
| JPS6110209A (en) | Permanent magnet | |
| JPH03236202A (en) | Sintered permanent magnet | |
| JPH01219143A (en) | Sintered permanent magnet material and its production | |
| JPS62136551A (en) | Permanent magnet material | |
| JPS60204862A (en) | Rare earth element-iron type permanent magnet alloy | |
| JPS60144908A (en) | Permanent magnet material | |
| US4954186A (en) | Rear earth-iron-boron permanent magnets containing aluminum | |
| JPS60144907A (en) | Permanent magnet material | |
| JPS6151901A (en) | Manufacture of permanent magnet | |
| JPH0660367B2 (en) | Method of manufacturing permanent magnet material | |
| JPS60257107A (en) | Manufacture of permanent magnet powder and permanent magnet | |
| JPS63128606A (en) | Permanent magnet | |
| JPS6180805A (en) | Permanent magnet material | |
| JPS60254709A (en) | Permanent magnet | |
| JP3178848B2 (en) | Manufacturing method of permanent magnet | |
| JPS62181403A (en) | Permanent magnet | |
| JPS60254707A (en) | Manufacture of permanent magnet | |
| JPS62136550A (en) | Permanent magnet material | |
| JPS62136553A (en) | Permanent magnet material | |
| JPH05211102A (en) | Powder for permanent magnet and permanent magnet | |
| JPS6178102A (en) | Permanent magnet material | |
| JPS59215460A (en) | Permanent magnet material and its production |