JP2006213530A - Mn-Zn-Ni-BASED FERRITE - Google Patents
Mn-Zn-Ni-BASED FERRITE Download PDFInfo
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- 229910000859 α-Fe Inorganic materials 0.000 title claims abstract description 50
- UQSXHKLRYXJYBZ-UHFFFAOYSA-N Iron oxide Chemical compound [Fe]=O UQSXHKLRYXJYBZ-UHFFFAOYSA-N 0.000 claims abstract description 50
- 230000035699 permeability Effects 0.000 claims abstract description 34
- ZAMOUSCENKQFHK-UHFFFAOYSA-N Chlorine atom Chemical compound [Cl] ZAMOUSCENKQFHK-UHFFFAOYSA-N 0.000 claims abstract description 31
- 239000000460 chlorine Substances 0.000 claims abstract description 31
- 229910052801 chlorine Inorganic materials 0.000 claims abstract description 31
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 26
- 229910007567 Zn-Ni Inorganic materials 0.000 claims abstract description 20
- 229910007614 Zn—Ni Inorganic materials 0.000 claims abstract description 20
- 239000000654 additive Substances 0.000 claims abstract description 8
- 230000000996 additive effect Effects 0.000 claims abstract description 8
- 230000004907 flux Effects 0.000 claims description 48
- 229910004298 SiO 2 Inorganic materials 0.000 claims description 10
- 239000002994 raw material Substances 0.000 claims description 10
- FBAFATDZDUQKNH-UHFFFAOYSA-M iron chloride Chemical compound [Cl-].[Fe] FBAFATDZDUQKNH-UHFFFAOYSA-M 0.000 claims description 5
- 238000010438 heat treatment Methods 0.000 abstract description 24
- 230000006698 induction Effects 0.000 abstract description 12
- 239000000463 material Substances 0.000 abstract description 8
- 229910052742 iron Inorganic materials 0.000 abstract description 4
- 230000001105 regulatory effect Effects 0.000 abstract 1
- 239000011162 core material Substances 0.000 description 14
- 238000010304 firing Methods 0.000 description 11
- 239000000203 mixture Substances 0.000 description 10
- 230000000694 effects Effects 0.000 description 8
- 230000007423 decrease Effects 0.000 description 7
- 238000000034 method Methods 0.000 description 6
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- 239000007864 aqueous solution Substances 0.000 description 4
- 239000000696 magnetic material Substances 0.000 description 4
- 238000002156 mixing Methods 0.000 description 4
- 239000000843 powder Substances 0.000 description 4
- 230000008569 process Effects 0.000 description 4
- 235000013339 cereals Nutrition 0.000 description 3
- 239000013078 crystal Substances 0.000 description 3
- 230000006872 improvement Effects 0.000 description 3
- 239000012535 impurity Substances 0.000 description 3
- 150000002500 ions Chemical class 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- MBMLMWLHJBBADN-UHFFFAOYSA-N Ferrous sulfide Chemical compound [Fe]=S MBMLMWLHJBBADN-UHFFFAOYSA-N 0.000 description 2
- 229910000831 Steel Inorganic materials 0.000 description 2
- 229910010413 TiO 2 Inorganic materials 0.000 description 2
- 230000002159 abnormal effect Effects 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 239000012141 concentrate Substances 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 230000005389 magnetism Effects 0.000 description 2
- 239000007769 metal material Substances 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 229910052760 oxygen Inorganic materials 0.000 description 2
- 239000000700 radioactive tracer Substances 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- 239000010959 steel Substances 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 238000004804 winding Methods 0.000 description 2
- 229910018605 Ni—Zn Inorganic materials 0.000 description 1
- 240000007594 Oryza sativa Species 0.000 description 1
- 235000007164 Oryza sativa Nutrition 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 238000001354 calcination Methods 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000000748 compression moulding Methods 0.000 description 1
- 238000009499 grossing Methods 0.000 description 1
- 230000020169 heat generation Effects 0.000 description 1
- 230000005415 magnetization Effects 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000010298 pulverizing process Methods 0.000 description 1
- 235000009566 rice Nutrition 0.000 description 1
- 230000000630 rising effect Effects 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 238000005245 sintering Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 229910052596 spinel Inorganic materials 0.000 description 1
- 239000011029 spinel Substances 0.000 description 1
- 230000007480 spreading Effects 0.000 description 1
- 238000003892 spreading Methods 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- 238000005406 washing Methods 0.000 description 1
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- Compounds Of Iron (AREA)
- Magnetic Ceramics (AREA)
- Soft Magnetic Materials (AREA)
Abstract
Description
本発明は、周波数が20ｋＨz〜60ｋＨz程度の高周波電流による誘導加熱方式により加熱を行う電磁調理器、電子写真式複写機、プリンタおよびファクシミリの加熱定着装置等の磁性部品に用いて好適な、高いキュリー点と、高い飽和磁束密度、比透磁率を有するMn−Zn−Ni系フェライトに関するものである。 The present invention is a high curie suitable for use in magnetic parts such as an electromagnetic cooker, an electrophotographic copying machine, a printer, and a heat fixing device of a facsimile machine that heats by an induction heating method using a high-frequency current having a frequency of about 20 kHz to 60 kHz. The present invention relates to an Mn-Zn-Ni ferrite having a point, a high saturation magnetic flux density, and a relative magnetic permeability.
誘導加熱は、高周波インバータにより加熱コイルに高周波電流を供給してコイル周辺に高周波磁界を発生させ、この磁界により被加熱物に誘起される渦電流のジュール熱によって加熱する方式である。鉄鋼などの金属材料の加熱、溶解には、古くから用いられてきたが、最近では、電磁調理器や炊飯器さらには電子写真式複写機でトナーを紙に定着させる定着器の加熱等にも用いられている。また、被加熱物が磁性体である場合には、加熱コイルの磁界による磁束分布に応じて、渦電流が被加熱物にも流れ、高周波磁界による鉄損(ヒステリシス損失及び渦電流損失)が発生し、これも発熱に寄与する。 Induction heating is a system in which a high-frequency current is supplied to a heating coil by a high-frequency inverter to generate a high-frequency magnetic field around the coil, and heating is performed by Joule heat of eddy currents induced in an object to be heated by this magnetic field. It has been used for a long time to heat and melt metal materials such as steel, but recently it has also been used to heat fixing machines that fix toner on paper using electromagnetic cookers, rice cookers, and electrophotographic copying machines. It is used. In addition, when the object to be heated is a magnetic material, eddy current flows to the object to be heated according to the magnetic flux distribution due to the magnetic field of the heating coil, and iron loss (hysteresis loss and eddy current loss) due to the high frequency magnetic field occurs. This also contributes to heat generation.
誘導加熱の効率を高めるには、加熱コイルと被加熱物の加熱面の間隔をできるだけ小さくし、加熱コイルからの磁束の多くが被加熱物を貫くようにする必要がある。しかし、コイルと被加熱物の間隔を狭めることには限界がある。そこで、コイルによって発生する磁界から周りの空間に発散する磁束をできるだけ被加熱物に集中させた磁路を形成するため、加熱コイル外側や被加熱物内部の空間に磁性体のコアを配置することが一般に行われている。そして、コイル外側に配置された磁性体のコアは、周囲への漏洩磁束をシールドする役割も果たす。ここで、上記磁性体は、誘導加熱の加熱条件によって適宜選定する必要があるが、上記用途で使用する誘導電流は20ｋＨzから60ｋＨz程度の高周波であるため、金属磁性材料ではなく、酸化物磁性材料のフェライトの方が適している。 In order to increase the efficiency of induction heating, it is necessary to make the distance between the heating coil and the heating surface of the object to be heated as small as possible so that most of the magnetic flux from the heating coil penetrates the object to be heated. However, there is a limit to reducing the distance between the coil and the object to be heated. Therefore, in order to form a magnetic path that concentrates the magnetic flux emanating from the magnetic field generated by the coil in the surrounding space on the object to be heated as much as possible, a magnetic core is disposed outside the heating coil and inside the object to be heated. Is generally done. And the core of the magnetic body arrange | positioned on the coil outer side also plays the role which shields the leakage magnetic flux to the circumference | surroundings. Here, the magnetic material must be appropriately selected according to the heating conditions of induction heating. However, since the induction current used in the above application is a high frequency of about 20 kHz to 60 kHz, it is not a metal magnetic material but an oxide magnetic material. Ferrite is more suitable.
また、複写機の定着器などでは、加熱ロールが、140℃程度から最高200℃以上の温度まで加熱されるため、フェライトコアのキュリー点Ｔcは、これ以上の高い温度であることが必要である。さらに、誘導加熱では、加熱コイルからの高周波磁束を被加熱物および磁路となるコアに集中させることが目的であるから、フェライトコアは、加熱される温度域で誘導コイルからの強い磁界に対する比透磁率が高く、かつ飽和磁束密度が高いことが必要である。 Further, in a fixing device of a copying machine, since the heating roll is heated from about 140 ° C. to a maximum temperature of 200 ° C. or more, the Curie point Tc of the ferrite core needs to be higher than this. . Furthermore, since the purpose of induction heating is to concentrate the high-frequency magnetic flux from the heating coil on the object to be heated and the core that becomes the magnetic path, the ferrite core has a ratio to the strong magnetic field from the induction coil in the heated temperature range. It is necessary that the magnetic permeability is high and the saturation magnetic flux density is high.
現在、高周波域で使用される電源トランスなどの磁芯材料に用いられるフェライトは、Mn−Zn系フェライトが主流となっている。特に、平滑回路のチョークコイルに用いられる磁心材料は、飽和磁束密度が高いことが必要であることから、Ni−Zn系よりも、Mn−Zn系のフェライトの方が有利である。 At present, Mn-Zn ferrite is mainly used as a ferrite used for a magnetic core material such as a power transformer used in a high frequency range. In particular, since the magnetic core material used for the choke coil of the smoothing circuit needs to have a high saturation magnetic flux density, the Mn—Zn ferrite is more advantageous than the Ni—Zn ferrite.
ところで、近年、電子機器の電源部分に対する小型化への要請から、電源部分の各種部品は高密度に積載されるようになってきている。そのため、フェライト材料以外の部品からの発熱量が大きく、積載されているフェライトコアの温度は80〜100℃となることがある。そこで、従来の電源トランス用Mn−Zn系フェライトは、温度上昇とともに飽和磁束密度が低下するため、80℃〜100℃の温度域で最大の飽和磁束密度を有する材料であることが望まれておいた。 By the way, in recent years, various parts of the power supply part have been loaded with high density due to the demand for downsizing the power supply part of the electronic device. Therefore, the amount of heat generated from parts other than the ferrite material is large, and the temperature of the loaded ferrite core may be 80 to 100 ° C. Therefore, the conventional Mn-Zn ferrite for power transformers is desired to be a material having the maximum saturation magnetic flux density in the temperature range of 80 ° C to 100 ° C because the saturation magnetic flux density decreases with increasing temperature. It was.
発明者らは、この要請に応えるべく、80℃で最も高い飽和磁束密度を示すと共に、100ｋＨz〜500ｋＨz程度の周波数域でも低鉄損なMn−Zn−Ni系フェライト磁心材料を、特許文献１に提案した。しかし、このフェライト材料は、電源トランス用として、温度80〜100℃、周波数100ｋＨz以上で低鉄損であることを開発目的としていたため、100℃以上の温度、20ｋＨz〜60ｋＨzの周波数域で、高い飽和磁束密度と比透磁率を求められる誘導加熱用のコアに適用するには、十分な特性とは言えなかった。 In order to meet this demand, the inventors disclosed in Patent Document 1 a Mn-Zn-Ni ferrite core material that exhibits the highest saturation magnetic flux density at 80 ° C. and has low iron loss even in a frequency range of about 100 kHz to 500 kHz. Proposed. However, since this ferrite material was intended to be used for power transformers as a low iron loss at a temperature of 80 to 100 ° C. and at a frequency of 100 kHz or higher, it is high at a temperature of 100 ° C. or higher and a frequency range of 20 kHz to 60 kHz. It could not be said that the characteristics were sufficient to be applied to the core for induction heating that requires the saturation magnetic flux density and the relative magnetic permeability.
また、特許文献２には、酸化鉄の含有量を60〜85mol％とすることにより、高い飽和磁束密度を実現したフェライト焼結体が開示されている。しかし、この技術は、焼成プロセスにおいて、高温保持中の酸素濃度を１％以下に制御する煩雑な操作が必要であり、また、比透磁率も5000以上の大きな値が得られないという問題があった。
そこで、本発明の目的は、キュリー点が300℃以上と高く、100℃以上の温度域かつ20ｋＨz〜60ｋＨzの周波数領域で、高い飽和磁束密度と比透磁率を有するMn−Zn−Ni系フェライトを提供することを目的とする。 Therefore, an object of the present invention is to provide an Mn-Zn-Ni ferrite having a high Curie point of 300 ° C or higher, a temperature range of 100 ° C or higher, and a high saturation magnetic flux density and a relative permeability in a frequency range of 20 kHz to 60 kHz. The purpose is to provide.
発明者らは、上記目的の実現に向けて、MnＯ−ZnＯ−Fe2Ｏ3三元系フェライトに、NiＯ，SiＯ2およびCaＯを含有する成分組成からなるフェライトをベースとし、NiＯの含有量と、上記Fe2Ｏ3の原料となる酸化鉄中に含まれる不純物の含有量とが、最終焼結体であるフェライトコアの飽和磁束密度と比透磁率にどのような影響を及ぼすかに着目して検討を重ねた。その結果、上記成分組成におけるNiＯ含有量を、従来よりも幾分高くするとともに、原料酸化鉄中の塩素量を一定値以下に制限し、最終焼結体中における塩素量を所定値以下に低減すれば、所期した目的を達成することができることを知見し、本発明を完成させた。 In order to achieve the above object, the inventors made MnO-ZnO-Fe 2 O 3 ternary ferrite based on ferrite composed of components containing NiO, SiO 2 and CaO, and the content of NiO Focusing on how the content of impurities contained in the iron oxide that is the raw material of Fe 2 O 3 affects the saturation magnetic flux density and relative permeability of the ferrite core that is the final sintered body Repeated examination. As a result, the content of NiO in the above component composition is made somewhat higher than before, the amount of chlorine in the raw iron oxide is limited to a certain value or less, and the amount of chlorine in the final sintered body is reduced to a predetermined value or less. As a result, it was found that the intended purpose could be achieved, and the present invention was completed.
すなわち、本発明は、基本成分が、Fe2Ｏ3：53〜57mol％、ZnＯ：４〜11mol％、NiＯ：0.5〜４mol％、残部が実質的にMnＯからなり、添加成分として0.005〜0.05mass％のSiＯ2および0.02〜0.2mass％のCaＯを含有するMn−Zn−Ni系フェライトにおいて、前記Fe2Ｏ3原料として、塩素含有量が0.050mass％以下の酸化鉄を用い、得られる最終焼結体中が80massppm以下の塩素を含有するものからなるMn−Zn−Ni系フェライトである。 That is, the present invention is basic component, Fe 2 O 3: 0.005~0.05mass 0.5~4mol %, balance being substantially MnO, as an additive component: 53~57mol%, ZnO: 4~11mol% , NiO % of the Mn-Zn-Ni ferrite containing SiO 2 and 0.02～0.2Mass% of CaO, as the Fe 2 O 3 raw material, the chlorine content using 0.050 mass% or less of iron oxide, obtained final sintered It is Mn-Zn-Ni type ferrite which consists of what contains 80 massppm or less of chlorine in the body.
本発明における上記酸化鉄は、塩化鉄溶液を焙焼して得たものであることを特徴とする。 The iron oxide in the present invention is obtained by roasting an iron chloride solution.
また、本発明のMn−Zn−Ni系フェライトは、キュリー点が300℃以上、140℃における磁化力1200Ａ／ｍでの飽和磁束密度が400ｍＴ以上、140℃における磁束密度300ｍＴ、周波数20ｋＨzおよび60ｋＨzでの比透磁率が5000以上であることを特徴とする。 The Mn-Zn-Ni ferrite of the present invention has a Curie point of 300 ° C. or higher, a saturation magnetic flux density of 400 mT or higher at a magnetizing force of 1200 A / m at 140 ° C., a magnetic flux density of 300 mT at 140 ° C., frequencies of 20 kHz and 60 kHz. The relative magnetic permeability is 5,000 or more.
本発明によれば、キュリー点が300℃以上と高く、100℃以上の温度域、20ｋＨz〜60ｋＨzの周波数領域で高い飽和磁束密度と比透磁率を有するMn−Zn−Ni系フェライトを提供することができる。このフェライト材料は、誘導加熱装置のコア材に用いて好適である。 According to the present invention, there is provided an Mn—Zn—Ni ferrite having a high Curie point of 300 ° C. or higher, a temperature range of 100 ° C. or higher, and a high saturation magnetic flux density and a relative magnetic permeability in a frequency range of 20 kHz to 60 kHz. Can do. This ferrite material is suitable for use as a core material of an induction heating device.
本発明において、Mn−Zn−Ni系フェライトの基本成分組成を、上記範囲に限定する理由について説明する。
Fe2Ｏ3：53〜57mol％
Fe2Ｏ3は、含有量が少なすぎると飽和磁束密度が低下し、飽和磁束密度を高い値に維持するためには、53mol％以上とする必要がある。一方、本発明に係るフェライト磁心材料のように、NiＯを含むものでは、磁性イオンであるNi２＋イオンは、フェライトのスピネル化合物の格子点に入り込み、他の格子点にある磁性イオンとの相互作用を介して、磁気異方性定数Ｋ1ならびに飽和磁歪定数λsを変化させることにより、MnＯ−ZnＯ−Fe2Ｏ3三元系フェライトの比透磁率に関する最適組成範囲をFe2Ｏ3リッチ側に広げる作用を有する。しかし、Fe2Ｏ3の含有量が多過ぎると、NiＯを含む組成でも損失が大きくなり、比透磁率が低下するので、上限を57mol％とする。好ましいFe2Ｏ3の範囲は、54〜56mol％である。
The reason why the basic component composition of the Mn—Zn—Ni ferrite in the present invention is limited to the above range will be described.
Fe 2 O 3: 53~57mol%
If the content of Fe 2 O 3 is too small, the saturation magnetic flux density decreases, and in order to maintain the saturation magnetic flux density at a high value, it is necessary to make it 53 mol% or more. On the other hand, in the case where NiO is contained like the ferrite magnetic core material according to the present invention, Ni 2+ ions that are magnetic ions enter the lattice points of the spinel compound of ferrite and interact with the magnetic ions at other lattice points. By changing the magnetic anisotropy constant K 1 and the saturation magnetostriction constant λ s, the optimum composition range for the relative permeability of the MnO—ZnO—Fe 2 O 3 ternary ferrite is set to the Fe 2 O 3 rich side. Has the effect of spreading. However, if the content of Fe 2 O 3 is too large, even the composition containing NiO increases the loss and decreases the relative magnetic permeability, so the upper limit is set to 57 mol%. A preferable range of Fe 2 O 3 is 54 to 56 mol%.
ZnＯ：４〜11mol％
ZnＯは、含有量が少なすぎると飽和磁束密度が小さくなるが、Fe2Ｏ3とNiＯの組成を好適範囲に選択すれば、高い飽和磁束密度を維持することができる。一方、ZnＯの含有量が少ない場合、100ｋＨz以下では比透磁率が低下するため、ZnＯの含有量は４mol％以上とする必要がある。しかし、ZnＯの含有量が多すぎると、室温での飽和磁束密度が小さくなるだけでなく、キュリー温度が低下する。また、ZnＯの含有量が多すぎると、NiＯの比透磁率の向上効果がなくなってしまう。従って、ZnＯの含有量は、上限を11mol％とする。好ましいZnＯの範囲は、６〜10mol％である。
ZnO: 4-11 mol%
If the content of ZnO is too small, the saturation magnetic flux density decreases. However, if the composition of Fe 2 O 3 and NiO is selected within a suitable range, a high saturation magnetic flux density can be maintained. On the other hand, when the content of ZnO is small, the relative permeability decreases at 100 kHz or less, so the content of ZnO needs to be 4 mol% or more. However, when the content of ZnO is too large, not only the saturation magnetic flux density at room temperature is reduced, but also the Curie temperature is lowered. Moreover, when there is too much content of ZnO, the improvement effect of the relative permeability of NiO will be lost. Therefore, the upper limit of the ZnO content is 11 mol%. A preferable range of ZnO is 6 to 10 mol%.
NiＯ：0.5〜４mol％
NiＯは、比透磁率を向上する成分である。しかし、その含有量が0.5mol％に満たない場合には、比透磁率の改善効果が顕著でなく、飽和磁束密度も小さい。一方、NiＯの含有量が多すぎると、100ｋＨz程度までの周波数帯域で損失が急激に増大し、比透磁率も低減するため、NiＯの含有量は４mol％を上限とする。なお、従来技術との比較の意味で、NiＯの含有量をmass％で表示すると0.3〜2.5mass％となる。この数値からも明らかなように、本発明にかかるフェライト磁心材料は、従来の材料に比べてNiＯの含有量を幾分多めに設定している。その理由は、NiＯは、MnＯ−ZnＯ−Fe2Ｏ3三元系フェライトに容易に固溶する酸化物で、かつ、磁性の向上に寄与するものだからであり、また、従来よりも多くする理由は、飽和磁束密度の向上とキュリー温度の上昇に有効だからである。なお、好ましいNiＯの範囲は、２〜４mol％である。
本発明のフェライト材料は、上記Fe2Ｏ3，ZnＯ，NiＯ以外の残部は、実質的にMnＯからなる基本成分で構成されている。
NiO: 0.5-4 mol%
NiO is a component that improves the relative magnetic permeability. However, when the content is less than 0.5 mol%, the effect of improving the relative magnetic permeability is not remarkable and the saturation magnetic flux density is small. On the other hand, if the content of NiO is too large, the loss rapidly increases in the frequency band up to about 100 kHz and the relative magnetic permeability also decreases, so the NiO content is limited to 4 mol%. In addition, in terms of comparison with the prior art, when the content of NiO is expressed in mass%, it becomes 0.3 to 2.5 mass%. As is clear from this numerical value, the ferrite magnetic core material according to the present invention has a slightly higher NiO content than the conventional material. The reason is that NiO is an oxide that readily dissolves in MnO—ZnO—Fe 2 O 3 ternary ferrite and contributes to the improvement of magnetism, and the reason why it is increased more than before. This is because it is effective in improving the saturation magnetic flux density and raising the Curie temperature. In addition, the range of preferable NiO is 2-4 mol%.
In the ferrite material of the present invention, the balance other than the above Fe 2 O 3 , ZnO, and NiO is composed of a basic component substantially made of MnO.
次に、本発明のフェライトが必須とする添加成分である、SiＯ2およびCaＯについて説明する。
SiＯ2：0.005〜0.05mass％、CaＯ：0.02〜0.2mass％
SiＯ2およびCaＯは、焼結性を高めると共に、粒界相を高抵抗化して低損失化し、高い比透磁率を実現するために必要不可欠な添加成分である。特に、SiＯ2は、焼結を促進する効果があり、この効果を充分に引き出すためには0.005mass％以上の添加が必要である。しかし、SiＯ2が多すぎると、異常粒成長を起こしたり、飽和磁束密度が低減したりするため、その上限を0.05mass％とする。一方、CaＯは、SiＯ2とともに粒界を高抵抗化して損失を小さくし、比透磁率を高める効果があり、この効果を引き出すためには0.02mass％以上の添加が必要である。しかし、0.2mass％を超えて添加すると、焼結性が悪化するので、その上限を0.2mass％とする。
Next, SiO 2 and CaO, which are essential components of the ferrite of the present invention, will be described.
SiO 2: 0.005~0.05mass%, CaO: 0.02~0.2mass%
SiO 2 and CaO are additive components that are indispensable for improving the sinterability, increasing the resistance of the grain boundary phase to reduce the loss, and realizing a high relative magnetic permeability. In particular, SiO 2 has an effect of promoting sintering, and 0.005 mass% or more is necessary to sufficiently bring out this effect. However, when SiO 2 is too large, or causing abnormal grain growth, the saturation magnetic flux density or reduced, so the upper limit and 0.05 mass%. On the other hand, CaO has the effect of increasing the resistivity of the grain boundary together with SiO 2 to reduce the loss and increasing the relative magnetic permeability. In order to bring out this effect, addition of 0.02 mass% or more is necessary. However, if added over 0.2 mass%, the sinterability deteriorates, so the upper limit is made 0.2 mass%.
また、本発明のMn−Zn−Ni系フェライトは、上述した基本成分および添加成分を必須のとするが、それ以外に、Ta2Ｏ5，ZrＯ2，Nb2Ｏ5，Ｖ2Ｏ5，TiＯ2およびHfＯ2のうちから選ばれるいずれか１種または２種以上の微量添加成分を、Ta2Ｏ5：0.0050〜0.1000mass％、ZrＯ2：0.0100〜0.1500mass％、Nb2Ｏ5：0.0050〜0.0500mass％、Ｖ2Ｏ5：0.0050〜0.0500mass％、TiＯ2：0.0500〜0.3000mass％、HfＯ2：0.0050〜0.0500mass％の範囲で加えることができる。これらの微量添加成分は、いずれも損失改善に寄与し、比透磁率を高める効果がある。 In addition, the Mn—Zn—Ni ferrite of the present invention requires the basic component and the additive component described above, but besides that, Ta 2 O 5 , ZrO 2 , Nb 2 O 5 , V 2 O 5 , Any one or two or more trace addition components selected from TiO 2 and HfO 2 are used, Ta 2 O 5 : 0.0050 to 0.1000 mass%, ZrO 2 : 0.0100 to 0.1500 mass%, Nb 2 O 5 : 0.0050 ˜0.0500 mass%, V 2 O 5 : 0.0050 to 0.0500 mass%, TiO 2 : 0.0500 to 0.3000 mass%, HfO 2 : 0.0050 to 0.0500 mass% can be added. Any of these trace additive components contributes to loss improvement and has an effect of increasing the relative magnetic permeability.
原料酸化鉄中の塩素：0.05mass％以下、最終焼結体中の塩素：80massppm以下
さて、Fe2Ｏ3，ZnＯ，NiＯおよびMnＯの基本成分や添加成分の組成を、上記範囲に調整することは重要なことであるが、それだけでは、大きな飽和磁束密度と比透磁率を同時に確保することができない。そこで、発明者らは、さらに検討を重ねた結果、Fe2Ｏ3の原料となる酸化鉄中の不純物、特に塩素の量を限定することにより、具体的には、原料酸化鉄中の塩素を0.050mass％以下とし、さらに、最終焼結体中に残存する塩素量を80massppm以下に低減することにより、異常粒の発生や結晶粒の粒度分布ばらつきなどの組織不均一が抑制されるとともに、焼結体密度の向上が図られて、飽和磁束密度と比透磁率をさらに向上できることを新たに見出した。なお、Mn−Zn系フェライトにおける、各種不純物の影響については、例えば、文献「フェライト」（平賀ら、丸善、1986、47頁）に記載されているが、原料酸化鉄中の塩素が、磁気特性に対してどのように影響するかについては全く述べられていない。
Chlorine in the raw iron oxide: 0.05 mass% or less, chlorine in the final sintered body: 80 massppm or less Now, the composition of the basic components and additive components of Fe 2 O 3 , ZnO, NiO and MnO should be adjusted to the above ranges. However, it is not possible to secure a large saturation magnetic flux density and relative permeability at the same time. Therefore, as a result of further studies, the inventors limited the amount of impurities, particularly chlorine, in the iron oxide used as the raw material for Fe 2 O 3 , specifically, the chlorine in the raw iron oxide. By reducing the amount of chlorine remaining in the final sintered body to 80 massppm or less by reducing the amount of chlorine to 0.050 mass% or less, structural nonuniformity such as generation of abnormal grains and variation in grain size distribution of crystals is suppressed, and It has been newly found that the density of the solid can be improved and the saturation magnetic flux density and the relative magnetic permeability can be further improved. The influence of various impurities in the Mn-Zn ferrite is described in, for example, the document “Ferrite” (Hiraga et al., Maruzen, 1986, p. 47). Chlorine in the raw iron oxide is a magnetic property. There is no mention of how it will affect.
原料酸化鉄中の塩素が、最終焼結体の特性に影響を及ぼす機構については、まだ明確に解明されたわけではないが、塩素は、Mn−Zn−Ni系フェライトの製造工程においては、原料の酸化鉄のみから混入するものであるため、原料混合後の仮焼工程や焼成工程などの化学反応を伴う工程で結晶成長や結晶組織に影響を与え、最終焼結体の特性、とくに100℃以上の高温度での飽和磁束密度や比透磁率に影響を及ぼすものと考えられる。従って、上記のような反応工程に入る前、すなわち原料酸化鉄の段階で塩素を極力低減しておく必要がある。また、最終焼結体中に残留する塩素量が多いと、焼結体中に空孔が多く残留し、飽和磁束密度と比透磁率の低下が生じるので、これもまた極力低減しておく必要がある。 The mechanism by which chlorine in the raw iron oxide affects the properties of the final sintered body has not yet been clearly elucidated, but chlorine is a source of raw material in the Mn-Zn-Ni ferrite manufacturing process. Since it is mixed only from iron oxide, it affects the crystal growth and crystal structure in the process involving chemical reaction such as calcination process and firing process after mixing raw materials, and the characteristics of the final sintered body, especially 100 ° C or higher This is thought to affect the saturation magnetic flux density and relative permeability at high temperatures. Therefore, it is necessary to reduce chlorine as much as possible before entering the reaction step as described above, that is, at the stage of raw iron oxide. In addition, if there is a large amount of chlorine remaining in the final sintered body, many voids remain in the sintered body, resulting in a decrease in saturation magnetic flux density and relative permeability. This must also be reduced as much as possible. There is.
なお、塩素量の少ない酸化鉄としては、塩素を含まない硫化鉄水溶液を焙焼して得たものが好ましい。しかし、硫化鉄水溶液は、原料コストが高いので、工業的には塩化鉄水溶液を焙焼して得た酸化鉄が好ましく、特に、塩化鉄水溶液から得られる酸化鉄からは、上記焙焼工程後に、熱処理や水洗を行うことによって、塩素含有量が極めて少ない酸化鉄を得ることができるので、この点からも好ましい。 In addition, as iron oxide with little chlorine content, what was obtained by baking the iron sulfide aqueous solution which does not contain chlorine is preferable. However, since the iron sulfide aqueous solution has a high raw material cost, industrially preferred is iron oxide obtained by roasting an iron chloride aqueous solution. In particular, from the iron oxide obtained from an iron chloride aqueous solution, Since iron oxide with extremely low chlorine content can be obtained by performing heat treatment or washing with water, this is also preferable from this point.
次に、本発明のMn−Zn−Ni系フェライトの製造方法について説明する。
通常、Mn−Zn−Ni系フェライトは、各粉末原料を、所定の最終組成になるように混合して仮焼し、次いで、得られたフェライト仮焼粉に各種の添加成分を必要に応じて添加、混合して粉砕した後、造粒して圧縮成形し、焼成することにより製造される。この際、本発明では、酸化鉄の原料として、塩素含有量が、0.050mass％以下のものを用いることが必要である。0.050mass％を超えて塩素を含む場合には、飽和磁束密度や比透磁率に悪影響を及ぼすからである。また、本発明では、焼成工程において焼成温度を高くしたり、焼成時間を長くしたりすることによって、最終焼結体中における塩素量を80massppm以下まで低減することが重要である。というのは、80massppmを超える塩素が残存していると、前述したとおり、焼結体中の空孔が多くなって、飽和磁束密度と比透磁率の低下が生じるからである。
Next, a method for producing the Mn—Zn—Ni ferrite of the present invention will be described.
Usually, Mn-Zn-Ni ferrite is calcined by mixing each powder raw material so as to have a predetermined final composition, and then various additive components are added to the obtained calcined ferrite powder as necessary. It is manufactured by adding, mixing and pulverizing, granulating, compression molding, and firing. At this time, in the present invention, it is necessary to use a raw material for iron oxide having a chlorine content of 0.050 mass% or less. This is because if the chlorine content exceeds 0.050 mass%, the saturation magnetic flux density and the relative magnetic permeability are adversely affected. In the present invention, it is important to reduce the chlorine content in the final sintered body to 80 massppm or less by increasing the firing temperature or extending the firing time in the firing step. This is because, if chlorine exceeding 80 massppm remains, as described above, the number of vacancies in the sintered body increases and the saturation magnetic flux density and the relative permeability are reduced.
また、本発明では、フェライト焼成に当たっては、500℃から最高保持温度までの昇温速度は、600℃／hr以上とすることが好ましい。焼成時の昇温速度が600℃／hrに満たないと、高い飽和磁束密度を実現できず、140℃での飽和磁束密度が、従来材並みの400ｍＴ以下に止まるからである。また、焼成時の最高保持温度は、1300℃以上の高温とすることが好ましい。1300℃未満の場合には、焼結体密度が低くなり、高い飽和磁束密度を得ることが難しくなるからである。なお、保持時間は、組成によっても異なるが、通常１〜８時間程度であり、好ましくは２時間以上とするのがよい。焼成時の雰囲気は、大気または窒素あるいはそれらの混合ガス中で行うことが好ましい。 In the present invention, the rate of temperature increase from 500 ° C. to the maximum holding temperature is preferably 600 ° C./hr or more when firing the ferrite. This is because if the heating rate during firing is less than 600 ° C./hr, a high saturation magnetic flux density cannot be realized, and the saturation magnetic flux density at 140 ° C. is below 400 mT, which is the same level as that of conventional materials. The maximum holding temperature during firing is preferably a high temperature of 1300 ° C. or higher. This is because if the temperature is lower than 1300 ° C., the density of the sintered body becomes low and it becomes difficult to obtain a high saturation magnetic flux density. In addition, although holding time changes also with a composition, it is about 1 to 8 hours normally, Preferably it is 2 hours or more. The firing atmosphere is preferably performed in air, nitrogen, or a mixed gas thereof.
上記成分組成からなり、上記製造方法により製造された本発明のMn−Zn−Ni系フェライトは、キュリー点が300℃以上、140℃における磁化力1200Ａ／ｍでの飽和磁束密度が400ｍＴ以上、140℃における磁束密度300ｍＴ、周波数20ｋＨzおよび60ｋＨzでの比透磁率が5000以上のものであることが好ましい。キュリー点を300℃以上とした理由は、200℃以上の高温になっても十分な磁性を有する必要があるからである。また、140℃における飽和磁束密度と比透磁率を上記の値とした理由は、そのような大きな値を設定することにより、加熱コイルからの大きな磁界に対しても十分な磁束が発生し、かつ磁気飽和しないようにするためである。140℃の飽和磁束密度と比透磁率が重要なのは、まず誘導加熱に用いられたときの使用温度の最低温度がこの付近であり、従来の電源トランス用フェライトでは、80〜100℃の温度域を重視しているため、これより高温、特に140℃付近では、急激に磁気特性が劣化し、大きな比透磁率が得られなくなるからである。 The Mn—Zn—Ni-based ferrite of the present invention, which has the above component composition and is manufactured by the above manufacturing method, has a Curie point of 300 ° C. or higher and a saturation magnetic flux density of 400 mT or higher at a magnetizing force of 1200 A / m at 140 ° C. The relative permeability at a magnetic flux density of 300 mT and frequencies of 20 kHz and 60 kHz is preferably 5000 or more. The reason why the Curie point is set to 300 ° C. or higher is that it needs to have sufficient magnetism even at a high temperature of 200 ° C. or higher. The reason for setting the saturation magnetic flux density and relative permeability at 140 ° C. to the above values is that, by setting such a large value, sufficient magnetic flux is generated even for a large magnetic field from the heating coil, and This is to prevent magnetic saturation. The saturation magnetic flux density of 140 ° C and relative permeability are important because the minimum temperature of the operating temperature when it is used for induction heating is around this range. In conventional power transformer ferrite, the temperature range of 80-100 ° C is used. This is because the emphasis is placed on this, and at higher temperatures, particularly around 140 ° C., the magnetic characteristics deteriorate rapidly and a large relative magnetic permeability cannot be obtained.
塩化鉄の溶液を焙焼して得た酸化鉄を、500℃程度までの温度範囲で再度熱処理したり水洗したりすることにより、種々の量の塩素を含有する原料酸化鉄とした。この酸化鉄を用いて、基本成分であるFe2Ｏ3，ZnＯ，NiＯおよびMnＯが、表１および表２に示すように種々の組成を有するよう、それぞれの原料粉末を混合した後、930℃で３時間の仮焼を行い、さらに、表１および表２に併記したように、種々の量のSiＯ2，CaＯを添加し、ボールミルで10時間粉砕した。その後、この粉砕した粉末を、外径36mm、内径24mm、高さ12mmのリング状に成形した後、酸素分圧を１〜５vol％に制御した窒素・空気混合ガス中で、500℃から1330℃までの昇温速度を650℃／hrで加熱後、1330℃で３時間の焼成を行った。 The iron oxide obtained by roasting the iron chloride solution was heat-treated again in the temperature range up to about 500 ° C. and washed with water to obtain raw iron oxide containing various amounts of chlorine. Using this iron oxide, after mixing each raw material powder so that the basic components Fe 2 O 3 , ZnO, NiO and MnO have various compositions as shown in Tables 1 and 2, 930 ° C. Then, as shown in Tables 1 and 2, various amounts of SiO 2 and CaO were added and pulverized with a ball mill for 10 hours. Thereafter, the pulverized powder was formed into a ring shape having an outer diameter of 36 mm, an inner diameter of 24 mm, and a height of 12 mm, and then in a nitrogen / air mixed gas in which the oxygen partial pressure was controlled to 1 to 5 vol%, from 500 ° C to 1330 ° C. After heating at a temperature rising rate of 650 ° C./hr, firing was performed at 1330 ° C. for 3 hours.
このようにして得たリング状試料に、１次側５巻・２次側５巻の巻線を施し、交流ＢＨループトレーサーを用いて、20℃〜140℃において、20ｋＨz〜60ｋＨzの周波数で磁束密度300ｍＴまで励磁したときの比透磁率を測定した。次に、１次側20巻・２次側40巻の巻線を施し、直流ＢＨループトレーサーを用いて、20℃〜200℃において、1200Ａ／ｍの磁界をかけたときの磁束密度を測定した。なお、この大きさの磁界では、磁束はほぼ飽和しており、この値は飽和磁束密度と見なせる。さらに、これらの焼結体試料を破砕した小片に、試料振動型磁力計で40ｋＡ／ｍの磁界をかけながら500℃まで昇温し、磁化がなくなるキュリー温度を測定した。また、焼結体中に含まれる塩素量の測定も行った。なお、上記原料酸化鉄中および焼結体中の塩素量の測定は、蛍光Ｘ線分析を用いて行った。 The ring-shaped sample thus obtained was wound with 5 turns on the primary side and 5 turns on the secondary side, and the magnetic flux was applied at a frequency of 20 kHz to 60 kHz at 20 ° C to 140 ° C using an AC BH loop tracer. The relative permeability when excited to a density of 300 mT was measured. Next, 20 windings on the primary side and 40 windings on the secondary side were applied, and using a DC BH loop tracer, the magnetic flux density was measured when a magnetic field of 1200 A / m was applied at 20 ° C to 200 ° C. . In this magnitude of magnetic field, the magnetic flux is almost saturated, and this value can be regarded as the saturation magnetic flux density. Furthermore, the temperature was raised to 500 ° C. while applying a magnetic field of 40 kA / m to a small piece obtained by crushing these sintered body samples using a sample vibration type magnetometer, and the Curie temperature at which the magnetization disappeared was measured. The amount of chlorine contained in the sintered body was also measured. The amount of chlorine in the raw iron oxide and the sintered body was measured using fluorescent X-ray analysis.
上記測定の結果を、表１および表２中に併記して示した。なお、比透磁率は、20〜60ｋＨzの範囲での最小値を示した。ここで、表１に示したNo.１〜24の実施例は本発明例であり、表２に示したNo.25〜44の実施例は比較例である。表１からわかるように、本発明の条件を満たしたNo.１〜24は、原料酸化鉄中の塩素量を0.050mass％以下に低減すると共に、焼結体中の塩素量を80massppm以下に抑制した結果、いずれの焼結体も、キュリー点が300℃以上、140℃での飽和磁束密度が400ｍＴ以上、140℃、20ｋＨzおよび60ｋＨz、300ｍＴでの比透磁率が5000以上という優れた特性を有するMn−Zn−Ni系フェライトとなっていることがわかる。これに対して、本発明の条件を満たさないNo.25〜44の比較例は、キュリー点、飽和磁束密度、比透磁率のいずれか１つ以上の特性が劣るものしか得られなかった。 The results of the above measurements are shown together in Tables 1 and 2. In addition, the relative magnetic permeability showed the minimum value in the range of 20-60 kHz. Here, Examples Nos. 1 to 24 shown in Table 1 are examples of the present invention, and Examples Nos. 25 to 44 shown in Table 2 are comparative examples. As can be seen from Table 1, Nos. 1 to 24 satisfying the conditions of the present invention reduce the chlorine content in the raw iron oxide to 0.050 mass% or less and suppress the chlorine content in the sintered body to 80 massppm or less. As a result, all the sintered bodies have excellent characteristics such as Curie point of 300 ° C. or higher, saturation magnetic flux density at 140 ° C. of 400 mT or higher, and relative permeability at 140 ° C., 20 kHz, 60 kHz, and 300 mT of 5000 or higher. It turns out that it is Mn-Zn-Ni type ferrite. On the other hand, the comparative examples of Nos. 25 to 44 that do not satisfy the conditions of the present invention had only inferior one or more characteristics of Curie point, saturation magnetic flux density, and relative permeability.
本発明のフェライトは、鉄鋼などの金属材料の誘導加熱装置にも適用することができる。 The ferrite of the present invention can also be applied to an induction heating device of a metal material such as steel.
Claims (3)
It has a Curie point of 300 ° C or higher, a saturation magnetic flux density of 400 mT or higher at a magnetizing force of 1200 A / m at 140 ° C, a magnetic flux density of 300 mT at 140 ° C, and a relative magnetic permeability of 5000 or higher at frequencies of 20 kHz and 60 kHz. The Mn-Zn-Ni ferrite according to claim 1 or 2.
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|---|---|---|---|---|
| JP2008127230A (en) * | 2006-11-17 | 2008-06-05 | Jfe Ferrite Corp | MnZnNi FERRITE |
| JP2011017767A (en) * | 2009-07-07 | 2011-01-27 | Konica Minolta Business Technologies Inc | Fixing device and image forming apparatus, as well as, heating element |
| JP2012057829A (en) * | 2010-09-06 | 2012-03-22 | Jfe Chemical Corp | Electromagnetic wave-absorbing heating body and cooking utensil for microwave oven |
| JP2016141602A (en) * | 2015-02-03 | 2016-08-08 | Fdk株式会社 | NiMnZn-BASED FERRITE |
| CN107200574A (en) * | 2017-05-12 | 2017-09-26 | 天长市中德电子有限公司 | A kind of low loss soft magnetic ferrite material |
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| JP2003142328A (en) * | 2001-08-20 | 2003-05-16 | Tdk Corp | Method of manufacturing ferrite core |
| JP2003306376A (en) * | 2002-04-10 | 2003-10-28 | Jfe Steel Kk | MANUFACTURING METHOD OF Mn-Zn FERRITE |
| JP2004161500A (en) * | 2002-11-08 | 2004-06-10 | Jfe Chemical Corp | Manganese-zinc-nickel-based ferrite |
| JP2004315312A (en) * | 2003-04-17 | 2004-11-11 | Jfe Steel Kk | Mn-zn-based ferrite |
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| JPH1064715A (en) * | 1996-08-14 | 1998-03-06 | Kawasaki Steel Corp | Low loss ferrite magnetic core material |
| JP2003142328A (en) * | 2001-08-20 | 2003-05-16 | Tdk Corp | Method of manufacturing ferrite core |
| JP2003306376A (en) * | 2002-04-10 | 2003-10-28 | Jfe Steel Kk | MANUFACTURING METHOD OF Mn-Zn FERRITE |
| JP2004161500A (en) * | 2002-11-08 | 2004-06-10 | Jfe Chemical Corp | Manganese-zinc-nickel-based ferrite |
| JP2004315312A (en) * | 2003-04-17 | 2004-11-11 | Jfe Steel Kk | Mn-zn-based ferrite |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008127230A (en) * | 2006-11-17 | 2008-06-05 | Jfe Ferrite Corp | MnZnNi FERRITE |
| JP2011017767A (en) * | 2009-07-07 | 2011-01-27 | Konica Minolta Business Technologies Inc | Fixing device and image forming apparatus, as well as, heating element |
| JP2012057829A (en) * | 2010-09-06 | 2012-03-22 | Jfe Chemical Corp | Electromagnetic wave-absorbing heating body and cooking utensil for microwave oven |
| JP2016141602A (en) * | 2015-02-03 | 2016-08-08 | Fdk株式会社 | NiMnZn-BASED FERRITE |
| CN107200574A (en) * | 2017-05-12 | 2017-09-26 | 天长市中德电子有限公司 | A kind of low loss soft magnetic ferrite material |
| CN107200574B (en) * | 2017-05-12 | 2021-01-01 | 天长市中德电子有限公司 | Low-loss soft magnetic ferrite material |
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| JP4551782B2 (en) | 2010-09-29 |
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