JPH09180926A - Low loss oxide magnetic material - Google Patents
Low loss oxide magnetic materialInfo
- Publication number
- JPH09180926A JPH09180926A JP7350402A JP35040295A JPH09180926A JP H09180926 A JPH09180926 A JP H09180926A JP 7350402 A JP7350402 A JP 7350402A JP 35040295 A JP35040295 A JP 35040295A JP H09180926 A JPH09180926 A JP H09180926A
- Authority
- JP
- Japan
- Prior art keywords
- oxide
- pcv
- magnetic material
- cao
- low loss
- 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.)
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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
- H01F1/12—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 soft-magnetic materials
- H01F1/34—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 soft-magnetic materials non-metallic substances, e.g. ferrites
- H01F1/342—Oxides
- H01F1/344—Ferrites, e.g. having a cubic spinel structure (X2+O)(Y23+O3), e.g. magnetite Fe3O4
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- Chemical & Material Sciences (AREA)
- Dispersion Chemistry (AREA)
- Engineering & Computer Science (AREA)
- Power Engineering (AREA)
- Magnetic Ceramics (AREA)
- Soft Magnetic Materials (AREA)
- Compounds Of Iron (AREA)
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、スイッチング電源
等の各種電源用トランス材として用いられる低損失酸化
物磁性材料に関し、特に、Ｍｎ−Ｚｎ系フェライトに関
するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a low loss oxide magnetic material used as a transformer material for various power supplies such as switching power supplies, and more particularly to a Mn-Zn ferrite.
【０００２】[0002]
【従来の技術】近年、各種電源機器の高性能化、かつ、
軽量小型化の進展が著しい。それ故、この各種電源機器
に搭載されるスイッチング電源用トランス材の、より一
層の高性能化が求められている。2. Description of the Related Art In recent years, the performance of various power supply devices has been improved, and
Significant progress has been made in reducing the size and weight. Therefore, it is required to further improve the performance of the switching power supply transformer material mounted on the various power supply devices.
【０００３】トランス材の高性能化に必要な代表的項目
としては、高磁束密度、高振幅透磁率、低電力損失（低
損失）が挙げられる。なお、以下においては、振幅透磁
率をμa、電力損失をＰcvと称する。Typical items required for improving the performance of transformer materials are high magnetic flux density, high amplitude magnetic permeability, and low power loss (low loss). In the following, the amplitude permeability is referred to as μa and the power loss is referred to as Pcv.
【０００４】ところで、一般に、Ｍｎ−Ｚｎ系フェライ
トは、粉末冶金法により、混合、予焼、解砕、造粒、成
形、焼成の工程を経て製造され、この製造プロセス条件
の適切なコントロールにより、高性能化が図られてい
る。又、更に、Ｆｅ2Ｏ3、ＭｎＯ、ＺｎＯというマトリ
ックス相を形成する主成分組成と、ＳｉＯ2、ＣａＯ、
Ｔａ2Ｏ5、Ｎｂ2Ｏ5等の粒界相を形成する副成分組成の
厳密なコントロールにより、高性能化が図られている。By the way, in general, Mn-Zn ferrite is manufactured by powder metallurgy through the steps of mixing, pre-firing, crushing, granulation, molding and firing, and by controlling the manufacturing process conditions appropriately, Higher performance has been achieved. In addition, the main component composition of Fe 2 O 3 , MnO, and ZnO forming a matrix phase, and SiO 2 , CaO,
Higher performance has been achieved by strictly controlling the composition of subcomponents forming the grain boundary phase such as Ta 2 O 5 and Nb 2 O 5 .
【０００５】Ｐcvを下げるためには、粒界相の厚みを大
きくして、より高抵抗化を図ることが最も効果的であ
る。一方、μaを大きくするためには、粒界相の厚さを
極力薄くする、あるいは、マトリックス相中に残存する
不純物量を低減することが必要である。In order to lower Pcv, it is most effective to increase the thickness of the grain boundary phase to achieve higher resistance. On the other hand, in order to increase μa, it is necessary to reduce the thickness of the grain boundary phase as much as possible or reduce the amount of impurities remaining in the matrix phase.
【０００６】このように、μa、Ｐcvにおける高性能化
のための原理は、二律背反の関係にあり、従来は、両者
を満足させる高性能なＭｎ−Ｚｎ系フェライトが得難
く、１００ｋＨｚ、２０００Ｇ、１００℃の条件におい
て、Ｐcvで３５０〜５００（ｋＷ／ｍ3）程度のもの
か、あるいは、μaで３０００〜５０００程度のものし
か得られなかった。As described above, the principle for high performance in μa and Pcv is in a trade-off relationship, and it has been difficult to obtain a high-performance Mn-Zn-based ferrite satisfying both of them in the past, at 100 kHz, 2000 G, 100 Under the conditions of ° C, only Pcv of about 350 to 500 (kW / m 3 ) or μa of about 3000 to 5000 was obtained.
【０００７】[0007]
【発明が解決しようとする課題】本発明は、前述の問題
点を解決し、より高性能な、高いμaを有する低損失酸
化物磁性材料を提供することにある。SUMMARY OF THE INVENTION It is an object of the present invention to solve the above-mentioned problems and to provide a high-performance, low-loss oxide magnetic material having a high μa.
【０００８】[0008]
【課題を解決するための手段】前述した如く、Ｍｎ−Ｚ
ｎ系フェライトは、ＳｉＯ2、ＣａＯ等を主成分とした
粒界相が存在しており、この粒界相により、フェライト
焼結体の高抵抗化が図られ、渦電流損失が低減され、低
損失化が実現できるものである。As described above, Mn-Z
The n-type ferrite has a grain boundary phase composed mainly of SiO 2 , CaO, etc. This grain boundary phase increases the resistance of the ferrite sintered body, reduces the eddy current loss, and reduces the eddy current loss. It is possible to realize loss.
【０００９】ところが、高抵抗化により渦電流損失を低
減させるために、ＳｉＯ2、ＣａＯ等の副成分量を増加
させ、粒界相を厚くし過ぎると、逆に粒界相による応力
が大きくなり、磁性を担うマトリックス相の磁気特性、
例えば、μaの劣化、Ｈｃの増大を招き、高性能化を図
ることがきない。However, in order to reduce the eddy current loss by increasing the resistance, if the amount of subcomponents such as SiO 2 and CaO is increased and the grain boundary phase is made too thick, the stress due to the grain boundary phase becomes large on the contrary. , The magnetic properties of the matrix phase responsible for magnetism,
For example, deterioration of μa and increase of Hc are caused, and high performance cannot be achieved.
【００１０】又、マトリックス相中に残存する空隙中に
は、ＳｉＯ2、ＣａＯ等の副成分が高濃度に残留する。
このため、これらの副成分量の増加は、磁壁の滑らかな
移動の妨げとなり、μa、μi等の劣化を引き起こす原因
ともなっている。Further, in the voids remaining in the matrix phase, secondary components such as SiO 2 and CaO remain in high concentration.
For this reason, the increase in the amount of these sub-components hinders the smooth movement of the domain wall, and causes deterioration of μa, μi, and the like.
【００１１】逆に、ＳｉＯ2、ＣａＯ等の副成分の量を
減少させ、粒界相を、例えば、全く存在しないような状
態にすると、μa、μi等は、著しく高い値が得られる。
しかし、電気抵抗が著しく小さくなるため、渦電流損失
が大きくなり、Ｐcvの低下は図れない上、μa、μiの周
波数特性も著しく劣化する欠点が生じる。On the contrary, when the amounts of the subcomponents such as SiO 2 and CaO are reduced so that the grain boundary phase does not exist at all, for example, μa, μi, etc. have remarkably high values.
However, since the electric resistance is remarkably reduced, the eddy current loss is increased, Pcv cannot be reduced, and the frequency characteristics of μa and μi are significantly deteriorated.
【００１２】本発明者は、種々検討を行った結果、Ｓ
ｉＯ2量を極力少なく含有せしめる、Ｔａ2Ｏ5あるい
はＮｂ2Ｏ5を含有するＣａＯを主成分とする粒界相を形
成させる、ことにより、前述した二律背反の関係による
影響を極力小さくし、低いＰcvで、かつ、高いμaを有
する高性能なＭｎ−Ｚｎ系フェライトを提供できること
を見い出したものである。As a result of various investigations, the present inventor found that S
By making the amount of iO 2 as small as possible and forming a grain boundary phase containing CaO containing Ta 2 O 5 or Nb 2 O 5 as the main component, the influence of the above-mentioned trade-off relationship is minimized and reduced. It has been found that a high-performance Mn-Zn-based ferrite having Pcv and high μa can be provided.
【００１３】即ち、本発明は、主成分として５２〜５４
ｍｏｌ％の酸化鉄（Ｆｅ2Ｏ3）、３３〜３７ｍｏｌ％の
酸化マンガン（ＭｎＯ）及び残部酸化亜鉛（ＺｎＯ）か
らなり、副成分として０.００１〜０.００８ｗｔ％の二
酸化珪素（ＳｉＯ2）及び０.０２〜０.１０ｗｔ％の酸
化カルシウム（ＣａＯ）を含有し、更に、０〜０.０６
ｗｔ％（０を含まず）の酸化タンタル（Ｔａ2Ｏ5）、又
は０〜０.０２ｗｔ％（０を含まず）の酸化ニオブ（Ｎ
ｂ2Ｏ5）を含有し、かつ、Ｔａ2Ｏ5及びＮｂ2Ｏ5の総量
で０〜０.０６ｗｔ％（０を含まず）含有することを特
徴とする低損失酸化物磁性材料である。That is, according to the present invention, the main components are 52 to 54.
Consists of mol% iron oxide (Fe 2 O 3 ), 33 to 37 mol% manganese oxide (MnO) and balance zinc oxide (ZnO), and 0.001 to 0.008 wt% silicon dioxide (SiO 2 ) as a subcomponent. And 0.02 to 0.10 wt% calcium oxide (CaO), and further 0 to 0.06.
wt% (not including 0) tantalum oxide (Ta 2 O 5 ) or 0 to 0.02 wt% (not including 0) niobium oxide (N)
b 2 O 5 ), and a total content of Ta 2 O 5 and Nb 2 O 5 of 0 to 0.06 wt% (not including 0), which is a low loss oxide magnetic material. .
【００１４】本発明において、Ｔａ2Ｏ5及びＮｂ2Ｏ5を
用いたのは、上述した問題点を解決できる上、異常粒成
長等の組織不整のない結晶粒径の均一な組織が得られる
ため、ヒステリシス損失の低減が可能となり、更に、Ｔ
ａ2Ｏ5及び、あるいはＮｂ2Ｏ5を含有するＣａＯを主成
分とする粒界相が形成され、渦電流損失の低減が可能と
なるためである。従って、ＳｉＯ2を極力少なく含有さ
せた場合においても、これまで達成できなかった低いＰ
cvで、かつ、高いμaを含有するＭｎ−Ｚｎ系フェライ
トを得ることができる。In the present invention, the use of Ta 2 O 5 and Nb 2 O 5 can solve the above-mentioned problems and can obtain a structure having a uniform crystal grain size without irregularities such as abnormal grain growth. Therefore, it is possible to reduce the hysteresis loss.
This is because a grain boundary phase containing Ca 2 O 5 and / or CaO containing Nb 2 O 5 as a main component is formed, and eddy current loss can be reduced. Therefore, even if the content of SiO 2 is as small as possible, the low P that could not be achieved until now.
It is possible to obtain a Mn-Zn-based ferrite containing cv and high μa.
【００１５】又、本発明において、Ｆｅ2Ｏ3を５２〜５
４ｍｏｌ％、ＭｎＯを３３〜３７ｍｏｌ％の組成範囲と
したのは、通常、電源トランス材が使用される環境下で
ある、６０〜１００℃程度の温度範囲では、主成分であ
るＦｅ2Ｏ3及びＭｎＯの組成に強く依存するＰcvの温度
特性が負であり、かつ、Ｐcvが低いからである。Further, in the present invention, Fe 2 O 3 is contained in an amount of 52-5.
The composition range of 4 mol% and MnO of 33 to 37 mol% is usually in the environment where the power transformer material is used. In the temperature range of about 60 to 100 ° C., the main components of Fe 2 O 3 and This is because the temperature characteristic of Pcv, which strongly depends on the composition of MnO, is negative and Pcv is low.
【００１６】更に、ＳｉＯ2を０.００１〜０.００８ｗ
ｔ％、ＣａＯを０.０２〜０.１０ｗｔ％としたのは、下
限値以下では、粒界相がほとんど形成されず、渦電流損
失が著しく増大し、低いＰcvが得られないためであり、
又、上限値を越えた領域においては、高いμaが得られ
ないためである。Further, SiO 2 is 0.001 to 0.008 w.
The reason why t% and CaO are set to 0.02 to 0.10 wt% is that the grain boundary phase is hardly formed, the eddy current loss is significantly increased and a low Pcv cannot be obtained at the lower limit value or less.
Also, in a region exceeding the upper limit value, a high μa cannot be obtained.
【００１７】Ｔａ2Ｏ5を０〜０.０６ｗｔ％（０を除
く）、Ｎｂ2Ｏ5を０〜０.０２ｗｔ％（０を除く）とし
た理由は、各添加物共に上限値を越えても、高抵抗化に
より渦電流損失が低減でき、低いＰcvが得られる領域も
あるが、マトリックス中の空隙が多くなる等、組織制御
が困難となり、高いμaが得られないためである。The reason for setting Ta 2 O 5 to 0 to 0.06 wt% (excluding 0) and Nb 2 O 5 to 0 to 0.02 wt% (excluding 0) is that each additive exceeds the upper limit. Also, although there is a region in which eddy current loss can be reduced by increasing the resistance and low Pcv can be obtained, it is difficult to control the structure such as an increase in voids in the matrix and a high μa cannot be obtained.
【００１８】又、Ｔａ2Ｏ5とＮｂ2Ｏ5の総量を０〜０.
０６ｗｔ％（０を除く）とした理由は、０.０６ｗｔ％
を越えた領域では、同様に、組織制御が困難であり、低
いＰcv、高いμaが得られないためである。The total amount of Ta 2 O 5 and Nb 2 O 5 is 0 to 0.
The reason for setting 06 wt% (excluding 0) is 0.06 wt%
This is because it is difficult to control the structure in a region exceeding the above range, and low Pcv and high μa cannot be obtained.
【００１９】[0019]
【発明の実施の形態】以下、本発明に係わる低損失酸化
物磁性材料の実施例について説明する。BEST MODE FOR CARRYING OUT THE INVENTION Examples of the low loss oxide magnetic material according to the present invention will be described below.
【００２０】（実施例１）高純度のＦｅ2Ｏ3、Ｍｎ3Ｏ4
及びＺｎＯ原料を用いて、５２.８Ｆｅ2Ｏ3−３６.０Ｍ
ｎＯ−１１.２ＺｎＯ（ｍｏｌ％）となるように秤量
し、ボールミルで混合した後、９００℃の大気中で２時
間仮焼した。Example 1 High-purity Fe 2 O 3 and Mn 3 O 4
And ZnO raw material, 52.8Fe 2 O 3 -36.0M
It was weighed so as to be nO-11.2 ZnO (mol%), mixed with a ball mill, and then calcined in the atmosphere at 900 ° C. for 2 hours.
【００２１】次に、この仮焼粉末に、ＣａＯを０.０５
ｗｔ％添加し、更に、Ｔａ2Ｏ5を０.０３ｗｔ％添加
し、ＳｉＯ2を０.００１〜０.０１２ｗｔ％（０を含ま
ず）の範囲で添加した後、ボールミルにて更に微粉砕
（解砕）を行った。Then, CaO was added to the calcined powder in an amount of 0.05.
was added wt%, further, the Ta 2 O 5 was added 0.03 wt%, was added in the range of the SiO 2 0.001~0.012wt% (0 not including), further finely pulverized in a ball mill ( Crushing) was performed.
【００２２】更に、ポリビニルアルコール（ＰＶＡ）を
バインダーとして０.５ｗｔ％添加し、スプレードライ
ヤーにて乾燥・造粒した。Further, polyvinyl alcohol (PVA) was added as a binder in an amount of 0.5 wt% and dried and granulated with a spray dryer.
【００２３】得られた造粒体を、外径３０ｍｍ×内径２
０ｍｍ×高さ１０ｍｍのトロイダル形状に加圧成形した
後、１２００〜１４００℃で窒素と酸素の混合気流中で
酸素分圧が０.５〜１０％となるよう焼成した。The obtained granules were treated with an outer diameter of 30 mm and an inner diameter of 2
After pressure forming into a toroidal shape of 0 mm × height 10 mm, it was fired at 1200 to 1400 ° C. in a mixed air flow of nitrogen and oxygen so that the oxygen partial pressure was 0.5 to 10%.
【００２４】図１に、Ｍｎ−Ｚｎ系フェライト焼結体に
おけるＳｉＯ2含有量を変化させた時のＰcv及びμaの値
の変化を示す。ここで、Ｐcv及びμaは、１００ｋＨ
ｚ，２０００Ｇ，１００℃における値を示した。FIG. 1 shows the changes in the values of Pcv and μa when the SiO 2 content in the Mn-Zn ferrite sintered body was changed. Here, Pcv and μa are 100 kH
The values at z, 2000 G and 100 ° C. are shown.
【００２５】図１に示す如く、ＳｉＯ2含有量が０.００
１〜０.００８ｗｔ％の範囲で低いＰcv、かつ、高いμa
値を示すことがわかる。As shown in FIG. 1, the SiO 2 content is 0.00
Low Pcv and high μa in the range of 1 to 0.008 wt%
It turns out that it shows a value.
【００２６】（実施例２）実施例１で得られた仮焼粉末
に、ＳｉＯ2を０.００４ｗｔ％、Ｎｂ2Ｏ5を０.０１ｗ
ｔ％添加し、ＣａＯを０.０１〜０.１３ｗｔ％の範囲で
添加し、実施例１と同様の製造方法により焼結体を作製
した。Example 2 The calcined powder obtained in Example 1 contains 0.002 wt% of SiO 2 and 0.01 w of Nb 2 O 5 .
t% was added, CaO was added in the range of 0.01 to 0.13 wt%, and a sintered body was manufactured by the same manufacturing method as in Example 1.
【００２７】図２に、Ｍｎ−Ｚｎ系フェライト焼結体に
おけるＣａＯ含有量を変化させた時のＰcv値及びμa値
の変化を示す。図２に示す如く、ＣａＯ含有量が０.０
２〜０.１０ｗｔ％の範囲で低いＰcv、かつ、高いμa値
を示すことがわかる。FIG. 2 shows changes in the P cv value and the μa value when the CaO content in the Mn-Zn ferrite sintered body was changed. As shown in FIG. 2, the CaO content is 0.0
It can be seen that a low Pcv and a high μa value are exhibited in the range of 2 to 0.10 wt%.
【００２８】（実施例３）実施例１で得られた仮焼粉末
に、ＳｉＯ2を０.００４ｗｔ％、ＣａＯを０.０６ｗｔ
％添加し、更に、Ｔａ2Ｏ5を０〜０.０９ｗｔ％の範囲
で添加し、実施例１と同一の製造方法により焼結体を作
製した。(Example 3) The calcined powder obtained in Example 1 contains 0.002 wt% of SiO 2 and 0.06 wt of CaO.
%, And Ta 2 O 5 was further added in the range of 0 to 0.09 wt%, and a sintered body was manufactured by the same manufacturing method as in Example 1.
【００２９】図３に、Ｍｎ−Ｚｎ系フェライト焼結体に
おけるＴａ2Ｏ5含有量とＰcv、μaとの関係を示す。こ
こで、Ｐcv及びμaは、１００ｋＨｚ，２０００Ｇ，１
００℃における値を示した。FIG. 3 shows the relationship between the Ta 2 O 5 content and Pcv, μa in the Mn-Zn system ferrite sintered body. Here, Pcv and μa are 100 kHz, 2000 G, 1
The value at 00 ° C is shown.
【００３０】図３より、Ｔａ2Ｏ5含有量が０〜０.０６
ｗｔ％（０を含まず）の範囲で、低いＰcv、かつ、高い
μa値を示すことがわかる。According to FIG. 3, the content of Ta 2 O 5 is 0 to 0.06.
It can be seen that a low Pcv and a high μa value are exhibited in the range of wt% (not including 0).
【００３１】（実施例４）実施例１で得られた仮焼粉末
に、ＳｉＯ2を０.００４ｗｔ％、ＣａＯを０.０６ｗｔ
％添加し、更に、Ｎｂ2Ｏ5を０〜０.０３ｗｔ％の範囲
で添加し、実施例１と同一の製造方法により焼結体を作
製した。Example 4 The calcined powder obtained in Example 1 contains 0.002 wt% of SiO 2 and 0.06 wt of CaO.
%, And Nb 2 O 5 was further added in the range of 0 to 0.03 wt%, and a sintered body was manufactured by the same manufacturing method as in Example 1.
【００３２】図４に、Ｍｎ−Ｚｎ系フェライト焼結体に
おけるＮｂ2Ｏ5含有量とＰcv、μaとの関係を示す。こ
こで、Ｐcv及びμaは、１００ｋＨｚ，２０００Ｇ，１
００℃における値を示した。FIG. 4 shows the relationship between the Nb 2 O 5 content and Pcv, μa in the Mn-Zn system ferrite sintered body. Here, Pcv and μa are 100 kHz, 2000 G, 1
The value at 00 ° C is shown.
【００３３】図４より、Ｎｂ2Ｏ5含有量が０〜０.０２
ｗｔ％（０を含まず）の範囲で、低いＰcv、かつ、高い
μa値を示すことがわかる。From FIG. 4, the Nb 2 O 5 content is 0 to 0.02.
It can be seen that a low Pcv and a high μa value are exhibited in the range of wt% (not including 0).
【００３４】（実施例５）実施例１で得られた仮焼粉末
に、ＳｉＯ2を０.００５ｗｔ％、ＣａＯを０.０７ｗｔ
％添加し、更にＴａ2Ｏ5を０〜０.０８ｗｔ％、Ｎｂ2Ｏ
5を０〜０.０３ｗｔ％の範囲で同時添加し、実施例１と
同一の製造方法により焼結体を作製した。Example 5 The calcined powder obtained in Example 1 contains 0.002 wt% of SiO 2 and 0.07 wt of CaO.
%, Ta 2 O 5 is further added in an amount of 0 to 0.08 wt%, Nb 2 O
5 was simultaneously added in the range of 0 to 0.03 wt%, and a sintered body was manufactured by the same manufacturing method as in Example 1.
【００３５】表１に、Ｍｎ−Ｚｎ系フェライト焼結体に
おけるＴａ2Ｏ5及びＮｂ2Ｏ5含有量を変化させた時のＰ
cv値及びμa値の変化を示す。Table 1 shows P when the contents of Ta 2 O 5 and Nb 2 O 5 in the Mn-Zn system ferrite sintered body were changed.
The changes in cv value and μa value are shown.
【００３６】 [0036]
【００３７】表１より、Ｔａ2Ｏ5とＮｂ2Ｏ5の総量が０
〜０.０６ｗｔ％（０を含まず）の範囲で含有せしめる
ことにより、低いＰcv、かつ、高いμa値を示すことが
わかる。From Table 1, the total amount of Ta 2 O 5 and Nb 2 O 5 is 0.
It can be seen that when the content is in the range of 0.06 wt% (not including 0), low Pcv and high μa value are exhibited.
【００３８】[0038]
【発明の効果】以上、述べた如く、本発明によれば、よ
り高性能で、高いμaを有する低損失酸化物磁性材料を
提供することができ、工業的にも極めて有益である。As described above, according to the present invention, it is possible to provide a high-performance low-loss oxide magnetic material having a high μa, which is extremely useful industrially.
【図面の簡単な説明】[Brief description of the drawings]
【図１】実施例１におけるＭｎ−Ｚｎ系フェライト焼結
体のＳｉＯ2含有量とＰcv、μaとの関係を示す図。FIG. 1 is a diagram showing the relationship between the SiO 2 content and Pcv, μa of a Mn—Zn ferrite sintered body in Example 1.
【図２】実施例２におけるＭｎ−Ｚｎ系フェライト焼結
体のＣａＯ含有量とＰcv、μaとの関係を示す図。FIG. 2 is a diagram showing the relationship between the CaO content and Pcv, μa of the Mn—Zn ferrite sintered body in Example 2.
【図３】実施例３におけるＭｎ−Ｚｎ系フェライト焼結
体のＴａ2Ｏ5含有量とＰcv、μaとの関係を示す図。FIG. 3 is a diagram showing the relationship between the Ta 2 O 5 content and Pcv, μa of the Mn—Zn based ferrite sintered body in Example 3.
【図４】実施例４におけるＭｎ−Ｚｎ系フェライト焼結
体のＮｂ2Ｏ5含有量とＰcv、μaとの関係を示す図。FIG. 4 is a diagram showing the relationship between the Nb 2 O 5 content and Pcv, μa of the Mn—Zn system ferrite sintered body in Example 4.
Claims (1)
鉄（Ｆｅ2Ｏ3）、３３〜３７ｍｏｌ％の酸化マンガン
（ＭｎＯ）及び残部酸化亜鉛（ＺｎＯ）からなり、副成
分として０.００１〜０.００８ｗｔ％の二酸化珪素（Ｓ
ｉＯ2）及び０.０２〜０.１０ｗｔ％の酸化カルシウム
（ＣａＯ）を含有し、更に、０〜０.０６ｗｔ％（０を
含まず）の酸化タンタル（Ｔａ2Ｏ5）、又は０〜０.０
２ｗｔ％（０を含まず）の酸化ニオブ（Ｎｂ2Ｏ5）を含
有し、かつ、Ｔａ2Ｏ5及びＮｂ2Ｏ5の総量で０〜０.０
６ｗｔ％（０を含まず）含有することを特徴とする低損
失酸化物磁性材料。1. A main component comprising 52 to 54 mol% iron oxide (Fe 2 O 3 ), 33 to 37 mol% manganese oxide (MnO) and the balance zinc oxide (ZnO), and 0.001 to 0 as a subcomponent. 0.008 wt% silicon dioxide (S
iO 2) and containing 0.02～0.10Wt% of calcium oxide (CaO), further, tantalum oxide 0~0.06wt% (0 not including) (Ta 2 O 5), or 0-0 .0
It contains 2 wt% (not including 0) of niobium oxide (Nb 2 O 5 ), and the total amount of Ta 2 O 5 and Nb 2 O 5 is 0 to 0.0.
A low loss oxide magnetic material containing 6 wt% (not including 0).
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP7350402A JPH09180926A (en) | 1995-12-22 | 1995-12-22 | Low loss oxide magnetic material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP7350402A JPH09180926A (en) | 1995-12-22 | 1995-12-22 | Low loss oxide magnetic material |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH09180926A true JPH09180926A (en) | 1997-07-11 |
Family
ID=18410257
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP7350402A Pending JPH09180926A (en) | 1995-12-22 | 1995-12-22 | Low loss oxide magnetic material |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH09180926A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001220146A (en) * | 2000-02-07 | 2001-08-14 | Hitachi Metals Ltd | Low-loss ferrite and magnetic core using the same |
| JP2015229626A (en) * | 2014-06-06 | 2015-12-21 | Ｊｆｅケミカル株式会社 | Mn-Zn-Co FERRITE AND PRODUCTION METHOD THEREOF |
| JP2015229625A (en) * | 2014-06-06 | 2015-12-21 | Ｊｆｅケミカル株式会社 | Mn-Zn-Co FERRITE AND PRODUCTION METHOD THEREOF |
-
1995
- 1995-12-22 JP JP7350402A patent/JPH09180926A/en active Pending
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001220146A (en) * | 2000-02-07 | 2001-08-14 | Hitachi Metals Ltd | Low-loss ferrite and magnetic core using the same |
| JP2015229626A (en) * | 2014-06-06 | 2015-12-21 | Ｊｆｅケミカル株式会社 | Mn-Zn-Co FERRITE AND PRODUCTION METHOD THEREOF |
| JP2015229625A (en) * | 2014-06-06 | 2015-12-21 | Ｊｆｅケミカル株式会社 | Mn-Zn-Co FERRITE AND PRODUCTION METHOD THEREOF |
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