JPH0319682B2 - - Google Patents
Info
- Publication number
- JPH0319682B2 JPH0319682B2 JP12678182A JP12678182A JPH0319682B2 JP H0319682 B2 JPH0319682 B2 JP H0319682B2 JP 12678182 A JP12678182 A JP 12678182A JP 12678182 A JP12678182 A JP 12678182A JP H0319682 B2 JPH0319682 B2 JP H0319682B2
- Authority
- JP
- Japan
- Prior art keywords
- thin plate
- core
- case
- adhesive
- convex
- 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.)
- Expired
Links
- 239000011162 core material Substances 0.000 description 34
- 239000000463 material Substances 0.000 description 21
- 239000000853 adhesive Substances 0.000 description 17
- 230000001070 adhesive effect Effects 0.000 description 17
- 229910045601 alloy Inorganic materials 0.000 description 16
- 239000000956 alloy Substances 0.000 description 16
- 239000013078 crystal Substances 0.000 description 16
- 238000005452 bending Methods 0.000 description 12
- 238000010791 quenching Methods 0.000 description 8
- 238000010586 diagram Methods 0.000 description 7
- 238000000034 method Methods 0.000 description 7
- 239000000155 melt Substances 0.000 description 6
- 238000010438 heat treatment Methods 0.000 description 5
- 229910000702 sendust Inorganic materials 0.000 description 5
- 229910017082 Fe-Si Inorganic materials 0.000 description 4
- 229910017133 Fe—Si Inorganic materials 0.000 description 4
- 238000010030 laminating Methods 0.000 description 4
- 238000003475 lamination Methods 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 4
- 238000000227 grinding Methods 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 238000005498 polishing Methods 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- 229910001030 Iron–nickel alloy Inorganic materials 0.000 description 2
- 230000004907 flux Effects 0.000 description 2
- 239000000696 magnetic material Substances 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 230000035699 permeability Effects 0.000 description 2
- 229910018125 Al-Si Inorganic materials 0.000 description 1
- 229910001017 Alperm Inorganic materials 0.000 description 1
- 229910018520 Al—Si Inorganic materials 0.000 description 1
- 229910020711 Co—Si Inorganic materials 0.000 description 1
- 229910000976 Electrical steel Inorganic materials 0.000 description 1
- 229910052688 Gadolinium Inorganic materials 0.000 description 1
- 229910000990 Ni alloy Inorganic materials 0.000 description 1
- 229910000676 Si alloy Inorganic materials 0.000 description 1
- 229910018619 Si-Fe Inorganic materials 0.000 description 1
- 229910008289 Si—Fe Inorganic materials 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 229920006332 epoxy adhesive Polymers 0.000 description 1
- 229910052735 hafnium Inorganic materials 0.000 description 1
- 239000001307 helium Substances 0.000 description 1
- 229910052734 helium Inorganic materials 0.000 description 1
- SWQJXJOGLNCZEY-UHFFFAOYSA-N helium atom Chemical compound [He] SWQJXJOGLNCZEY-UHFFFAOYSA-N 0.000 description 1
- 239000011261 inert gas Substances 0.000 description 1
- 238000002347 injection Methods 0.000 description 1
- 239000007924 injection Substances 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 239000005300 metallic glass Substances 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 238000003672 processing method Methods 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 229910052718 tin Inorganic materials 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
- 238000004804 winding Methods 0.000 description 1
- 229910052725 zinc Inorganic materials 0.000 description 1
Classifications
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F41/00—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties
- H01F41/02—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets
- H01F41/0206—Manufacturing of magnetic cores by mechanical means
Landscapes
- Engineering & Computer Science (AREA)
- Power Engineering (AREA)
- Manufacturing & Machinery (AREA)
- Magnetic Heads (AREA)
Description
【発明の詳細な説明】
本発明は、例えば融体超急冷法を採用すること
により、特に磁気ヘツド、トランス等のコア材を
形成する場合に好適な材料としての軟磁性薄板に
関する。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a soft magnetic thin plate as a material suitable for forming a core material of a magnetic head, a transformer, etc., by employing, for example, a melt ultra-quenching method.
従来、テープ・レコーダに用いる磁気ヘツド、
トランス等のコア材にセンダスト合金、アルパー
ム合金、高珪素鋼などの硬くて脆い軟磁性材料を
用いる場合には研削などの方法でブロツクからコ
ア材を切り出したり、研磨加工、ラツピング加工
を経てコア材を製造していた。しかしこの方法で
は、生産性が著しく悪くなつて加工費が高くな
り、しかも製作できるコア材の板厚も加工上から
制限されることになる。 Traditionally, magnetic heads used in tape recorders,
When using hard and brittle soft magnetic materials such as Sendust alloy, Alperm alloy, and high-silicon steel for the core material of transformers, etc., the core material is cut out from the block using methods such as grinding, or processed through polishing and wrapping. was manufacturing. However, with this method, productivity is significantly reduced and processing costs are increased, and furthermore, the thickness of the core material that can be manufactured is also limited from the viewpoint of processing.
これらの欠点を解決するために最近では硬くて
脆い材料の薄板加工法として融体超急冷法が採用
されるようになつた。 In order to solve these drawbacks, the melt super-quenching method has recently been adopted as a thin plate processing method for hard and brittle materials.
しかし融体超急冷法によつて得られる薄板は、
一般的に連続した状態で加熱用の容器からノズル
によつて噴出されるものであり、その断面に凹凸
面を生じていた。この場合、磁気ヘツド、トラン
スなどのコア材として使用する場合には、薄板を
積層してラミネート・コア形状としたり、トロイ
ダル・コアのように、リングに巻き付けたりして
製造していた。さらに種々のコア形状を形成する
ためにプレス加工や研削加工、研磨加工などを施
こしていた。そして上記のような、プレス加工、
研削加工、研磨加工などの負荷を与えた場合に、
凹面形の断面形状をした薄板では破断してしまう
欠点があつた。 However, the thin plate obtained by the melt ultra-quenching method is
Generally, it is continuously ejected from a heating container through a nozzle, and its cross section has an uneven surface. In this case, when used as a core material for magnetic heads, transformers, etc., it was manufactured by laminating thin plates to form a laminate core shape, or by winding it around a ring like a toroidal core. Furthermore, in order to form various core shapes, pressing, grinding, polishing, etc. were performed. And as mentioned above, press processing,
When applying a load such as grinding or polishing,
A thin plate with a concave cross-sectional shape had the disadvantage of breaking.
またコア材を接着剤を用いて積層することによ
りラミネート・コアを製造する場合、積層時の加
圧により接着剤がラミネート・コアの外部に濾み
出易い。この為、ラミネート・コアの製造として
の特に厚さの管理が困難で特にコア材相互の接着
力が弱い欠点がある。 Furthermore, when a laminate core is manufactured by laminating core materials using an adhesive, the adhesive tends to leak out of the laminate core due to the pressure applied during lamination. For this reason, it is difficult to control the thickness especially when manufacturing the laminate core, and there is a drawback that the adhesion between the core materials is particularly weak.
本発明は上述の如き点に鑑みてなされたもの
で、その目的とするところは長さ方向に垂直な断
面形状を凸面形としたことにより機械的に強く、
また積層した場合の占積率が高く、材料本来の性
能、例えば磁束密度、透磁率などの性能を活かす
ことができ、また積層の際に用いる接着材の厚さ
が均一で薄くできるので接着力が強く、剥離等の
トラブルが少ない軟磁性薄板を提供するのにあ
る。 The present invention has been made in view of the above-mentioned points, and its purpose is to provide mechanical strength by making the cross-sectional shape perpendicular to the length direction convex.
In addition, the space factor when laminated is high, and the inherent properties of the material, such as magnetic flux density and magnetic permeability, can be utilized.Also, the thickness of the adhesive used during lamination can be made uniform and thin, resulting in adhesive strength. The object of the present invention is to provide a soft magnetic thin plate that is strong and has fewer problems such as peeling.
以下本発明の詳細を図面に従つて説明する。 The details of the present invention will be explained below with reference to the drawings.
第１図は、本発明を実施するのに使用する融体
超急冷装置０の一例を示したもので、この融体超
急冷装置０は、溶融母材２をヒータＨによつて加
熱、溶融するための耐熱容器１と、この溶融母材
２をローラ３，３に噴出するように耐熱容器１の
先端に設けられたノズル１Ａとから形成される。 FIG. 1 shows an example of a melt super-quenching device 0 used to carry out the present invention. This melt super-quenching device 0 heats a molten base material 2 with a heater H to melt it. The molten base material 2 is formed of a heat-resistant container 1 and a nozzle 1A provided at the tip of the heat-resistant container 1 so as to spray the molten base material 2 onto rollers 3, 3.
そして耐熱容器１によつて熱された溶融母材２
をノズル１Ａからロール３，３に噴出して超急冷
法により、薄板４を得るが、薄板４の寸法及び断
面形状は、溶融母材温度、射出速度、ローラ径、
回転速度などの諸条件で決まる。 Then, the molten base material 2 heated by the heat-resistant container 1
is injected from the nozzle 1A onto the rolls 3, 3 to obtain a thin plate 4 by an ultra-quenching method. The dimensions and cross-sectional shape of the thin plate 4 are determined by the molten base material temperature, injection speed, roller diameter,
Determined by various conditions such as rotation speed.
溶融母材２の温度を低くし、回転速度を速くし
て均一に冷却すると、第２図および第３図に示す
ように長さ方向に垂直な断面形状が凸面形の軟磁
性薄帯に製造される。ここで、凸面形とは、断面
での中心点Ａにおける厚さD0と、薄板４の全幅
Ｌの1/4離れた点Ｂの厚さｄとの比D0／ｄが１以
上のものをいう。 When the temperature of the molten base material 2 is lowered and the rotational speed is increased to cool it uniformly, a soft magnetic ribbon with a convex cross section perpendicular to the length direction is produced as shown in Figures 2 and 3. be done. Here, a convex shape is one in which the ratio D 0 /d of the thickness D 0 at the center point A in the cross section and the thickness d at a point B 1/4 of the total width L of the thin plate 4 is 1 or more. means.
逆に、溶融母材温度が高く、ローラ３，３の回
転速度を遅くさせた場合には、断面形状が凹面形
になる。また溶融母材温度と、ローラ３，３の回
転速度とが上記凸面形と凹面形との中間である場
合には、薄板４の断面形状として矩形のものが得
られる。 Conversely, when the temperature of the molten base material is high and the rotational speed of the rollers 3, 3 is slowed down, the cross-sectional shape becomes concave. Further, when the temperature of the molten base material and the rotational speed of the rollers 3, 3 are intermediate between the convex shape and the concave shape, the cross-sectional shape of the thin plate 4 is rectangular.
そして溶融母材２としてセンダスト合金（Al
−Si−Fe合金）で上記凸面形が得られる条件は、
ロール３，３の径が100mmφの場合、溶融母材温
度1250℃〜1600℃、回転数400〜2000r.p.mの範囲
である。 As the molten base material 2, sendust alloy (Al
-Si-Fe alloy), the conditions for obtaining the above convex shape are as follows:
When the diameter of the rolls 3, 3 is 100 mmφ, the molten base material temperature is in the range of 1250° C. to 1600° C., and the rotation speed is in the range of 400 to 2000 rpm.
またFe−Si系合金では溶融母材２温度は1350
℃〜1600℃、回転数600〜1500r.p.mである。 In addition, for Fe-Si alloys, the molten base metal 2 temperature is 1350
℃~1600℃, rotation speed 600~1500r.pm.
また薄板４の断面形状を第３図のように、中心
における点Ａでの厚さD0および中心から全幅Ｌ
の1/4、離れた点Ｂでの厚さｄで表わしたとき、
曲げ強度の形状依存性は第４図に示すようにな
る。ここで曲げ強度は棒に薄板４を巻き付けたと
き、破断しない最小半径によつて表わされる。 In addition, the cross-sectional shape of the thin plate 4 is as shown in Fig. 3, with a thickness D 0 at a point A at the center and a total width L from the center.
When expressed as 1/4 of the thickness d at a distant point B,
The shape dependence of bending strength is shown in FIG. Here, the bending strength is expressed by the minimum radius at which the thin plate 4 will not break when it is wrapped around a rod.
第４図からD0／ｄが大きいほど、すなわち凸
面形の方が曲げ強度が良いことが明らかである。
これは、加熱容器１からローラ３，３に噴出され
た溶融母材２が、ローラ３，３から離れる瞬間
に、十分に冷却された薄板４になつているため
に、内部歪が凹面形にした場合よりも小さいこと
と、冷却速度が速いことにより結晶粒径が小さい
ことに起因していると思われる。 It is clear from FIG. 4 that the larger D 0 /d, that is, the convex shape, has better bending strength.
This is because the molten base material 2 ejected from the heating container 1 to the rollers 3, 3 becomes a sufficiently cooled thin plate 4 at the moment it leaves the rollers 3, 3, so that the internal strain becomes concave. It is thought that this is due to the fact that the crystal grain size is smaller than that in the case where the crystal grain size is smaller than that in the case where the crystal grain size is smaller than that in the case where the crystal grain size is lower than that in the case where the crystal grain size is lower than that in the case where the crystal grain size is lower than that in the case where the crystal grain size is lower than that in the case where the crystal grain size is lower than that in the case where the crystal grain size is lower than that in the case where the crystal grain size is lower than that in the case where the crystal grain size is lower than that in the case where the crystal grain size is lower than that in the case where the crystal grain size is lower than that in the case where the crystal grain size is lower than that in the case where the crystal grain size is lower than that in the case where the crystal grain size is lower.
コア材を製造する場合には、軟磁性材料で製造
された断面凸面形の薄板４から、縦スタガー取り
（第８図参照）、横スタガー取り（第９図参照）、
縦平行取り（第１０図参照）、横平行取り（第１
１図参照）によつてコア取りを行ない、コア材を
形成する。曲げ強度が良いことは、取り扱い易い
だけではなく、トロイダルコアに使用する場合に
は径が小さくて済み、小型化できる。 When manufacturing the core material, from a thin plate 4 made of soft magnetic material and having a convex cross section, vertical stagger removal (see Fig. 8), horizontal stagger removal (see Fig. 9),
Vertical parallel (see Figure 10), horizontal parallel (1st)
1) to form a core material. Having good bending strength not only makes it easier to handle, but also allows for smaller diameters when used in toroidal cores, allowing for miniaturization.
更に第６図に示すように凸面形のコア材５を接
着剤６を用いて接着して積層したことによつて形
成されるラミネート・コアは、積層時における加
圧が充分に行えるので占積率は高くなり、実効的
な磁束密度、透磁率は良くなる。これに対して第
７図に示すように凹面形のコア材５′を接着剤６
を用いて接着して積層したことによつて形成され
るラミネート・コアは、上下のコア材５′の凹部
７に接着剤６が残り、占積率が悪化するばかりで
なく、製品化した後に温度サイクルにより接着剤
６が滲み出て来るようなトラブルが起り易い。ま
た深い凹部７に溜つた接着剤６の接着力が発揮で
きず、剥れ易い。 Furthermore, as shown in FIG. 6, a laminate core formed by laminating convex core materials 5 by bonding them together using an adhesive 6 can be sufficiently pressurized during lamination, so that it can be easily spaced. The effective magnetic flux density and magnetic permeability improve. On the other hand, as shown in FIG.
In the case of a laminate core formed by adhering and laminating the core material using a Troubles such as the adhesive 6 oozing out due to temperature cycles are likely to occur. Furthermore, the adhesive 6 that has accumulated in the deep recess 7 cannot exert its adhesive strength and is likely to peel off.
これに対し凸面形に形成された薄板４は、積層
したコア材５の上下に滲みが出ず、製品としての
信頼性が優れている。 On the other hand, the thin plate 4 formed in a convex shape does not bleed above and below the laminated core material 5, and has excellent reliability as a product.
次に図面を参照しながら本発明の一実施例を説
明する。 Next, an embodiment of the present invention will be described with reference to the drawings.
先ず溶融母材２としてFe−Al−Si系のセンダ
スト合金、例えばFe：Al：Siの組成比が85：
5.4：9.6を耐熱容器１内に入れてヒータＨで加熱
して溶融させる。そして耐熱容器１によつて加熱
された溶融母材２を不活性ガス、例えばヘリウ
ム、アルゴン等を注入することによつて耐熱容器
１内の内圧を高め、ノズル１Ａからロール３，３
に噴出して超急冷法により、薄板４を得る。この
場合、センダスト合金の温度は1250℃〜1600℃、
ローラ３，３の回転数は400〜2000r.p.mである。
こうして、第３図のように、中心における点Ａで
の厚さD0が55μｍ、および中心から全幅Ｌの1/4、
離れた点Ｂでの厚さｄが50μｍの凸面形の薄板４
が得られる。この薄板４の曲げ強度の形状依存性
は、第４図に示され、D0／d0が大きく凸面形の
方が曲げ強度が強く、加工性が良いものが得られ
た。このように凸面形に形成した薄板４から、縦
スタガー取り（第８図参照）によつてコア材５を
コア取りし、このコア材５を接着剤６として例え
ばエポキシ系の接着剤を用いて11枚、積層し、ラ
ミネート・コアを形成した。この場合、接着剤６
は積層したコア材５の上下に滲み出ない。また接
着剤６の厚さが均一で薄くできるため、コア材５
相互の接着力が強く、剥離する等のトラブルが少
なく、製品としての信頼性が優れている。 First, as the molten base material 2, a Fe-Al-Si based sendust alloy, for example, a Fe:Al:Si composition ratio of 85:
5.4:9.6 is placed in heat-resistant container 1 and heated with heater H to melt it. Then, the internal pressure inside the heat-resistant container 1 is increased by injecting an inert gas such as helium, argon, etc. into the molten base material 2 heated by the heat-resistant container 1, and the rolls 3, 3 are
A thin plate 4 is obtained by ejecting and ultra-quenching. In this case, the temperature of Sendust alloy is 1250℃~1600℃,
The rotation speed of the rollers 3, 3 is 400 to 2000 rpm.
Thus, as shown in Fig. 3, the thickness D 0 at point A at the center is 55 μm, and 1/4 of the total width L from the center.
Convex thin plate 4 with thickness d of 50 μm at distant point B
is obtained. The shape dependence of the bending strength of the thin plate 4 is shown in FIG. 4, and it was found that the convex shape had a larger D 0 /d 0 and the bending strength was stronger and the workability was better. A core material 5 is removed from the thin plate 4 thus formed into a convex shape by vertical stagger removal (see Fig. 8), and this core material 5 is used as an adhesive 6 using, for example, an epoxy adhesive. 11 sheets were laminated to form a laminate core. In this case, adhesive 6
does not ooze out above and below the laminated core material 5. In addition, since the thickness of the adhesive 6 is uniform and can be made thin, the core material 5
Mutual adhesive strength is strong, there are few problems such as peeling, and the reliability as a product is excellent.
また本発明の第２実施例を説明する。この第２
実施例においては、上記第１実施例における組成
のセンダスト合金に加えてTi、Cu、Mo、Ni、
Ｗ、Cr、Co、Hf、Gd、Zn、Nb、Sn、Mn等の
元素を５重量パーセント以下、添加したものを溶
融母材２として用いたほかは前記第１実施例と同
様の構成および作製条件である。 A second embodiment of the present invention will also be described. This second
In the example, in addition to the sendust alloy having the composition in the first example, Ti, Cu, Mo, Ni,
The structure and fabrication were the same as in the first example, except that the molten base material 2 contained elements such as W, Cr, Co, Hf, Gd, Zn, Nb, Sn, Mn, etc. in an amount of 5% by weight or less. It is a condition.
このようにして製造された薄板４は、第３図の
ように凸面形で中心における点Ａでの厚さD0が
55μｍ、および中心から全幅Ｌの1/4、離れた点
Ｂでの厚さｄが50μｍの凸面形の薄板４が得られ
る。このように薄板４が凸面形をした場合には、
曲げ強度が強く、加工性が良い。またこの薄板４
からコア取りして、接着剤６を用いてコア材５を
積層してラミネート・コアを形成した場合には接
着剤６の厚さが均一で薄くできるため、コア材５
相互の接着力が強く、占積率が高くなるとともに
製品化した後にも温度サイクルにより滲み出るこ
とがない。 The thin plate 4 manufactured in this way has a convex shape as shown in FIG. 3, and the thickness D 0 at the center point A is
A convex thin plate 4 having a thickness of 55 μm and a thickness d of 50 μm at a point B which is 1/4 of the total width L from the center is obtained. When the thin plate 4 has a convex shape like this,
Strong bending strength and good workability. Also, this thin plate 4
When a core is taken from the core material 5 and the core material 5 is laminated using the adhesive 6 to form a laminate core, the thickness of the adhesive 6 can be made uniform and thin.
The mutual adhesion is strong, the space factor is high, and even after the product is manufactured, it does not bleed due to temperature cycles.
また本発明の第３実施例として、Fe−Si系合
金（Fe：Siの重量パーセント93.5：6.5）を溶融
母材２として用い、そして耐熱容器１内に取納し
たFe−Si系合金を1350℃〜1600℃の温度でFe−
Si系合金を溶融し、この溶融されたFe−Si系合
金を600〜1500r.p.mの回転数で回転しているロー
ラ３，３に噴き付けて凸面形の薄板４を形成した
ほかは前記実施例と同様の構成、作用がある。 Further, as a third embodiment of the present invention, an Fe-Si alloy (weight percentage of Fe:Si: 93.5:6.5) was used as the molten base material 2, and the Fe-Si alloy received in the heat-resistant container 1 was Fe− at temperatures from ℃ to 1600℃
The above procedure was carried out except that a Si alloy was melted and the melted Fe-Si alloy was sprayed onto rollers 3, 3 rotating at a rotation speed of 600 to 1500 rpm to form a convex thin plate 4. It has the same structure and effect as the example.
また本発明の第４実施例として、Fe−Ni系合
金（Fe：Niの重量比40：60）を溶融母材２とし
て用い、加熱容器１内に収納したFe−Ni系合金
を1460〜1600℃の加熱温度で溶融し、この溶融さ
れたFe−Ni系合金800〜2000r.p.mの回転数で回
転しているローラ３，３に噴き付けて凸面形の薄
板４を形成した。 Further, as a fourth embodiment of the present invention, an Fe-Ni alloy (Fe:Ni weight ratio of 40:60) was used as the molten base material 2, and the Fe-Ni alloy stored in the heating container 1 was heated to a temperature of 1460 to 1600. The molten Fe--Ni alloy was melted at a heating temperature of 800 to 2000 rpm and sprayed onto rollers 3, 3 rotating at a rotation speed of 800 to 2000 rpm to form a convex thin plate 4.
また第５実施例として溶融母材２としてFe−
Co−Si系合金、（Fe：Co：Siの重量パーセント
77：13：10）を溶融温度、1400℃〜1550℃で溶融
したものを用いて、薄板４を形成した。 In addition, as a fifth embodiment, Fe-
Co-Si alloy, (weight percent of Fe:Co:Si
77:13:10) was melted at a melting temperature of 1400°C to 1550°C to form a thin plate 4.
さらに第６実施例として溶融母材２としてFe
−Al系合金（Fe：Alの重量比84：16）を用い、
その溶融温度として1500℃〜1650℃の範囲でFe
−Al系合金をローラ３，３に噴出させることに
よつて薄板４を形成した。 Furthermore, as a sixth embodiment, Fe is used as the molten base material 2.
-Using an Al-based alloy (Fe:Al weight ratio 84:16),
Fe with its melting temperature ranging from 1500℃ to 1650℃
-The thin plate 4 was formed by jetting the Al-based alloy onto the rollers 3,3.
なお薄板４を形成するのに上記実施例のほか、
アモルフアス金属で形成してもよい。 In addition to the above embodiments, in order to form the thin plate 4,
It may be formed of amorphous metal.
上述のように本発明は、長さ方向に垂直な断面
形状を凸面形としたので機械的に強く、また積層
した場合の占積率が高く、さらには材料本来の性
能、例えば磁束密度、透磁率などの性能を活かす
ことができる。また積層の際に用いる接着剤の厚
さが均一で薄くできるので接着力が強く、剥離し
易い等のトラブルが少ない。 As mentioned above, the present invention has a convex cross-sectional shape perpendicular to the length direction, so it is mechanically strong and has a high space factor when laminated. Performance such as magnetic property can be utilized. Furthermore, since the thickness of the adhesive used during lamination can be made uniform and thin, the adhesive strength is strong and there are fewer problems such as easy peeling.
第１図は本発明の軟磁性薄板を製造すべき融体
超急冷装置を示した断面図、第２図は上記装置を
用いて製造される断面凸面形の薄板を示した斜面
図、第３図は同じく断面図、第４図は上記薄板か
らの曲げ強度の形状依存性を示した特性図、第５
図は本実施例の薄板と比較すべき断面凹面形の薄
板を示した斜面図、第６図は上記凸面形の薄板を
用いてラミネート・コアを形成する場合の断面
図、第７図は同じく上記凹面形の薄板を用いてラ
ミネート・コアを形成する場合の断面図、第８図
は上記凸面形の薄板を用いて縦スタガーのコア取
りをする場合の平面図、第９図は同じく横スタガ
ーのコア取りをする場合の平面図、第１０図は同
じく縦平行のコア取りをする場合の平面図、第１
１図は同じく横平行のコア取りをする場合の平面
図、第１２図は本発明の第３実施例の薄板の曲げ
強度に形状特性図、第１３図は同じく本発明の第
４実施例の薄板の曲げ強度の形状依存性を示した
特性図、第１４図は同じく本発明の曲げ強度の形
状依存性を示した特性図、第１５図は同じく本発
明の第６実施例の薄板の曲げ強度の形状依存性を
示した特性図である。
１……加熱容器、２……溶融母材、３……ロー
ラ、４……薄板、５……コア材、６……接着剤。
FIG. 1 is a cross-sectional view showing a melt ultra-quenching apparatus for producing the soft magnetic thin plate of the present invention, FIG. 2 is a perspective view showing a thin plate with a convex cross-section produced using the above-mentioned apparatus, and FIG. The figure is also a cross-sectional view, Figure 4 is a characteristic diagram showing the shape dependence of the bending strength from the thin plate, and Figure 5
The figure is a perspective view showing a thin plate with a concave cross-section to be compared with the thin plate of this example, FIG. 6 is a cross-sectional view when a laminate core is formed using the above-mentioned convex thin plate, and FIG. 7 is the same. A sectional view when forming a laminate core using the above concave thin plate, Fig. 8 is a plan view when coring a vertical stagger using the above convex thin plate, and Fig. 9 shows a horizontal stagger as well. Fig. 10 is a plan view when coring is done vertically and parallelly.
Figure 1 is a plan view of the case where horizontally parallel cores are taken, Figure 12 is a diagram showing the bending strength and shape characteristics of a thin plate according to the third embodiment of the present invention, and Figure 13 is a diagram of the shape characteristics of the fourth embodiment of the present invention. A characteristic diagram showing the shape dependence of the bending strength of a thin plate, FIG. 14 is a characteristic diagram showing the shape dependence of the bending strength of the present invention, and FIG. 15 is a characteristic diagram showing the shape dependence of the bending strength of a thin plate according to the sixth embodiment of the present invention. FIG. 3 is a characteristic diagram showing shape dependence of strength. DESCRIPTION OF SYMBOLS 1... Heating container, 2... Melting base material, 3... Roller, 4... Thin plate, 5... Core material, 6... Adhesive.
Claims (1)
されたことを特徴とした軟磁性薄板。1. A soft magnetic thin plate characterized by having a convex cross section perpendicular to its length.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP12678182A JPS5918607A (en) | 1982-07-22 | 1982-07-22 | Soft magnetic thin plate |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP12678182A JPS5918607A (en) | 1982-07-22 | 1982-07-22 | Soft magnetic thin plate |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS5918607A JPS5918607A (en) | 1984-01-31 |
| JPH0319682B2 true JPH0319682B2 (en) | 1991-03-15 |
Family
ID=14943770
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP12678182A Granted JPS5918607A (en) | 1982-07-22 | 1982-07-22 | Soft magnetic thin plate |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS5918607A (en) |
-
1982
- 1982-07-22 JP JP12678182A patent/JPS5918607A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS5918607A (en) | 1984-01-31 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US4257830A (en) | Method of manufacturing a thin ribbon of magnetic material | |
| US4265682A (en) | High silicon steel thin strips and a method for producing the same | |
| EP0640419B1 (en) | Process for producing an amorphous alloy ribbon | |
| JPH0152811B2 (en) | ||
| US4337087A (en) | Microcrystalline thin strip for magnetic material having high permeability, a method of producing the same and articles made from the thin strip | |
| JPH0319682B2 (en) | ||
| JPS6038462B2 (en) | Silicon iron ribbon and its manufacturing method | |
| JPS60177936A (en) | Thin strip consisting of fe-base amorphous alloy having large thickness | |
| JP5029956B2 (en) | Magnetic core for antenna, method for manufacturing the same, and antenna | |
| JPH0554423B2 (en) | ||
| US6103396A (en) | Thick amorphous metal strip having improved ductility and magnetic properties | |
| JPH0416846B2 (en) | ||
| JPH0319683B2 (en) | ||
| JPH0471969B2 (en) | ||
| JPS5824924B2 (en) | Stork | |
| JPH0416845B2 (en) | ||
| JPH07300657A (en) | Amorphous alloy ribbon manufacturing method | |
| JPS6112856A (en) | Production of high-permeability amorphous alloy | |
| JPS6161212A (en) | Production of magnetic head core | |
| JPS6021328A (en) | Production of light-gauge high silicon steel strip having (100) <oki> texture | |
| JPS6041139B2 (en) | Amorphous magnetic alloy thin plate for magnetic heads | |
| JPS62281108A (en) | Magnetic core and its manufacture | |
| JPS6041140B2 (en) | Amorphous magnetic alloy thin plate for magnetic heads | |
| JPS5853705B2 (en) | Manufacturing method of high permeability alloy ribbon | |
| JPS6018128B2 (en) | Manufacturing method of magnetic tape |