JPH0238657B2 - - Google Patents
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- Publication number
- JPH0238657B2 JPH0238657B2 JP54072990A JP7299079A JPH0238657B2 JP H0238657 B2 JPH0238657 B2 JP H0238657B2 JP 54072990 A JP54072990 A JP 54072990A JP 7299079 A JP7299079 A JP 7299079A JP H0238657 B2 JPH0238657 B2 JP H0238657B2
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- Prior art keywords
- magnetic field
- alloy
- isothermal
- field treatment
- max
- Prior art date
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- 229910045601 alloy Inorganic materials 0.000 claims description 28
- 239000000956 alloy Substances 0.000 claims description 28
- 229910052804 chromium Inorganic materials 0.000 claims description 10
- 238000001330 spinodal decomposition reaction Methods 0.000 claims description 6
- 229910052761 rare earth metal Inorganic materials 0.000 claims description 5
- 150000002910 rare earth metals Chemical class 0.000 claims description 5
- 229910052720 vanadium Inorganic materials 0.000 claims description 5
- 229910017313 Mo—Co Inorganic materials 0.000 claims description 3
- 238000001816 cooling Methods 0.000 description 20
- 230000032683 aging Effects 0.000 description 19
- 229910052750 molybdenum Inorganic materials 0.000 description 5
- 238000002844 melting Methods 0.000 description 4
- 230000008018 melting Effects 0.000 description 4
- 229910000521 B alloy Inorganic materials 0.000 description 3
- 238000005266 casting Methods 0.000 description 3
- 239000002994 raw material Substances 0.000 description 3
- 229910052726 zirconium Inorganic materials 0.000 description 3
- 229910000640 Fe alloy Inorganic materials 0.000 description 2
- 239000000654 additive Substances 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 229910017110 Fe—Cr—Co Inorganic materials 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000004134 energy conservation Methods 0.000 description 1
- 230000004907 flux Effects 0.000 description 1
- 230000002431 foraging effect Effects 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 229910001004 magnetic alloy Inorganic materials 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000004904 shortening Methods 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
Landscapes
- Hard Magnetic Materials (AREA)
Description
本発明はスピノーダル分解型磁石合金に関する
もので、特に磁場中時効時間および連続冷却時効
（あるいは多段時効）処理時間が短縮されるこの
種磁石合金に関する。
従来スピノーダル分解型磁石合金としてはFe
−Cr−Co磁石合金が知られており、この合金は、
合金鋳造後、800〜1200℃の温度で溶体化処理を
行なつた後、560〜700℃の温度で磁場中時効（あ
るいは単に等温時効）を行い、その後、580〜400
℃の温度迄冷却する連続冷却時効（あるいは多段
時効）処理を施して永久磁石特性を付与している
が、低Co含有（３〜10wt％Co）合金系になると
磁場中時効時間（あるいは等温時効時間）、およ
びそれにつづく連続冷却時効（あるいは多段時
効）処理時間が長くなる欠点がある。
本発明は、この欠点を除去して上述した熱処理
時間が短かくてすむこの種磁石合金を提供するこ
とを目的とするものである。
本発明は、Fe−Cr−Mo−Co鋳造永久磁石合
金であつて、重量比で15〜35％Cr、15％以下
Mo、１〜６％Co残部実質的にFeとすることによ
つて、等温磁場処理時間を、磁気特性を維持しつ
つ短縮できるようにしたことを特徴とするスピノ
ーダル分解型Fe−Cr−Mo−Co永久磁石合金で
ある。
なお、ここで“残部実質的にFeよりなる”と
の表現は、原料中に不可否的に混入する不純物
（例えばSiやＣ等）を含んでも良いことを意味す
る。例えば、Feの一部とCr原料としてフエクロ
ームを用いることができ、この場合、Siが0.01〜
0.5％含まれ、Ｃが0.01〜0.2含まれる。
また、この合金は、副成分として0.1〜0.9％
Ti、0.01〜0.1％Al、0.02〜2.％希土類ミツシユメ
タル、１〜２％Ｖ、0.5〜２％Siおよび0.05〜２％
Zrの少なくとも一種を添加含有させても良い。
本発明の合金によれば、磁場中時効（あるいは
等温時効）時間が２時間以内で良く、また連続冷
却時効（あるいは多段時効）処理における平均冷
却速度を３℃／時間〜40℃／時間とすることがで
き、熱処理時間を大巾に短縮できる利点がある。
以下に、本発明を実施例について説明する。
実施例 １
26wt％Cr、6wt％Mo、4wt％Co、残実質的に
Fe（以下Ａ合金と呼ぶ）と、26wt％Cr、4wt％
Co、残実質的にFe（以下Ｂ合金と呼ぶ）とを、そ
れぞれ真空溶解して、シエル鋳型で５mmφ×40mm
Ｌの合金試料を鋳造し、その後、これらの試料を
1000℃で１時間の溶体化処理を行なつた後、等温
磁場処理を、Ａ合金の場合590℃、Ｂ合金の場合
は600℃の温度で0.5時間、１時間および２時間に
わたつて施し、その後、570℃から、冷却速度１
℃／時間、３℃／時間、５℃／時間をもつて、
400℃迄連続冷却時効を行なつて磁気特性を測定
した。その結果を、Ａ合金については第１図に、
Ｂ合金については第２図に示す。
両図から明かなように、本発明によるＡ合金で
は、従来のＢ合金に比して、等温磁場処理時間が
２時間以内で時効処理の冷却速が３℃／時間で
も、充分な残留磁束密度（Br）と高い保磁力
（Hc）や最大エネルギー積（（BH）max）を示
す。即ち、Ｂ合金のように、等温磁場処理時間が
２時間以上、時効冷却速度を１℃／時間のような
ゆつくりした冷却速度とする必要がない。
実施例 ２
xwt％Cr、6wt％Mo、4wt％Co、残実質的に
Feよりなる合金試料を、ｘが10、15、20、35、
40として、実施例１と同様に真空溶解して５mmφ
×40mmＬにシエル鋳型で鋳造し、これらの合金試
料を1000℃で１時間溶体化処理を行なつた後、
570〜630℃の温度で１時間の等温磁場処理をし、
その後、570℃から400℃迄３℃／時間の冷却速度
で連続冷却時効を行いその磁気特性を測定した。
ｘ＝10では、等温磁場処理温度625℃で、Br＝
3KG、
Hc＝50Oe、（BH）max＝0.05MGOeであり、
ｘ＝15では、等温磁場処理温度625℃で、Br＝
16KG、
Hc＝300Oe、（BH）max＝2MGOe、であり、
ｘ＝20では、等温磁場処理温度600℃で、Br＝
14KG、
Hc＝600Oe（BH）max＝5.5MGOe、ｘ＝35で
は、等温磁場処理温度575℃で、Br＝8KG、
Hc＝800Oe、（BH）max＝3MGOeであつた。
しかし、ｘ＝40では、等温磁場処理温度570℃と
したが、Brが1KG以下という不満足な磁気特性
を得られたにすぎなかつた。従つて、ｘは15〜35
が安定な磁気特性を示す範囲であることがわか
る。
実施例 ３
26wt％Cr、ywt％Mo、4wt％Co残実質的にFe
よりなる合金試料を、ｙが0.001、２、４、６、
８、10、14、18、20として、実施例１と同様に、
真空溶解し、５mmφ×40mmにＬにシエル鋳型で鋳
造し、これらの合金試料を1000℃で１時間の溶体
化処理を施し、570゜〜600℃の温度で１時間の等
温磁場処理を行ない、その後、570℃から400℃ま
で、冷却速度３℃／時間で、冷却して、磁気特性
を測定した。ｙ＝0.001では、等温磁場処理温度
600℃で、Br＝13.5KG、Hc＝500Oe、（BH）
max＝4MGOe、ｙ＝２では、等温磁場処理温度
600℃で、Br＝13KG、
Hc＝570Oe、（BH）max＝4MGOe、ｙ＝４で
は、等温磁場処理温度595℃で、Br＝12.8KG、
Hc＝630Oe、（BH）max＝5.5MGOe、ｙ＝６で
は、等温磁場処理温度590℃で、Br＝12.5KG、
Hc＝700Oe（BH）max＝6.5MGOe、ｙ＝８で
は、等温磁場処理温度585℃で、Br＝12.0KG、
Hc＝720Oe、（BH）max＝6MGOe、ｙ＝10で
は、等温磁場処理温度580℃で、Br＝11KG、Hc
＝730Oe、（BH）max＝4MGOe、ｙ＝14では、
等温磁場処理温度が575℃で、Br＝10KG、
Hcw750Oe、（BH）max＝3.5MGOe、ｙ＝18
では、等温磁場処理温度570℃で、Br＝9KG、
Hc＝800Oe、（BH）max＝3MGOe、ｙ＝20で
は、等温磁場処理温度570℃で、Br＝7KG、Hc
＝820Oe、（BH）max＝2MGOeを示した。しか
し、ｙ＝18以上では、鋳造段階で試料が割れるの
で、事実上製造困難である。従つて、ｙは、
0.001〜16の範囲であることがわかる。
実施例 ４
26wt％Cr、6wt％Mo、zwt％Co、残実質的に
Feよりなる合金試料を、ｚが０、２、４、６、
８、10、12として、実施例１と同様に真空溶解
し、５mmφ×40mmにＬにシエル鋳型で鋳造し、こ
れらの合金試料を1000℃で１時間の溶体化処理を
施し、570℃〜630℃の温度で１時間の等温磁場処
理を行ない、その後、570℃から400℃まで、冷却
速度３℃／時間で連続冷却を行なつて、磁気特性
を測定した。
ｚ＝０では、等温磁場処理温度570℃で、Br＝
12.5KG、Hc＝640Oe、（BH）max＝4MGOe、
ｚ＝２では、等温磁場処理温度575℃で、Br＝
12.5KG、He＝660Oe、（BH）max＝6MGOe、
ｚ＝４では、等温磁場処理温度580℃で、Br＝
12.5KG、Hc＝700Oe、（BH）max＝6.5MGOe、
ｚ＝６では、等温磁場処理温度590℃で、Br＝
12.7KG、Hc＝710Oe、（BH）max＝6.8MGOe、
ｚ＝８では、等温磁場処理温度600℃で、Br＝
12.5KG、Hc＝720Oe、（BH）max＝5.5MGOe、
ｚ＝10では、等温磁場処理温度620℃で、Br＝
13KG、Hc＝730Oe、（BH）max＝6MGOe、
ｚ＝12では、等温磁場処理温度630℃で、Br＝
12.8KG、Hc＝740.Oe、（BH）max＝5.5MGOe
を示した。しかし、ｚ＝８以上では、冷間加工等
の磁石製品成形工程に於て、望ましくないσ相が
析出しやすくこのため加工上の問題が生じる。こ
の観点から磁気特性および加工性の両者を共に満
足させるためには、Coは、6wt％以下としなけれ
ばならない。
実施例 ５
26wt％Cr、6wt％Mo、4wt％Co、残実質的に
Feよりなる主成分に(a)、0.5wt％Ti、(b)0.05wt％
Al、(c)0.1wt％希土類ミツシユメタル、(d)1.5wt
％Ｖ、(e)0.6wt％Si、(f)0.1wt％Zrをそれぞれ添加
して、大気溶解し、シエル鋳型で５mmφ×40mmＬ
に鋳造して合金試料を得、1000℃で１時間の溶体
化処理を施し、590℃の温度で１時間の等温磁場
処理を行なつた後、570℃から400℃まで、冷却速
度３℃／時間で、連続冷却を行なつて、その磁気
特性を測定したところ、実施例１の合金Ａと同様
の特性を得た。その結果を第１表に示す。
The present invention relates to a spinodal decomposition type magnet alloy, and particularly to this type of magnet alloy in which the aging time in a magnetic field and the continuous cooling aging (or multistage aging) treatment time are shortened. The conventional spinodal decomposition type magnet alloy is Fe.
-Cr-Co magnet alloy is known, and this alloy is
After casting the alloy, it is subjected to solution treatment at a temperature of 800 to 1200°C, then aged in a magnetic field (or simply isothermal aging) at a temperature of 560 to 700°C, and then aged at a temperature of 580 to 400°C.
Permanent magnetic properties are imparted by continuous cooling aging (or multi-stage aging) that cools the alloy to a temperature of There is a disadvantage that the continuous cooling aging (or multi-stage aging) treatment time is long. The object of the present invention is to eliminate this drawback and provide a magnet alloy of this type which requires a short heat treatment time as described above. The present invention is a Fe-Cr-Mo-Co cast permanent magnet alloy, which has a weight ratio of 15 to 35% Cr and 15% or less.
A spinodal decomposition type Fe-Cr-Mo- characterized in that the isothermal magnetic field treatment time can be shortened while maintaining the magnetic properties by making Mo, 1 to 6% Co the balance substantially Fe. Co permanent magnet alloy. Note that the expression "the remainder substantially consists of Fe" herein means that impurities (for example, Si, C, etc.) that are inevitably mixed into the raw material may be included. For example, Fechrome can be used as a part of Fe and Cr raw material, and in this case, Si is 0.01~
Contains 0.5% and 0.01 to 0.2 C. This alloy also has 0.1-0.9% as a subcomponent.
Ti, 0.01-0.1% Al, 0.02-2.% rare earth metal, 1-2% V, 0.5-2% Si and 0.05-2%
At least one type of Zr may be added. According to the alloy of the present invention, the aging time in a magnetic field (or isothermal aging) may be within 2 hours, and the average cooling rate in continuous cooling aging (or multistage aging) treatment is 3°C/hour to 40°C/hour. This has the advantage of greatly shortening the heat treatment time. The present invention will be described below with reference to Examples. Example 1 26wt%Cr, 6wt%Mo, 4wt%Co, remaining substantially
Fe (hereinafter referred to as A alloy), 26wt%Cr, 4wt%
Co and the remaining substantially Fe (hereinafter referred to as B alloy) were melted in vacuum and molded into a shell mold of 5 mmφ x 40 mm.
L alloy samples were cast, and then these samples were
After solution treatment at 1000°C for 1 hour, isothermal magnetic field treatment was performed at a temperature of 590°C for A alloy and 600°C for B alloy for 0.5 hour, 1 hour and 2 hours, Then, from 570℃, cooling rate 1
℃/hour, 3℃/hour, 5℃/hour,
The magnetic properties were measured after continuous cooling aging to 400℃. The results are shown in Figure 1 for alloy A.
Alloy B is shown in Figure 2. As is clear from both figures, compared to the conventional B alloy, the A alloy according to the present invention has a sufficient residual magnetic flux density even when the isothermal magnetic field treatment time is within 2 hours and the aging treatment cooling rate is 3°C/hour. (Br), exhibits high coercive force (Hc) and maximum energy product ((BH)max). That is, unlike alloy B, it is not necessary to set the isothermal magnetic field treatment time to 2 hours or more and the aging cooling rate to a slow cooling rate such as 1° C./hour. Example 2 xwt%Cr, 6wt%Mo, 4wt%Co, remaining substantially
For alloy samples made of Fe, x is 10, 15, 20, 35,
40, vacuum melted as in Example 1 to obtain 5mmφ
x40mmL with a shell mold, and after solution treatment of these alloy samples at 1000℃ for 1 hour,
Isothermal magnetic field treatment at a temperature of 570-630℃ for 1 hour,
Thereafter, continuous cooling aging was performed from 570°C to 400°C at a cooling rate of 3°C/hour, and the magnetic properties were measured.
At x=10, at an isothermal magnetic field treatment temperature of 625℃, Br=
3KG, Hc=50Oe, (BH)max=0.05MGOe,
At x=15, at an isothermal magnetic field treatment temperature of 625℃, Br=
16KG, Hc=300Oe, (BH)max=2MGOe,
At x=20, at an isothermal magnetic field treatment temperature of 600℃, Br=
At 14KG, Hc = 600Oe, (BH)max = 5.5MGOe, and x = 35, Br = 8KG, Hc = 800Oe, (BH)max = 3MGOe at an isothermal magnetic field treatment temperature of 575°C.
However, when x=40, the isothermal magnetic field treatment temperature was set at 570°C, but only unsatisfactory magnetic properties such as Br of 1 KG or less were obtained. Therefore, x is 15 to 35
It can be seen that this is a range that exhibits stable magnetic properties. Example 3 26wt%Cr, ywt%Mo, 4wt%Co remaining substantially Fe
Alloy samples with y of 0.001, 2, 4, 6,
8, 10, 14, 18, 20, as in Example 1,
The alloy samples were melted in vacuum and cast in a shell mold to a size of 5 mmφ x 40 mm using a shell mold. These alloy samples were subjected to solution treatment at 1000°C for 1 hour, and then subjected to isothermal magnetic field treatment at a temperature of 570° to 600°C for 1 hour. Thereafter, it was cooled from 570°C to 400°C at a cooling rate of 3°C/hour, and its magnetic properties were measured. At y=0.001, the isothermal magnetic field treatment temperature
At 600℃, Br=13.5KG, Hc=500Oe, (BH)
At max=4MGOe, y=2, isothermal magnetic field treatment temperature
At 600℃, Br=13KG, Hc=570Oe, (BH)max=4MGOe, y=4, isothermal magnetic field treatment temperature 595℃, Br=12.8KG,
Hc=630Oe, (BH)max=5.5MGOe, y=6, isothermal magnetic field treatment temperature 590℃, Br=12.5KG, Hc=700Oe (BH)max=6.5MGOe, y=8, isothermal magnetic field treatment temperature At 585℃, Br=12.0KG, Hc=720Oe, (BH)max=6MGOe, y=10, at isothermal magnetic field treatment temperature 580℃, Br=11KG, Hc
=730Oe, (BH)max=4MGOe, y=14,
Isothermal magnetic field treatment temperature is 575℃, Br=10KG, Hcw750Oe, (BH)max=3.5MGOe, y=18
Then, at isothermal magnetic field treatment temperature 570℃, Br = 9KG, Hc = 800Oe, (BH)max = 3MGOe, y = 20, at isothermal magnetic field treatment temperature 570℃, Br = 7KG, Hc
= 820Oe, (BH)max = 2MGOe. However, if y=18 or more, the sample will crack during the casting stage, making it practically difficult to manufacture. Therefore, y is
It can be seen that the range is from 0.001 to 16. Example 4 26wt%Cr, 6wt%Mo, zwt%Co, remaining substantially
Alloy samples made of Fe were prepared with z of 0, 2, 4, 6,
Samples 8, 10, and 12 were vacuum melted in the same manner as in Example 1, and cast into a 5 mmφ x 40 mm L shape using a shell mold. An isothermal magnetic field treatment was carried out for 1 hour at a temperature of 570°C and then continuous cooling was performed from 570°C to 400°C at a cooling rate of 3°C/hour, and the magnetic properties were measured. At z=0, at an isothermal magnetic field treatment temperature of 570℃, Br=
12.5KG, Hc=640Oe, (BH)max=4MGOe, z=2, isothermal magnetic field treatment temperature 575℃, Br=
12.5KG, He=660Oe, (BH)max=6MGOe, z=4, isothermal magnetic field treatment temperature 580℃, Br=
12.5KG, Hc=700Oe, (BH)max=6.5MGOe, z=6, isothermal magnetic field treatment temperature 590℃, Br=
12.7KG, Hc=710Oe, (BH)max=6.8MGOe, z=8, isothermal magnetic field treatment temperature 600℃, Br=
12.5KG, Hc=720Oe, (BH)max=5.5MGOe, z=10, isothermal magnetic field treatment temperature 620℃, Br=
13KG, Hc=730Oe, (BH)max=6MGOe, z=12, isothermal magnetic field treatment temperature 630℃, Br=
12.8KG, Hc=740.Oe, (BH)max=5.5MGOe
showed that. However, when z=8 or more, undesirable σ phase tends to precipitate during magnetic product forming processes such as cold working, which causes processing problems. From this point of view, in order to satisfy both magnetic properties and workability, Co must be contained at 6 wt% or less. Example 5 26wt%Cr, 6wt%Mo, 4wt%Co, remaining substantially
The main component is Fe (a), 0.5wt% Ti, (b) 0.05wt%
Al, (c) 0.1wt% rare earth metal, (d) 1.5wt
%V, (e) 0.6wt%Si, and (f) 0.1wt%Zr were added, dissolved in the atmosphere, and molded into 5mmφ×40mmL in a shell mold.
An alloy sample was obtained by casting at 1,000°C, solution treatment was performed at 1000°C for 1 hour, and an isothermal magnetic field treatment was performed at a temperature of 590°C for 1 hour, followed by a cooling rate of 3°C/3°C from 570°C to 400°C. When the magnetic properties were measured after continuous cooling for several hours, the same properties as Alloy A of Example 1 were obtained. The results are shown in Table 1.
【表】
即ち、(a)〜(f)の添加物を加えることにより、大
気溶解で、磁石特性を劣化させることなく、磁石
合金を得ることができる。なお、各添加物の量
は、塑性加工性および磁気特性の点で重量比にし
て、0.1〜0.9％Ti、0.01〜0.1％Al、0.02〜２％希
土類ミツシユメタル、１〜２％Ｖ、0.5〜0.2％Si、
0.05〜２％Zrの範囲に限定される。即ち、Tiは１
％以上であると、そ性加工性が悪くなり、0.1％
以下では磁気特性が真空溶解時以下となる。Al、
希土類ミツシユメタル、Ｖ、Zrについては、上
述の値の範囲外では磁気特性が真空溶解による場
合よりも悪くなる。Siも上述の範囲内で、溶解時
の湯流れを向上させ、かつ磁気特性を向上させ
る。なお、Siは原料中に不可避的に混入するSiの
量とは無関係に上述の量だけ添加されるものとす
る。
以上、本発明を特定の実施例について説明した
が、本発明では、Fe−Cr−CoにMoを含有した
Fe−Cr−Mo−Co系スピノーダル分解型永久磁
石であり、磁場中時効の処理時間の短縮および連
続冷却時効あるいは多段冷却時効処理の冷却速度
を早めることを可能にし、この結果処理工程が短
縮し、コストも低減できるとともに省エネルギー
の要求にもかなうものである。[Table] That is, by adding the additives (a) to (f), a magnetic alloy can be obtained by atmospheric melting without deteriorating the magnetic properties. In terms of plastic workability and magnetic properties, the amounts of each additive are 0.1-0.9% Ti, 0.01-0.1% Al, 0.02-2% rare earth metal, 1-2% V, and 0.5-0.5% by weight. 0.2%Si,
It is limited to a range of 0.05 to 2% Zr. That is, Ti is 1
If it is more than 0.1%, the processability will be poor.
Below, the magnetic properties will be lower than those of vacuum melting. Al,
For rare earth metals, V, and Zr, outside the above-mentioned value range, the magnetic properties become worse than those obtained by vacuum melting. Within the above-mentioned range, Si also improves melt flow during melting and improves magnetic properties. Note that Si is added in the above amount regardless of the amount of Si that is inevitably mixed into the raw material. The present invention has been described above with reference to specific examples, but in the present invention, Fe-Cr-Co contains Mo.
Fe-Cr-Mo-Co spinodal decomposition type permanent magnet, which makes it possible to shorten the processing time for aging in a magnetic field and accelerate the cooling rate for continuous cooling aging or multi-stage cooling aging, resulting in a shorter processing process. , it is possible to reduce costs and meet the requirements for energy conservation.
第１図は、26wt％Cr−6wt％Mo−4wt％Co−
残Fe合金の等温磁場処理時間に対する時効冷却
速度別の磁気特性の変化を示したグラフであり、
第２図は、26wt％のCr−4wt％Co−残Fe合金の
第１図と同様のグラフである。
Figure 1 shows 26wt%Cr-6wt%Mo-4wt%Co-
It is a graph showing changes in magnetic properties according to aging cooling rate with respect to isothermal magnetic field treatment time of residual Fe alloy,
FIG. 2 is a graph similar to FIG. 1 for a 26 wt% Cr-4 wt% Co-remaining Fe alloy.
Claims (1)
ず）Mo、１〜６％Co、残部実質的にFeよりな
り、等温磁場処理時間を、磁気特性を維持しつつ
短縮できるようにしたことを特徴とするスピノー
ダル分解型Fe−Cr−Mo−Co永久磁石合金。 ２ 重量比で15〜35％Crと、０〜15％（０は含
まず）Moと、１〜６％Coと、0.1〜0.9％Ti、
0.01〜0.1％Al、0.02〜２％希土類ミツシユメタ
ル、１〜２％Ｖ、0.5〜２％Siおよび0.05〜２％
Zrの群より選ばれた少なくとも一種と、残部実
質的にFeとよりなり、等温磁場処理時間を、磁
気特性を維持しつつ短縮できるようにしたことを
特徴とするスピノーダル分解型Fe−Cr−Mo−
Co永久磁石合金。[Claims] 1 Consisting of 15 to 35% Cr, 0 to 15% (not including 0) Mo, 1 to 6% Co, and the balance substantially Fe in terms of weight ratio, and the isothermal magnetic field treatment time is determined by the magnetic properties. A spinodal decomposition type Fe-Cr-Mo-Co permanent magnet alloy characterized by being able to shorten while maintaining. 2 Weight ratio: 15-35% Cr, 0-15% (not including 0) Mo, 1-6% Co, 0.1-0.9% Ti,
0.01-0.1% Al, 0.02-2% rare earth metal, 1-2% V, 0.5-2% Si and 0.05-2%
A spinodal decomposition type Fe-Cr-Mo characterized by consisting of at least one selected from the group of Zr and the remainder substantially Fe, making it possible to shorten the isothermal magnetic field treatment time while maintaining magnetic properties. −
Co permanent magnet alloy.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP7299079A JPS56254A (en) | 1979-06-12 | 1979-06-12 | Spinodal decomposition type fe-cr-mo-co permanent magnet alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP7299079A JPS56254A (en) | 1979-06-12 | 1979-06-12 | Spinodal decomposition type fe-cr-mo-co permanent magnet alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS56254A JPS56254A (en) | 1981-01-06 |
| JPH0238657B2 true JPH0238657B2 (en) | 1990-08-31 |
Family
ID=13505341
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP7299079A Granted JPS56254A (en) | 1979-06-12 | 1979-06-12 | Spinodal decomposition type fe-cr-mo-co permanent magnet alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS56254A (en) |
Families Citing this family (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS57149456A (en) * | 1981-03-10 | 1982-09-16 | Sumitomo Special Metals Co Ltd | Dendritic fe-cr-co magnet alloy |
| US4601876A (en) * | 1981-08-31 | 1986-07-22 | Sumitomo Special Metals Co., Ltd. | Sintered Fe-Cr-Co type magnetic alloy and method for producing article made thereof |
| JP2616085B2 (en) * | 1990-01-25 | 1997-06-04 | 日産自動車株式会社 | Actuating pressure control actuator for fluid pressure actuation system |
| JPH03279062A (en) * | 1990-03-28 | 1991-12-10 | Nissan Motor Co Ltd | Operating pressure control actuator for fluid pressure operating system |
| JP2534801B2 (en) * | 1990-12-28 | 1996-09-18 | 凸版印刷株式会社 | Liquid filling device |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS4920451A (en) * | 1972-06-23 | 1974-02-22 | ||
| JPS5118884A (en) * | 1974-06-25 | 1976-02-14 | Amp Inc | Denkisetsutenno kairyo |
| JPS5273120A (en) * | 1975-12-16 | 1977-06-18 | Nippon Telegr & Teleph Corp <Ntt> | Preparation of magnetic materials |
-
1979
- 1979-06-12 JP JP7299079A patent/JPS56254A/en active Granted
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS4920451A (en) * | 1972-06-23 | 1974-02-22 | ||
| JPS5118884A (en) * | 1974-06-25 | 1976-02-14 | Amp Inc | Denkisetsutenno kairyo |
| JPS5273120A (en) * | 1975-12-16 | 1977-06-18 | Nippon Telegr & Teleph Corp <Ntt> | Preparation of magnetic materials |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS56254A (en) | 1981-01-06 |
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