JPH04211103A

JPH04211103A - Magnetic amplifier

Info

Publication number: JPH04211103A
Application number: JP3026638A
Authority: JP
Inventors: Koichiro Inomata; 浩一郎猪俣; Michio Hasegawa; 長谷川　迪雄; Masakatsu Haga; 羽賀　正勝; Takao Sawa; 孝雄沢
Original assignee: Toshiba Corp
Current assignee: Toshiba Corp
Priority date: 1991-01-29
Filing date: 1991-01-29
Publication date: 1992-08-03
Anticipated expiration: 2010-08-02
Also published as: JPH0773086B2

Abstract

PURPOSE:To operate a magnetic amplifier well in high frequency region (above 50kHz) by employing a Co series amorphous alloy, containing specific atomic % of B and Si and having crystallization temperature higher than Curie temperature, in the core of the magnetic amplifier. CONSTITUTION:A Co series amorphous alloy shown by (Co1-X1-X2FeX1MX2)X3BX4 Si100-X3-X4 (where, M is at least one element selected from a group of Ti, V, Cr, Mn, Ni, Zr, Nb, Mo, Ru, Hf, Ta, W, Re and X1, X2, X3, X4 satisfy the relations 0<X1<=0.10, 0<=X2<=0.10, 70<=X3<=79, 5<=X4<=9) is employed as a core material for a magnetic amplifier. The amorphous alloy has low coercive force in high frequency region above 100kHz and excellent in rectangularity. Consequently, the magnetic amplifier operates well with high efficiency and low exciting current even in high frequency region above 100kHz.

Description

[Detailed description of the invention]

［発明の目的］［０００１］ [Purpose of the invention] [0001]

【産業上の利用分野】本発明は磁気増幅器に関する。更
に詳しくは、高周波にける低保磁力、角形特性にすぐれ
る非晶質合金を用いた磁気増幅器に関する。［０００２］BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to magnetic amplifiers. More specifically, the present invention relates to a magnetic amplifier using an amorphous alloy that has low coercive force and excellent square characteristics at high frequencies. [0002]

【従来の技術】電子計算機の周辺機器や一般通信器用の
安定化電源としては、近年、磁気増幅器を組込んだスイ
ッチング電源が広く用いられている。［０００３］　この磁気増幅器を構成する主要部は可飽
和リアクタであり、その鉄心には角形磁化特性にすぐれ
た磁心材料が必要とされている。従来は、このような磁
心材料としてはＦｅ−Ｎｉ結晶質合金から成るセンデル
タ（商品名）が使用されてきた。［０００４］Ｌかしながら、センデルタは角形磁化特性
にはすぐれているものの、２０　ｋＨｚ以上の高周波に
おいては、保磁力が大きくなってうず電流損が増大して
発熱し、使用不能となる。そのため、磁気増幅器を組込
んだスイッチング電源のスイッチング周波数は２０ｋＨ
７以下に限られていた。［０００５］一方、近年においては、スイッチング電源
の小形化・計景化に対する要望と相俟って、スイッチン
グ周波数のより高周波化が求められているが、現在まで
高周波における保磁力が小さく、かつ角形性にすぐれた
磁心材料で満足のいくものは見出されていない。［０００６］2. Description of the Related Art In recent years, switching power supplies incorporating magnetic amplifiers have been widely used as stabilized power supplies for peripheral devices of electronic computers and general communication devices. [0003] The main part constituting this magnetic amplifier is a saturable reactor, and its iron core requires a magnetic core material with excellent square magnetization characteristics. Conventionally, Sendelta (trade name), which is made of a Fe--Ni crystalline alloy, has been used as such a magnetic core material. [0004]L However, although center delta has excellent square magnetization characteristics, at high frequencies of 20 kHz or higher, the coercive force increases, eddy current loss increases, and heat is generated, making it unusable. Therefore, the switching frequency of a switching power supply incorporating a magnetic amplifier is 20kHz.
It was limited to 7 or below. [0005] On the other hand, in recent years, along with the desire for smaller and more economical switching power supplies, there has been a demand for higher switching frequencies. No satisfactory magnetic core material with excellent properties has been found. [0006]

【発明が解決しようとする課題】本発明は以上の点を考
慮してなされたもので、高周波領域で良好な駆動が可能
な磁気増幅器を提供することを目的とする。　［発明の
構成］［０００７］SUMMARY OF THE INVENTION The present invention has been made in consideration of the above points, and an object of the present invention is to provide a magnetic amplifier that can be driven favorably in a high frequency region. [Configuration of the invention] [0007]

【課題を解決するための手段及び作用】本発明者らは、
上記のような問題点を解消するために鋭意研究を重ねた
結果、ＢとＳｉを所定の原子％置台み、かつ結晶化温度
（Ｔｘ）がキューり温度（Ｔｃ）よりも大きいという関
係を有するＣｏ系非晶質合金は、１００　ｋＨｚ以上の
高周波において、低保磁力でありしかも角形性にも優れ
るとの事実を見出し本発明を完成するに到った。［０００８１本発明は、次式：％式％（式中、ＭはＴｉ、Ｖ、Ｃｒ、Ｍｎ、Ｎｉ、Ｚｒ、Ｎｂ
、Ｍｏ、Ｒｕ、Ｈｆ、Ｔａ、Ｗ、Ｒｅの群から選ばれる
少くとも１種の元素であり、ＸＩ、　Ｘ２．　Ｘ３、Ｘ
４はそれぞれ、０くＸ１≦０．１０．　　Ｏ≦Ｘ２≦０
．１０．７０≦Ｘ３≦７９，５≦Ｘ４≦９の関係を満た
す数である。）で示される高周波における角形比が大き
く、保磁力の小さい非晶質合金を磁心に用い、５０　ｋ
Ｈｚ以上の周波数で駆動することを特徴とする磁気増幅
器である。［０００９］本発明に係る非晶質合金の組成において、
Ｆｅは得られる合金の高磁束密度化に寄与し、その組成
比Ｘ１は０くＸ１≦０．１０の範囲に設定される。Ｘｌ
が０．１０を越えると、全体の磁歪が大きくなり、かつ
保磁力（Ｈｃ　）も増大するので好ましくない。（００１０１Ｍ　（Ｔｉ、Ｖ、Ｃｒ、Ｍｎ、Ｎ１ｊｒ、
Ｎｂ、Ｍｏ、Ｒｕ、Ｈｆ、Ｔａ、Ｗ。Ｒｅの群から選ばれる少くとも１種）は、合金の熱的安
定性に関与し、その組成比Ｘ２はＯ≦Ｘ２≦０．１０の
範囲に設定される。Ｘ２が０．１０を越えると、非晶質
化が困難となる。これら元素Ｍのうち、Ｎｂ、Ｔａ、Ｍｏ、Ｃｒはその効
果が大きく有用である。なお少量の添加でその効果を発
揮するが、Ｘ２≧０．叶であることが実用的である。［００１１１上記３成分（Ｃｏ、　Ｆｅ、　Ｍ）は、全
体でその組成比Ｘ３が７０≦Ｘ３≦７９の範囲に設定さ
れる。Ｘ３が７０未満の場合には、非晶質化が困難とな
り、逆に７９を越えると結晶化温度（Ｔｘ）がキューり
温度（Ｔｃ）より低くなるため全体として低保磁力が得
られなくなる。［００１２］つぎに、本発明の非晶質合金において、Ｂ
及びＳｉの半金属元素は非晶質化のためには不可欠であ
るが、Ｂの組成比Ｘ４が５未満の場合には非晶質合金が
得られない。しかし、Ｘ４が９を超えると、磁気特性に
おける角形比が小さくなる。したがって、Ｂの組成比Ｘ
４は５≦Ｘ４≦９の範囲に設定される。［００１３］一般に、非晶質合金は、所定組成比の合金
素材を溶融状態から１０５℃／秒以上の冷却速度で急冷
すること（液体急冷法）によって得られることが知られ
ている。本発明の非晶質合金も、上記した常法によって
容易に製造できる。［００１４１本発明の非晶質合金は、例えば常用の単ロ
ール法によって製造された板状の薄体として使用される
。この場合、厚み１０μｍ未満の薄体を製造することは
液体急冷法では実質的に困難であり、また厚みが２５μ
ｍを超えると高周波における保磁力が増大するので、通
常、薄体の厚みを１０〜２５μｍ両端を含む）の範囲に
設定するのが好ましい。［００１５］本発明に係る非晶質合金の磁気特性、特に
角形比は周波数が高くなるにつれ良好になるため、本発
明に係る磁気増幅器の駆動周波数は５０　ｋＨｚ以上、
更には１００ｋＨｚ以上とすることが好ましい。［００１６］なお磁気増幅器の回路構成は特に問わず、
スイッチングレギュレータに用いられる可飽和リアクト
ルを用いたものなど各種の構成があげられる。［００１７］[Means and effects for solving the problem] The present inventors have
As a result of extensive research to solve the above problems, we found that B and Si are placed at a predetermined atomic percent, and the relationship is such that the crystallization temperature (Tx) is higher than the quenching temperature (Tc). We have completed the present invention by discovering the fact that Co-based amorphous alloys have low coercive force and excellent squareness at high frequencies of 100 kHz or higher. [00081 The present invention is based on the following formula: % formula % (wherein M is Ti, V, Cr, Mn, Ni, Zr, Nb
, Mo, Ru, Hf, Ta, W, and Re, and XI, X2. X3,X
4 are respectively 0×X1≦0.10. O≦X2≦0
．． The number satisfies the following relationships: 10.70≦X3≦79, 5≦X4≦9. ), an amorphous alloy with a large squareness ratio at high frequencies and a small coercive force is used for the magnetic core, and 50 k
This magnetic amplifier is characterized by being driven at a frequency of Hz or higher. [0009] In the composition of the amorphous alloy according to the present invention,
Fe contributes to increasing the magnetic flux density of the obtained alloy, and its composition ratio X1 is set in the range of 0 and X1≦0.10. Xl
If it exceeds 0.10, the overall magnetostriction becomes large and the coercive force (Hc) also increases, which is not preferable. (00101M (Ti, V, Cr, Mn, N1jr,
Nb, Mo, Ru, Hf, Ta, W. At least one element selected from the group Re) is involved in the thermal stability of the alloy, and its composition ratio X2 is set in the range O≦X2≦0.10. When X2 exceeds 0.10, it becomes difficult to make it amorphous. Among these elements M, Nb, Ta, Mo, and Cr are highly effective and useful. The effect can be achieved with a small amount of addition, but if X2≧0. Being a leaf is practical. [00111 The composition ratio X3 of the three components (Co, Fe, M) as a whole is set in the range of 70≦X3≦79. If X3 is less than 70, it will be difficult to make it amorphous, and if it exceeds 79, the crystallization temperature (Tx) will be lower than the cueing temperature (Tc), making it impossible to obtain a low coercive force as a whole. [0012] Next, in the amorphous alloy of the present invention, B
The metalloid elements of Si and Si are essential for amorphization, but if the composition ratio X4 of B is less than 5, an amorphous alloy cannot be obtained. However, when X4 exceeds 9, the squareness ratio in the magnetic properties becomes small. Therefore, the composition ratio of B
4 is set in the range of 5≦X4≦9. [0013] Generally, it is known that an amorphous alloy can be obtained by rapidly cooling an alloy material having a predetermined composition ratio from a molten state at a cooling rate of 105° C./sec or more (liquid quenching method). The amorphous alloy of the present invention can also be easily produced by the conventional method described above. [00141] The amorphous alloy of the present invention is used, for example, as a plate-like thin body produced by a conventional single roll method. In this case, it is virtually difficult to produce a thin body with a thickness of less than 10 μm using the liquid quenching method, and
If the thickness exceeds m, the coercive force at high frequencies will increase, so it is usually preferable to set the thickness of the thin body in the range of 10 to 25 μm (including both ends). [0015] Since the magnetic properties of the amorphous alloy according to the present invention, especially the squareness ratio, become better as the frequency increases, the driving frequency of the magnetic amplifier according to the present invention is 50 kHz or higher,
Furthermore, it is preferable to set it to 100kHz or more. [0016] The circuit configuration of the magnetic amplifier is not particularly limited.
There are various configurations such as one using a saturable reactor used in a switching regulator. [0017]

【実施例】以下に本発明を実施例に基づいて説明する。［００１８］実施例１表１に示した各種組成の非晶質合金の薄体を常用の単ロ
ール法で作製した。各薄体の幅は約５ｍｍで、厚みはい
ずれも１８〜２２μｍの範囲にあった。これら薄体から
長さ１ｍの帯を切り取り、直径２０ｍｍのボビンに巻き
つけてトロイダルコアを作製した。つぎに、これをそれ
ぞれ、結晶化温度（Ｔｘ）以下、キューり温度（Ｔｃ）
以上の適宜な温度で熱処理した後、全体を水中（２５℃
）に投入して急冷した。（００１９］得られたコアに１次及び２次巻線を施し、
外部磁場１０ｅ下で交流磁化測定装置を用いて交流ヒス
テリシス曲線を測定し、ここから保磁力Ｈｃ及び角形比
Ｂｒ／Ｂ１（Ｂｒ：残留磁束密度、Ｂｌ　：　１０ｅの
磁場における磁束密度）を求めた。２０ｋＨｚ、　５０
ｋＨｚ、　１００ｋＨｚの高周波における各薄体のＨｅ
、　Ｂｒ／ＢｌＯ値を表１に示した。比較のため、従来
用いられているセンデルタの値も併記した。［００２０１EXAMPLES The present invention will be explained below based on examples. [0018] Example 1 Thin bodies of amorphous alloys having various compositions shown in Table 1 were produced by a conventional single roll method. The width of each thin body was about 5 mm, and the thickness of each thin body was in the range of 18 to 22 μm. A 1 m long strip was cut from these thin bodies and wound around a bobbin with a diameter of 20 mm to produce a toroidal core. Next, these are respectively below the crystallization temperature (Tx) and the curative temperature (Tc).
After heat treatment at the above appropriate temperature, the entire body was placed in water (25°C).
) and quenched. (0019) Applying primary and secondary winding to the obtained core,
An AC hysteresis curve was measured using an AC magnetization measuring device under an external magnetic field of 10e, and from this the coercive force Hc and squareness ratio Br/B1 (Br: residual magnetic flux density, Bl: magnetic flux density in a magnetic field of 10e) were determined. 20kHz, 50
He of each thin body at high frequency of kHz, 100kHz
, Br/BIO values are shown in Table 1. For comparison, the conventionally used sender delta values are also shown. [00201

【表１］この表から明らかな様に、本発明の非晶質合金は１００
ｋＨｚの高周波でＨｃ≦０．３３．　Ｂｒ／Ｂｌ≧９０
と優れていることがわかる。［００２１１これに反し、センデルタは、Ｂｒ／Ｂｌは
大きいけれどもＨｃも大きく、とりわけ５０ｋＨｚ以上
の高周波では１０ｅの外部磁場の下では測定不能となり
、高周波における磁心材料としては不適であった。［００２２］実施例２式：　　（ＣＯｏ９２Ｆｅｏ、ｏｅＮｂｏ、ｏ２）　７
７ＢＸ　Ｓ　１２３−で示され、Ｂ景を種々に変えた（
すなわち、Ｂ組成比Ｘを種々に変化させた）非晶質合金
の薄体を実施例１と同様の方法で作製し、これらについ
てＨｅ、　Ｂｒ／Ｂｌを測定した。その結果を図１に示
した。図では（○）はＨｅ、　　（・）はＢｒ／Ｂｌを
表す。（００２３１図１から明らかな様にＸが５．６．７．８
．９のものは、いずれもその角形比Ｂｒ／Ｂｌが８５％
以上であり、Ｘが１０．１１（比較例２，３）のものは
８５％より小さかった。このことがらＢの組成比Ｘは５
≦Ｘ≦９の範囲で良好な特性を有していることが分かる
。［００２４］なおＸが５未満のものは非晶質とならなか
った。［００２５］実施例３表２に示した組成でＭの異なる非晶質合金の薄体を単ロ
ール法で作製した。薄体の厚みはいずれも１８〜２２μ
ｍの範囲内にあった。［００２６］　これら薄体から実施例１と同様にしてト
ロイダルコアを作製し、コアに１次及び２次巻線を施し
た後、外部磁場１０ｅ下で交流磁化測定装置を用いて５
０　ｋＨｚ及び１００ｋＨ７における交流ヒステリシス
曲線を測定し、保磁力Ｈｅ、角形比Ｂｒ／Ｂｌを求めた
。［００２７］ついで、これらを１２０℃の恒温槽に１０
００時間エージング処理した後、５０ＫＨｚで再Ｕ’Ｈ
ｃ及’Ｏ＝”Ｂｒ／Ｂｌを測定した。その結果を表２に
示した。比較のため、Ｍを含まないものの測定値も併記
した。［００２８］【表２】この表から明らかなように、本発明の非晶質合金は高周
波において低保磁力、高角形性であるのみならず、熱的
安定性にすぐれることが判明した。とくに、ＭがＮｂ。Ｍｏ、Ｔａ、Ｃｒの場合はその効果が著しい。［００２９］また１００ｋＨｚでの値も同様に表３に示
した。［００３０１[Table 1] As is clear from this table, the amorphous alloy of the present invention has a
Hc≦0.33 at high frequency of kHz. Br/Bl≧90
It can be seen that it is excellent. [00211] On the other hand, Sendelta has a large Br/Bl but also a large Hc, and is unmeasurable under an external magnetic field of 10 e especially at high frequencies of 50 kHz or higher, making it unsuitable as a magnetic core material at high frequencies. [0022] Example 2 Formula: (COo92Feo, oeNbo, o2) 7
It was shown as 7BX S 123-, and the B view was changed in various ways (
That is, thin bodies of amorphous alloys (with various B composition ratios X) were prepared in the same manner as in Example 1, and He and Br/Bl were measured for these thin bodies. The results are shown in Figure 1. In the figure, (○) represents He, and (.) represents Br/Bl. (00231 As is clear from Figure 1, X is 5.6.7.8
．． 9, the squareness ratio Br/Bl is 85%.
The results are as follows, and those with X of 10.11 (Comparative Examples 2 and 3) were smaller than 85%. This means that the composition ratio X of B is 5
It can be seen that it has good characteristics in the range of ≦X≦9. [0024] In addition, those in which X was less than 5 did not become amorphous. [0025] Example 3 Thin bodies of amorphous alloys having the compositions shown in Table 2 and different M were produced by a single roll method. Thickness of thin body is 18-22μ
It was within the range of m. [0026] A toroidal core was produced from these thin bodies in the same manner as in Example 1, and after primary and secondary windings were applied to the core, 5
AC hysteresis curves at 0 kHz and 100 kHz were measured, and the coercive force He and squareness ratio Br/Bl were determined. [0027] Next, these were placed in a constant temperature bath at 120°C for 10 minutes.
After aging for 00 hours, re-U'H at 50KHz.
c and 'O = "Br/Bl were measured. The results are shown in Table 2. For comparison, the measured values for those not containing M are also listed. [0028] [Table 2] As is clear from this table, In addition, it was found that the amorphous alloy of the present invention not only has a low coercive force and high angularity at high frequencies, but also has excellent thermal stability.Especially when M is Nb, Mo, Ta, or Cr. The effect is remarkable. [0029] The values at 100kHz are also shown in Table 3. [00301

【表３］この表から明らかな様に１００ｋＨｚでも同様の傾向を
示すことが分かる。［００３１］実施例４組成比：　　（ＣＯｏ、５ｓＦｅｏ、ｏｓＮｂｏ、ｏ２
Ｎｉｏ、ｏ４）７５ＢＩ５Ｓｉ１ｏの本発明非晶質合金
を用い、単ロール法でロール回転数を変えることによっ
て、厚み１２μｍ、１８μｍ、２２μｍ、２５μｍ、２
７μｍの薄体を作製した。これらについて、実施例１と
同様の方法で各種の高周波における保磁力Ｈｃを測定し
た結果を図２に示した。［００３２］図２から明らかなように、厚み１２μｍ、
１８１℃ｍ、　２２１℃ｍ、　２５μｍのものは、５０
ｋＨｚにおいてもＨｃは０．４０ｅ以下であった。一方
、厚み２７μｍのものは、５０　ｋＨｚ以上ではそのＨ
ｅが０．４０ｅを超えて、磁気増幅器用の磁心材料とし
ては実用的でなくなることが判明した。［００３３］実施例５組成が（ＣＯｏ９ｏＦｅｏ、ｏｅＣｒｏ、ｏ４）　７７
Ｂ８　Ｓ　ｉｌｓで厚み１６μｍの非晶質合金の薄体を
作製し、実施例１と同様にしてトロイダルコアを作製し
た。これを４３０℃（Ｔｃ　３８０℃、　Ｔｘ　５００
℃）で熱処理した後、水中に投入して急冷した。【００３４】得られたコアを、図３に示した回路の磁気
増幅器に適用し、１００ｋＨ２動作のスイッチング電源
としての性能を調べた。測定項目は、効率（出力／入力
×１００（％））、コア温度上昇（℃）及び励磁電流（
ｍＡ）であった。図３の回路において、１は入力フィル
タ、２はスイッチ、３はトランス、４は磁気増幅器、５
は整流器、６は出力フィルタ、７は制御部である。以上
の結果を表４に示した。なお、比較のため、センデルタ
を用いた場合の結果も併記した。［００３５］[Table 3] As is clear from this table, it can be seen that the same tendency is shown even at 100 kHz. [0031] Example 4 Composition ratio: (COo, 5sFeo, osNbo, o2
Using the amorphous alloy of the present invention of Nio, o4) 75BI5Si1o, by changing the roll rotation speed in a single roll method, thicknesses of 12 μm, 18 μm, 22 μm, 25 μm, 2
A thin body of 7 μm was produced. Regarding these, the coercive force Hc at various high frequencies was measured using the same method as in Example 1, and the results are shown in FIG. [0032] As is clear from FIG. 2, the thickness is 12 μm,
181℃m, 221℃m, 25μm, 50
Even at kHz, Hc was 0.40e or less. On the other hand, the one with a thickness of 27 μm loses its H at 50 kHz or higher.
It was found that when e exceeds 0.40e, it is no longer practical as a magnetic core material for a magnetic amplifier. [0033] Example 5 Composition is (COo9oFeo, oeCro, o4) 77
A thin body of an amorphous alloy having a thickness of 16 μm was produced using B8 Sils, and a toroidal core was produced in the same manner as in Example 1. This was heated at 430℃ (Tc 380℃, Tx 500℃
After heat treatment at 10°C), it was poured into water and quenched. The obtained core was applied to the magnetic amplifier of the circuit shown in FIG. 3, and its performance as a switching power supply operating at 100 kHz was investigated. The measurement items are efficiency (output/input x 100 (%)), core temperature rise (℃), and excitation current (
mA). In the circuit of Figure 3, 1 is an input filter, 2 is a switch, 3 is a transformer, 4 is a magnetic amplifier, 5
is a rectifier, 6 is an output filter, and 7 is a control section. The above results are shown in Table 4. For comparison, the results using Sendelta are also shown. [0035]

【表４】この表から明らかなように、本発明に係る非晶質合金を
用いた磁気増幅器では、センデルタを用いた場合に比べ
て効率が約１０％向上し、かつ励磁電流も１／９で、コ
アの温度上昇も小さいく優れたものであることが分かる
。［００３６］[Table 4] As is clear from this table, in the magnetic amplifier using the amorphous alloy according to the present invention, the efficiency is improved by about 10% compared to the case using the center delta, and the excitation current is also 1/9 It can be seen that the core temperature rise is also small and excellent. [0036]

【発明の効果】以上の説明で明らかなように、本発明に
係る非晶質合金を用いた磁気増幅器は１００ｋＨｚの高
周波領域でも、高効率、低励磁電流というように良好に
動作し、その工業的価値は極めて大である。Effects of the Invention As is clear from the above explanation, the magnetic amplifier using the amorphous alloy according to the present invention operates well with high efficiency and low excitation current even in the high frequency range of 100 kHz, and is suitable for industrial use. The value is extremely high.

[Brief explanation of the drawing]

【図１】　図１は組成（ＣＯｏ、　９２　Ｆ　ｅｏ、　
ｏ６Ｎ　ｂｏ、　０２）　７７Ｂｘ　Ｓ　１２３−なる
本発明に係る非晶質合金におけるＢ組成比（Ｘ）とＢｒ
／Ｂｌ　、　Ｈｅとの関係曲線図。[Figure 1] Figure 1 shows the composition (COo, 92 F eo,
o6N bo, 02) 77Bx S 123-B composition ratio (X) and Br in the amorphous alloy according to the present invention
/Bl, relationship curve diagram with He.

【図２】　図２は組成（ＣＯｏ、　ｓｓ　Ｆ　ｅｏ、　
０６　Ｎ　ｂｏ、　０２　Ｎ　ｉｏ、０４）　７５Ｂ＋
ｓｓ　ｉ＋ｏなる本発明に係る非晶質合金で厚みの異な
る薄体の試験周波数（ｆ）とＨｃとの関係曲線図。[Figure 2] Figure 2 shows the composition (COo, ss F eo,
06 N bo, 02 N io, 04) 75B+
FIG. 2 is a relationship curve diagram between test frequency (f) and Hc of a thin body of an amorphous alloy according to the present invention, ss i+o, having different thicknesses.

【図３】　図３は組成（ＣＯｏ、　９０　Ｆ　ｅｏ、　
０６　Ｃｒ　Ｏ，０４）　７７Ｂ８Ｓ１１５の本発明に
係る非晶質合金を可飽和リアクタに適用した磁気増幅器
を含んでなるスイッチング電源回路図。[Figure 3] Figure 3 shows the composition (COo, 90 F eo,
06 Cr O, 04) 77B8S115 is a switching power supply circuit diagram including a magnetic amplifier in which the amorphous alloy according to the present invention is applied to a saturable reactor.

[Explanation of symbols]

１・・・入力フィルタ２・・・スイッチ３・・・トランス４・・・磁気増幅器５・・・整流器６・・・出力フィルタフ・・・制御部 1...Input filter 2...Switch 3...Trance 4...Magnetic amplifier 5... Rectifier 6...Output filter F...control section

【図１】[Figure 1]

【図２】フロントページの続き[Figure 2] Continuation of front page

Claims

[Claims]

[Claim 1] The following formula: % formula % (wherein M is Ti, V, Cr, Mn, Ni, zr, N
b, Mo, Ru, Hf, Ta, W, and Re, and XI, X2. X3,
X4 is 0 and X1≦0.10, respectively. O≦X2≦
The number satisfies the following relationships: 0.10.70≦X3≦79, 5≦X4≦9. ), an amorphous alloy with a large squareness ratio at high frequencies and a small coercive force is used for the magnetic core.
A magnetic amplifier characterized by being driven at a frequency of kHz or higher.

2. The magnetic amplifier according to claim 1, which is a thin body having a thickness of 25 μm or less.

3. The amorphous alloy has a squareness ratio Br/Bl at 100 kHz (Br is the residual magnetic flux density, Bl is 1
0e magnetic flux density in magnetic field) is 90% or more, coercive force is 0.3
2. The magnetic amplifier according to claim 1, wherein the magnetic amplifier has a diameter of 30e or less.

4. The magnetic amplifier according to claim 1, wherein the amorphous alloy has a relationship of X2>0.

5. The amorphous alloy is heated at 120°C and 100°C.
Squareness ratio Br/Bl at 50 kHz after 0 hour aging treatment (Br is residual magnetic flux density,
2. The magnetic amplifier according to claim 1, wherein Bl has a magnetic flux density in a 10e magnetic field of 90% or more and a coercive force of 0.260e or less.