JP2011174103A - Magnetic material for iron core, method for producing the same, and iron core - Google Patents
Magnetic material for iron core, method for producing the same, and iron core Download PDFInfo
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本発明は、小型・軽量化、高出力化及び高効率化が必要とされる各種のモータ等の電動回転機、トランス、リアクトル等に用いる鉄心用磁性材及びその製造方法と、この鉄心用磁性材を用いた鉄心に関するものである。 The present invention relates to a magnetic material for an iron core used for electric rotating machines such as various motors, transformers, reactors, etc., which are required to be small and light, high output and high efficiency, and a method for manufacturing the same, and the magnetic material for the iron core It relates to iron cores made of wood.
近年、カーエレクトロニクスの発展により、自動車には車軸駆動用、ワイパー用、窓開閉用、ミラー駆動用として各種のモータから構成された電動回転機（以下、「回転機」という）が多量に搭載されている。年々、自動車一台当たりの回転機の搭載数は増加しており、車体重量の増加による燃費への影響も無視できなくなりつつある。加えて、地球環境保護の観点からも、自動車搭載用の回転機には小型・軽量化、高出力化及び高効率化が求められるようになってきている。このような回転機の高性能化には、回転機のステータやロータとして使用される鉄心用磁性材には、励磁可能な磁束密度（飽和磁束密度）の向上及び鉄損特性の向上が必要とされる。
同様に、各種のトランスに用いられる鉄心用磁性材からなるコア（鉄心）、あるいはリアクトルの鉄心用磁性材からなるコアについても、鉄損特性の向上が必要とされる。
In recent years, with the development of car electronics, automobiles are equipped with a large number of electric rotating machines (hereinafter referred to as “rotating machines”) composed of various motors for driving axles, wipers, opening / closing windows, and driving mirrors. ing. The number of installed rotating machines per car is increasing year by year, and the impact on fuel consumption due to the increase in the weight of the car body is becoming ignorable. In addition, from the viewpoint of protecting the global environment, rotating machines mounted on automobiles are required to be smaller, lighter, higher in output, and more efficient. In order to improve the performance of such rotating machines, it is necessary to improve the magnetic flux density (saturated magnetic flux density) and iron loss characteristics of magnetic materials for iron cores used as stators and rotors of rotating machines. Is done.
Similarly, an improvement in iron loss characteristics is required for a core (iron core) made of a magnetic material for an iron core used in various transformers or a core made of a magnetic material for an iron core of a reactor.
上記した回転機、トランス、リアクトル等に用いられる鉄心用磁性材としては、従来から無方向性電磁鋼板と呼ばれる安価なＦｅ−約３質量％Ｓｉ系合金が用いられている。しかし、無方向性電磁鋼板の飽和磁束密度（以下、「Ｂｓ」という）は約２．０Ｔであり、回転機、トランス、リアクトル等のさらなる高性能化には、より高Ｂｓな鉄心用磁性材が必要とされる。
このような高Ｂｓの鉄心用磁性材としては、Ｂｓが約２．２Ｔの純Ｆｅや約２．３〜２．４Ｔのパーメンダーまたはパーメンジュールと称されるＦｅ−約５０質量％Ｃｏ系合金が、古くから知られている。特に、Ｆｅ−約５０質量％Ｃｏ系合金は、高価な合金系ではあるものの、そのＢｓの高さから、近年になって回転機用等の磁性材として注目され始めている。
As a magnetic material for an iron core used in the above-described rotating machine, transformer, reactor, etc., an inexpensive Fe—about 3 mass% Si-based alloy called a non-oriented electrical steel sheet has been conventionally used. However, the saturation magnetic flux density (hereinafter referred to as “Bs”) of the non-oriented electrical steel sheet is about 2.0 T, and for higher performance of rotating machines, transformers, reactors, etc., higher Bs magnetic material for iron cores. Is needed.
Examples of such high Bs magnetic materials for iron cores include pure Fe with Bs of about 2.2T and Fe—about 50% by mass Co-based alloy with about 2.3 to 2.4T as a permender or permendur. But it has been known for a long time. In particular, Fe—about 50 mass% Co-based alloy is an expensive alloy system, but due to its high Bs, recently it has begun to attract attention as a magnetic material for rotating machines.
高ＢｓのＦｅ−約５０質量％Ｃｏ系合金は、常温下での脆さを改善するために、一般には、熱間圧延後の冷間圧延性を確保するため、約２質量％のＶ元素添加とともに、冷間圧延前に急速冷却を前提とした固溶化熱処理を必要とする。
このようなＦｅ−Ｃｏ系合金の冷間加工性を、工業規模の量産性で確保するために提案されている特許文献として、Ｆｅ−Ｃｏ系合金の製造方法（特許文献１）、Ｆｅ−Ｃｏ系磁性合金及びその製造方法（特許文献２）、鉄−コバルト合金板の製造方法（特許文献３）等の開示がなされている。
High-Bs Fe—about 50% by mass Co-based alloy is generally about 2% by mass of V element in order to improve brittleness at room temperature, and generally to ensure cold rollability after hot rolling. Along with the addition, a solution heat treatment on the premise of rapid cooling is required before cold rolling.
Patent documents proposed for securing the cold workability of such an Fe-Co-based alloy with mass productivity on an industrial scale include a method for producing an Fe-Co-based alloy (Patent Document 1), Fe-Co, and the like. Disclosure of a magnetic alloy and a method for producing the same (Patent Document 2), a method for producing an iron-cobalt alloy plate (Patent Document 3), and the like has been made.
特許文献１のＦｅ−Ｃｏ系合金の製造方法は、質量％でＣｏ：４６〜５２％を含むＦｅ−Ｃｏ系合金の厚さ２．５ｍｍ以下の熱間圧延コイルを、その長さ方向に連続的に走行させ、その走行中に固溶化加熱を行い、該加熱後の８００℃から４００までの間を４００℃／ｓｅｃ以上の冷却速度で急冷することにより、その後の冷間圧延性を確保するＦｅ−Ｃｏ系合金の製造方法である。 The manufacturing method of the Fe-Co type alloy of patent document 1 is the continuous hot rolling coil of thickness 2.5mm or less of the Fe-Co type alloy which contains Co: 46-52% by mass% in the length direction. The solution is heated in a solid state, and solution heating is performed during the traveling, and the subsequent cold rolling property is ensured by rapidly cooling between 800 ° C. and 400 ° C. at a cooling rate of 400 ° C./sec or more. This is a method for producing an Fe-Co alloy.
特許文献２のＦｅ−Ｃｏ系磁性合金及びその製造方法は、質量％でＣｏ：４０〜６０％、Ｖ：５．０％以下、Ｓｉ：３．０％以下、Ａｌ：３．０％以下、Ｃ：０．１％以下、残部実質的にＦｅからなるＦｅ−Ｃｏ系磁性合金を、９５０℃以上の温度から３０℃／ｓｅｃ以上の冷却速度で固溶化熱処理を行い、その後７００℃以上のα相領域の温度で磁性焼鈍することで、冷間圧延性と高Ｂｓを確保するＦｅ−Ｃｏ系合金の製造方法である。 The Fe—Co based magnetic alloy and the manufacturing method thereof in Patent Document 2 are, in mass%, Co: 40 to 60%, V: 5.0% or less, Si: 3.0% or less, Al: 3.0% or less, C: Fe—Co-based magnetic alloy consisting essentially of Fe of 0.1% or less and the balance being Fe is subjected to a solution heat treatment at a cooling rate of 30 ° C./sec from a temperature of 950 ° C. or higher, and then α of 700 ° C. or higher. This is a method for producing an Fe—Co alloy that secures cold rollability and high Bs by magnetic annealing at a temperature in the phase region.
特許文献３の鉄−コバルト合金板の製造方法は、質量％でＣｏ：４５〜５２％、Ｖ：０．５〜３．０％を含有するＦｅ−Ｃｏ系合金スラブを、加熱後、圧延終了温度７５０〜１１００℃の条件下で４．０ｍｍ未満の板厚に熱間圧延し、その後直ちに水量が１．０ｍ３／ｍｉｎ以上のジェット噴流ゾーンを走行させて急冷することにより、その後の冷間圧延性を確保するＦｅ−Ｃｏ系合金の製造方法である。 The manufacturing method of the iron-cobalt alloy plate of patent document 3 is the completion | finish of rolling, after heating the Fe-Co-type alloy slab containing Co: 45-52% and V: 0.5-3.0% by mass%. Hot rolling to a plate thickness of less than 4.0 mm under conditions of a temperature of 750 to 1100 ° C., and then immediately cooling by running in a jet jet zone where the amount of water is 1.0 m 3 / min or more, This is a method for producing an Fe—Co alloy that ensures rollability.
特許文献１から３に開示される何れの技術も、高ＢｓのＦｅ−Ｃｏ系合金の冷間加工性を、工業規模の量産性で確保するのに優れた技術である。
ところで、自動車搭載用の各種の回転機の高性能化には、高Ｂｓの他に、鉄損特性の向上が必要とされる。一般的に、渦電流損失とヒステリシス損失と呼ばれる損失で構成される鉄損特性の向上には、鉄心用磁性材の、渦電流損失を低減させるために板厚の減少やヒステリシス損失を低減させるために励磁特性の向上（保磁力の低減など）が必要となる。特にヒステリシス損失の低減に寄与する励磁特性の向上には、良好な励磁特性を得るための適切な成分範囲、製造プロセス条件に、鉄心用磁性材としての製造条件を管理する必要がある。
しかし、特許文献１から３に開示される何れの技術も、鉄心用磁性材の励磁特性と成分範囲、製造プロセス条件の関係については十分に検討されておらず、良好な励磁特性を安定して得ることが難しかった。
したがって、上述したような特許文献１から３に開示されるＦｅ−Ｃｏ系合金及びその製造方法では、近年の小型・軽量化、高出力化及び高効率化が要求される自動車搭載用の回転機の磁心材料である鉄心用磁性材として要求される鉄損特性には十分に対応できないという問題があった。同様に、各種の制御機器や通信機器において、高精度な制御を行うための電子回路において使用される各種のトランスやリアクトル等を構成する鉄心用磁性材についても、このような問題があった。
Any of the techniques disclosed in Patent Documents 1 to 3 is an excellent technique for securing the cold workability of a Fe-Co alloy having a high Bs with mass productivity on an industrial scale.
Incidentally, in order to improve the performance of various rotating machines mounted on automobiles, in addition to high Bs, improvement in iron loss characteristics is required. In general, to improve the iron loss characteristics composed of eddy current loss and loss called hysteresis loss, in order to reduce the eddy current loss and hysteresis loss of the magnetic material for iron core In addition, it is necessary to improve the excitation characteristics (such as reducing the coercive force). In particular, in order to improve the excitation characteristics that contribute to the reduction of hysteresis loss, it is necessary to manage the manufacturing conditions as the magnetic material for the iron core within an appropriate component range and manufacturing process conditions for obtaining good excitation characteristics.
However, none of the techniques disclosed in Patent Documents 1 to 3 has sufficiently studied the relationship between the excitation characteristics, the component range, and the manufacturing process conditions of the magnetic material for the iron core. It was difficult to get.
Therefore, in the Fe—Co alloy and the manufacturing method disclosed in Patent Documents 1 to 3 as described above, a rotating machine for mounting on an automobile, which is required to be small and light in weight in recent years, and to have high output and high efficiency. There is a problem that the iron loss characteristics required as a magnetic material for an iron core, which is a magnetic core material, cannot be sufficiently met. Similarly, the magnetic materials for iron cores constituting various transformers and reactors used in electronic circuits for performing high-precision control in various control devices and communication devices have such problems.
本発明の目的は、鉄心用磁性材としてのＦｅ−約５０質量％Ｃｏ系合金の良好な励磁特性を安定して得るための手段を明らかにするとともに、従来よりも良好な鉄損特性を具備した鉄心用磁性材及びその製造方法、この鉄心用磁性材を用いた鉄心を提供することである。 The object of the present invention is to clarify means for stably obtaining good excitation characteristics of an Fe—about 50 mass% Co-based alloy as a magnetic material for iron cores, and to have iron loss characteristics better than before. It is to provide a magnetic material for an iron core, a manufacturing method thereof, and an iron core using the magnetic material for an iron core.
本発明者等は、回転機等に用いる鉄心用磁性材としてパーメンダーまたはパーメンジュールと称されるＦｅ−Ｃｏ−Ｖ系合金において、高いＢｓを損なわず、且つ良好な励磁特性ならびに所望の鉄損特性が安定して得られるよう鋭意検討した。その結果、Ｃ、Ｍｎ、Ｖ等の不純物ならびに微量添加元素の成分量、固溶化熱処理、冷間圧延率、磁性焼鈍などの製造プロセス条件を適正に制御することにより、高いＢｓを損なわず、且つ、従来よりも良好な励磁特性ならびに所望の鉄損特性が安定して得られることを見出し本発明に到達した。 In the Fe-Co-V alloy called permender or permendur as a magnetic material for iron core used in a rotating machine or the like, the present inventors do not impair high Bs and have good excitation characteristics and desired iron loss. We intensively studied to obtain stable characteristics. As a result, by appropriately controlling the manufacturing process conditions such as the amount of impurities such as C, Mn, and V, as well as the component amount of trace addition elements, solution heat treatment, cold rolling rate, and magnetic annealing, high Bs is not impaired, and As a result, the inventors have found that excellent excitation characteristics as well as desired iron loss characteristics can be stably obtained compared with the prior art, and have reached the present invention.
すなわち、本発明は、板厚が２００μｍ以下の鉄心用磁性材であって、該鉄心用磁性材は、質量％で、Ｃｏ＋Ｆｅ：９７％以上、且つ、Ｆｅ：Ｃｏが０．９〜１．１、残部はＶ：１．７０〜２．００％、Ｍｎ：０．０１〜０．４５％と不純物でなり、該不純物のうち、Ｃ：０．００８％以下、Ｓ：０．０１％以下に規制し、且つ、前記ＶとＭｎは、Ｖ＋Ｍｎ：２．１５％以下であり、Ｍｎ：Ｓが１０〜１００の関係を満足する組成を有し、平均結晶粒径：３０μｍ以上、保磁力：４０Ａ／ｍ未満、動作磁束密度を１Ｔとし動作周波数４００Ｈｚにおける全鉄損：１１Ｗ／ｋｇ未満からなる鉄心用磁性材である。 That is, the present invention is a magnetic material for iron core having a plate thickness of 200 μm or less, and the magnetic material for iron core is in mass%, Co + Fe: 97% or more, and Fe: Co is 0.9 to 1.1. The remainder is made up of impurities such as V: 1.70 to 2.00%, Mn: 0.01 to 0.45%, and among these impurities, C: 0.008% or less, S: 0.01% or less In addition, V and Mn are V + Mn: 2.15% or less, Mn: S has a composition satisfying the relationship of 10 to 100, average crystal grain size: 30 μm or more, coercive force: 40 A It is a magnetic material for an iron core having a total iron loss of less than 11 W / kg at an operating frequency of 400 Hz with an operating magnetic flux density of 1 T.
また、本発明は、質量％で、Ｃｏ＋Ｆｅ：９７％以上、且つ、Ｆｅ：Ｃｏが０．９〜１．１、残部はＶ：１．７０〜２．００％、Ｍｎ：０．０１〜０．４５％と不純物でなり、該不純物のうち、Ｃ：０．００８％以下、Ｓ：０．０１％以下に規制し、且つ、前記ＶとＭｎは、Ｖ＋Ｍｎ：２．１５％以下であり、Ｍｎ：Ｓが１０〜１００の関係を満足する組成を有する熱間圧延材を、γ変態温度以上に加熱した後、急冷を行う熱処理工程と、該熱処理工程の後、９０％以上の圧延率で冷間圧延を行って板厚を２００μｍ以下の冷間圧延材とし、該冷間圧延材を８００〜９００℃で磁性焼鈍を行い、平均結晶粒径：３０μｍ以上、保磁力：４０Ａ／ｍ未満、動作磁束密度を１Ｔとし動作周波数４００Ｈｚにおける全鉄損：１１Ｗ／ｋｇ未満とする鉄心用磁性材の製造方法である。 In the present invention, the mass% is Co + Fe: 97% or more, Fe: Co is 0.9 to 1.1, the balance is V: 1.70 to 2.00%, Mn: 0.01 to 0 .45% of impurities, of which C: 0.008% or less, S: 0.01% or less, and V and Mn are V + Mn: 2.15% or less, A hot-rolled material having a composition satisfying the relationship of Mn: S of 10 to 100 is heated to a temperature equal to or higher than the γ transformation temperature and then rapidly cooled, and after the heat treatment step, at a rolling rate of 90% or more. Cold rolling is performed to obtain a cold rolled material having a plate thickness of 200 μm or less, the cold rolled material is subjected to magnetic annealing at 800 to 900 ° C., an average crystal grain size: 30 μm or more, a coercive force: less than 40 A / m, Iron with operating magnetic flux density of 1T and total iron loss at operating frequency of 400Hz: less than 11W / kg It is a manufacturing method of use magnetic material.
さらに、本発明は、上記した鉄心用磁性材を用いたことを特徴とする鉄心である。この本発明に係る鉄心は、板厚が２００μｍ以下の上記構成の鉄心用磁性材をプレス加工等により所望の形状に成形した板材を鉄心として、その複数枚を積層して回転機のステータ（固定子）またはロータ（回転子）、トランスのコア、リアクトルのコアとして使用されるものである。 Furthermore, the present invention provides an iron core using the above-described magnetic material for iron core. The iron core according to the present invention is a stator (fixed) of a rotating machine in which a plurality of sheets are laminated by using, as an iron core, a magnetic material for an iron core having a thickness of 200 μm or less formed into a desired shape by pressing or the like. Used as a core of a rotor or a rotor, a transformer core, or a reactor.
本発明によれば、鉄心用磁性材として、高Ｂｓを維持したまま、励磁特性を飛躍的に改善することができるとともに、従来よりも良好な鉄損特性を具備した、特に自動車に搭載される各種の回転機に使用してその高効率化の効果を発揮することができる鉄心用磁性材を提供することができる。さらに、本発明の鉄心用磁性材を用いた鉄心を、回転機のステータ本体、ロータ本体、各種のトランスのコア、あるいはリアクトルのコアとして使用することにより、良好な鉄損特性を得ることができる。 According to the present invention, as a magnetic material for an iron core, the excitation characteristics can be drastically improved while maintaining a high Bs, and the iron loss characteristics better than the conventional ones are mounted, particularly in automobiles. It is possible to provide a magnetic material for an iron core that can be used for various rotating machines and exhibit the effect of improving its efficiency. Furthermore, by using the iron core using the magnetic material for iron core of the present invention as a stator main body, a rotor main body, a core of various transformers, or a core of a reactor, good iron loss characteristics can be obtained. .
上述したように、本発明の重要な特徴は、Ｆｅ−Ｃｏ系合金において、励磁特性と成分範囲、製造プロセス条件の関係について鋭意検討した結果、高Ｂｓを維持したまま、良好な励磁特性ならびに鉄損特性を安定して得る成分範囲と製造プロセス条件を明らかにしたことにある。
本発明は、Ｆｅ−Ｃｏ系合金の成分、製造プロセス条件に対して、主成分のＦｅ、Ｃｏ量、微量添加元素のＶ、Ｍｎ量、不純物元素のＣ、Ｓ量などの成分範囲と、固溶化熱処理温度、冷間圧延率、磁性焼鈍温度等の製造プロセス条件の関係を適正化することで、高Ｂｓを維持したまま、励磁特性を飛躍的に改善できる。加えて、従来のＦｅ−Ｃｏ系合金が、磁性焼鈍と称される軟磁気特性を付与する熱処理工程の僅かな加熱温度の違いに、敏感に反応して、励磁特性を劣化させ易いという問題を改善することに成功したものである。
また、本発明は、鉄心用磁性材としてのＦｅ−Ｃｏ系合金の板厚ならびに励磁特性と鉄損特性の関係について鋭意検討した結果、回転機のステータ本体あるいはロータ本体、トランスのコア、リアクトルのコア等に使用する鉄心用磁性材として、所望の鉄損特性を得る手段を明らかにしたものである。これにより、本発明の鉄心用磁性材は、高Ｂｓを維持したまま、良好な励磁特性をもつＦｅ−Ｃｏ系合金により、高Ｂｓ、且つ良好な鉄損特性を具備した鉄心用磁性材の安定生産が可能となったものである。
このように、本発明の鉄心用磁性材を鉄心として製品化、すなわち、回転機のステータ本体あるいはロータ本体、トランスのコア、リアクトルのコアとして良好に使用可能である。
As described above, the important feature of the present invention is that, as a result of intensive studies on the relationship between excitation characteristics, component ranges, and manufacturing process conditions in Fe-Co alloys, good excitation characteristics and iron are maintained while maintaining high Bs. The purpose of this study is to clarify the component range and manufacturing process conditions for obtaining stable loss characteristics.
The present invention relates to a component range such as Fe, Co content of the main component, V, Mn content of trace addition element, C, S content of impurity element, etc. By optimizing the relationship between the manufacturing process conditions such as the solution heat treatment temperature, the cold rolling rate, and the magnetic annealing temperature, the excitation characteristics can be dramatically improved while maintaining high Bs. In addition, the conventional Fe-Co alloy is sensitive to the slight difference in heating temperature in the heat treatment process that imparts soft magnetic characteristics called magnetic annealing, and the excitation characteristics are likely to deteriorate. It has succeeded in improving.
In addition, as a result of intensive studies on the thickness of the Fe-Co alloy as the magnetic material for the iron core and the relationship between the excitation characteristics and the iron loss characteristics, the present invention has revealed that the stator body or rotor body of the rotating machine, the core of the transformer, and the reactor As a magnetic material for an iron core used for a core or the like, a means for obtaining a desired iron loss characteristic is clarified. As a result, the magnetic material for iron core of the present invention is stable in the magnetic material for iron core having high Bs and good iron loss characteristics by the Fe-Co alloy having good excitation characteristics while maintaining high Bs. Production is now possible.
As described above, the magnetic material for iron core of the present invention can be commercialized as an iron core, that is, can be satisfactorily used as a stator body or rotor body of a rotating machine, a core of a transformer, and a core of a reactor.
最初に、本発明の鉄心用磁性材を鉄心として、回転機のステータとして適用する場合の実施形態について説明する。
図１７は、本発明の鉄心を、回転機１のステータとして使用したときの実施形態の一例を説明するための図であって、ステータ部分の要部を示す平面図である。この回転機１は、例えば、ハイブリット車の駆動用の電動機に適用される。図１７に示すように、回転機１はステータ（固定子）２と、ステータ２の内側に所定の間隔３Ｓを設定して配置されたロータ（回転子）３を備え、これらステータ２とロータ３は、図示しないハウジング（モータケース）内に収容されて構成されている。
First, an embodiment in the case of applying the magnetic material for iron core of the present invention as an iron core as a stator of a rotating machine will be described.
FIG. 17 is a view for explaining an example of an embodiment when the iron core of the present invention is used as the stator of the rotating machine 1, and is a plan view showing the main part of the stator portion. The rotating machine 1 is applied to, for example, an electric motor for driving a hybrid vehicle. As shown in FIG. 17, the rotating machine 1 includes a stator (stator) 2 and a rotor (rotor) 3 arranged at a predetermined interval 3 </ b> S inside the stator 2, and the stator 2 and the rotor 3. Is housed in a housing (motor case) (not shown).
ステータ２は環状に形成されたヨーク部２ａと、ヨーク部２ａの内周面２ａ１（周面）に径方向内側に突出して形成される複数のティース部２ｂと、各ティース部２ｂに巻回されるコイル２ｃとで構成されている（図１７にはステータ２の一部のみを図示している）。ティース部２ｂは、ティース本体部２ｂ１と、ティース本体部２ｂ１の先端に形成されるティース先端鍔部２ｂ２とを有している。なお、ヨーク部２ａは、例えば図示しないハウジング内に固定されている。 The stator 2 is wound around each of the tooth portions 2b, a yoke portion 2a formed in an annular shape, a plurality of tooth portions 2b formed to project radially inward from an inner peripheral surface 2a1 (peripheral surface) of the yoke portion 2a, and the like. (Only a part of the stator 2 is shown in FIG. 17). The teeth part 2b has the teeth main-body part 2b1 and the teeth front-end collar part 2b2 formed in the front-end | tip of the teeth main-body part 2b1. The yoke portion 2a is fixed in a housing (not shown), for example.
コイル２ｃは、例えば、表面が絶縁材料で被覆された金属線（例えば、銅）で形成され、各ティース部２ｂのティース本体部２ｂ１の周囲に巻回されている。なお、コイル２ｃは、例えば、Ｕ相、Ｖ相、Ｗ相のコイルが周方向に順に配列されている。 The coil 2c is formed of, for example, a metal wire (for example, copper) whose surface is covered with an insulating material, and is wound around the tooth body 2b1 of each tooth 2b. In the coil 2c, for example, U-phase, V-phase, and W-phase coils are sequentially arranged in the circumferential direction.
ロータ３は、例えば、周縁部に、周方向に沿って永久磁石３ｂが埋め込まれたもので構成されている。すなわち、ロータ３は、環状のロータヨーク３ａを有し、ロータヨーク３ａの周方向に形成された各スロット（図示せず）内に永久磁石３ｂが埋め込まれて構成されている。また、ロータ３の中心には、動力を伝達する軸（シャフト）が固定されている。なお、永久磁石３ｂとしては、例えば、Ｒ−Ｔ−Ｂ系希土類磁石（Ｒ：Ｙを含む希土類元素の１種又は２種以上、Ｔ：Ｆｅ又はＦｅとＣｏ）を用いることができる。 The rotor 3 is configured by, for example, a permanent magnet 3b embedded in the peripheral portion along the circumferential direction. That is, the rotor 3 has an annular rotor yoke 3a, and is configured such that permanent magnets 3b are embedded in slots (not shown) formed in the circumferential direction of the rotor yoke 3a. A shaft (shaft) for transmitting power is fixed at the center of the rotor 3. As the permanent magnet 3b, for example, an R-T-B rare earth magnet (one or more of R: Y-containing rare earth elements, T: Fe or Fe and Co) can be used.
上記した構成を備えた回転機１において、ステータ２を構成する部材が、本発明に係る鉄心用磁性材を鉄心として適用している。
続いて、本発明に係る鉄心用磁性材について、その成分を含む材料構成の特徴について説明する。
In the rotating machine 1 having the above-described configuration, the member constituting the stator 2 uses the magnetic material for iron core according to the present invention as the iron core.
Then, the characteristic of the material structure containing the component is demonstrated about the magnetic material for iron cores which concerns on this invention.
本発明の鉄心用磁性材の板厚は２００μｍ以下とする。
これは、後述する本発明の成分をいくら適正な範囲に調整しても、板厚が２００μｍを超えて厚くすると、良好な励磁特性によるヒステリシス損失の低減を成しても、渦電流損失の増加により、所望の全鉄損を得ることができなくなるためである。
そのため、本発明では、所望の励磁特性及び全鉄損を得ることができる板厚として、２００μｍ以下と規定した。好ましい板厚は１０〜１５０μｍである。
The plate thickness of the magnetic material for iron core of the present invention is 200 μm or less.
Even if the components of the present invention to be described later are adjusted to an appropriate range, an increase in eddy current loss can be achieved even if the hysteresis loss is reduced by good excitation characteristics when the plate thickness exceeds 200 μm. This is because the desired total iron loss cannot be obtained.
Therefore, in the present invention, the plate thickness that can obtain desired excitation characteristics and total iron loss is defined as 200 μm or less. A preferred plate thickness is 10 to 150 μm.
次に、本発明で規定する各元素の添加の理由とその含有量について説明する。なお、各元素の含有量は質量％である。
Ｃｏ＋Ｆｅ：９７％以上、且つ、Ｆｅ：Ｃｏが０．９〜１．１
先ず、ＦｅとＣｏについて説明する。
本発明において、ＦｅとＣｏは高いＢｓを得るために必要不可欠な元素であり、ＣｏをＦｅに含有させることにより、例えば２．０Ｔ以上の高いＢｓを得ることができる。本発明では、この高いＢｓを得るための最適なＦｅとＣｏの含有量、及び、ＦｅとＣｏの最適バランスとしてＣｏとＦｅの総量を９７％以上とし、且つ、Ｆｅ：Ｃｏ（ＦｅとＣｏの含有量の比率）が０．９〜１．１の範囲とした。
Next, the reason for addition of each element prescribed | regulated by this invention and its content are demonstrated. In addition, content of each element is the mass%.
Co + Fe: 97% or more, and Fe: Co is 0.9 to 1.1
First, Fe and Co will be described.
In the present invention, Fe and Co are indispensable elements for obtaining high Bs. By incorporating Co into Fe, for example, high Bs of 2.0 T or more can be obtained. In the present invention, the optimal content of Fe and Co for obtaining this high Bs, and the total balance of Co and Fe as an optimal balance of Fe and Co is set to 97% or more, and Fe: Co (of Fe and Co) The content ratio was in the range of 0.9 to 1.1.
Ｖ：１．７０〜２．００％
Ｖは、少な過ぎると冷間圧延における脆化問題を引き起こすため、本発明では１．７０％以上含有させる。一方、Ｖ量が多過ぎると、Ｂｓの低下をまねく他、マトリックス中に微細なＶ系炭化物が多量に分散し、励磁特性ならびに鉄損特性の低下を引き起こすため、質量％で、２．００％以下の添加とする。Ｖの好ましい上限は１．９５％である。
Ｍｎ：０．０１〜０．４５％
Ｍｎは、その添加により、不純物元素のＳをＭｎＳとして固定するため、励磁特性及び鉄損特性の向上に効果を発揮するが、多過ぎると、逆に励磁特性ならびに鉄損特性の低下をまねくため、質量％で、０．４５％以下の添加とする。
なお、Ｍｎ添加による、上記効果を得るには下限を０．０１％以上とする。
V: 1.70-2.00%
If V is too small, it causes embrittlement problems in cold rolling, so 1.70% or more is contained in the present invention. On the other hand, if the amount of V is too large, Bs will be lowered, and fine V-based carbides will be dispersed in a large amount in the matrix, causing deterioration of excitation characteristics and iron loss characteristics. Add the following. A preferable upper limit of V is 1.95%.
Mn: 0.01 to 0.45%
When Mn is added, S of the impurity element is fixed as MnS, so that it is effective in improving the excitation characteristics and iron loss characteristics. However, if too much Mn is added, the excitation characteristics and iron loss characteristics are reduced. The addition of 0.45% or less by mass%.
In order to obtain the above effect by adding Mn, the lower limit is made 0.01% or more.
Ｖ＋Ｍｎ：２．１５％以下
本発明では、積極的に添加するＶとＭｎは、上記の範囲を満たした上で、更にＶとＭｎの総量を２．１５％以下の範囲とする。
これは、ＶとＭｎがＦｅ−Ｃｏ系合金において、γ変態温度を低下させる元素であり、ＶとＭｎの総量が２．１５％を超えると、結晶粒が粗大化し易い９００℃近傍まで磁性焼鈍温度を高くした場合に、逆に金属組織が不安定となり易く、保磁力が著しく大きくなる惧れがあるためである。そのため、ＶまたはＭｎの単独の範囲を満たしただけでは、良好な励磁特性ならびに鉄損特性を安定して得ることができ難くなる。したがって、Ｖ＋Ｍｎ量の上限を２．１５％以下に限定する。好ましい上限は２．１％である。
Ｍｎ：Ｓが１０〜１００
上述したとおり、Ｍｎは、その添加により、不純物元素のＳをＭｎＳとして固定する。そのため、不純物Ｓをより確実に固定できるＭｎが必要となる。ＭｎとＳの含有量の比率が、Ｍｎ：Ｓで１０未満であると、不純物ＳをＭｎＳとして固定することができず、一方、Ｍｎ：Ｓで１００を超えても、ＭｎＳとして固定するより一層の効果向上が望めないため、Ｍｎ：Ｓを１０〜１００の範囲とする。
V + Mn: 2.15% or less In the present invention, the positively added V and Mn satisfy the above range, and the total amount of V and Mn is set to a range of 2.15% or less.
In this Fe-Co alloy, V and Mn are elements that lower the γ transformation temperature. When the total amount of V and Mn exceeds 2.15%, the crystal grains tend to coarsen to near 900 ° C. This is because, when the temperature is increased, the metal structure tends to be unstable and the coercive force may be significantly increased. Therefore, it is difficult to stably obtain good excitation characteristics and iron loss characteristics only by satisfying the single range of V or Mn. Therefore, the upper limit of the amount of V + Mn is limited to 2.15% or less. A preferable upper limit is 2.1%.
Mn: S is 10 to 100
As described above, Mn fixes the impurity element S as MnS by its addition. Therefore, Mn that can fix impurities S more reliably is required. When the ratio of the contents of Mn and S is less than 10 in Mn: S, the impurity S cannot be fixed as MnS. On the other hand, even if it exceeds 100 in Mn: S, it is much more fixed than MnS. Therefore, Mn: S should be in the range of 10-100.
Ｃ：０．００８％以下、Ｓ：０．０１％以下
ＣとＳは良好な励磁特性ならびに鉄損特性を阻害する不純物元素である。Ｃが０．００８％を超えたり、Ｓが０．０１％を超えて残留すると、良好な励磁特性ならびに鉄損特性が安定して得られなくなる。そのため、本発明では不純物としてのＣ、Ｓを、Ｃ：０．００８％以下、Ｓ：０．０１％以下に規制する。好ましくは、Ｃ：０．００５％以下、Ｓ：０．００５％以下の範囲である。
C: 0.008% or less, S: 0.01% or less C and S are impurity elements that inhibit good excitation characteristics and iron loss characteristics. If C exceeds 0.008% or S exceeds 0.01%, good excitation characteristics and iron loss characteristics cannot be obtained stably. Therefore, in the present invention, C and S as impurities are restricted to C: 0.008% or less and S: 0.01% or less. Preferably, the range is C: 0.005% or less and S: 0.005% or less.
以上、説明した本発明で規定する各元素の成分範囲は、良好な励磁特性及び鉄損を安定して得るのに必要不可欠である。
例えば、板厚が２００μｍ以下の範囲において、上記の各元素の成分範囲や元素同士の関係が、多少本発明の範囲外となったとしても、良好な励磁特性及び鉄損特性が得られる場合がある。しかしながら、僅かな成分の差異によって、励磁特性及び鉄損特性は、後述する磁性焼鈍と称される軟磁気特性を付与する熱処理工程の僅かな加熱温度の違いに敏感に反応する。その結果、工業的に量産を行なう場合、同一ロットであっても、励磁特性や鉄損がばらついてしまう。
一方で、本発明で規定する成分範囲であれば、安定した磁気特性を得ることができる磁性焼鈍の温度範囲を広げることができる。そのため、本発明では、各元素共に極めて限定的な成分範囲とした。
この効果については、後記する実施例にて、詳しく示すことにする。
As described above, the component range of each element defined in the present invention is indispensable for stably obtaining good excitation characteristics and iron loss.
For example, in the range where the plate thickness is 200 μm or less, even if the component ranges of the above elements and the relationship between the elements are slightly out of the scope of the present invention, good excitation characteristics and iron loss characteristics may be obtained. is there. However, due to a slight difference in components, the excitation characteristics and the iron loss characteristics are sensitive to a slight difference in heating temperature in a heat treatment process that gives a soft magnetic characteristic called magnetic annealing, which will be described later. As a result, when mass production is industrially performed, even in the same lot, excitation characteristics and iron loss vary.
On the other hand, if it is the component range prescribed | regulated by this invention, the temperature range of the magnetic annealing which can acquire the stable magnetic characteristic can be expanded. Therefore, in the present invention, each element has an extremely limited component range.
This effect will be described in detail in the examples described later.
次に金属組織について説明する。
平均結晶粒径：３０μｍ以上
本発明の鉄心用磁性材の断面または平面ミクロ組織は、その平均結晶粒径が、３０μｍ以上と規定する。これは、磁壁移動の障害となる結晶粒界を少なくすることで、良好な励磁特性ならびに鉄損特性を得ることができるためである。
なお、本発明で言う平均結晶粒径とは、鉄心用磁性材の断面または平面ミクロ組織における結晶粒を円形に近似したときの平均直径のことである。もし、例えば、板厚方向に結晶粒が単独で存在する場合、その単独結晶粒から平均直径を求めることにする。
Next, the metal structure will be described.
Average crystal grain size: 30 μm or more The cross-sectional or planar microstructure of the magnetic material for iron core of the present invention is defined to have an average crystal grain size of 30 μm or more. This is because good excitation characteristics and iron loss characteristics can be obtained by reducing the crystal grain boundaries that hinder domain wall movement.
In addition, the average crystal grain diameter said by this invention is an average diameter when the crystal grain in the cross section or planar microstructure of a magnetic material for iron cores is approximated circularly. For example, when crystal grains exist alone in the plate thickness direction, the average diameter is determined from the single crystal grains.
次に保磁力について説明する。
保磁力：４０Ａ／ｍ未満
本発明の鉄心用磁性材は、保磁力を４０Ａ／ｍ未満と規定する。保磁力が４０Ａ／ｍを超えると、良好な励磁特性とは言えず、ヒステリシス損失の増加を促し、所望の全鉄損を得難くなるためである。
Next, the coercive force will be described.
Coercive force: less than 40 A / m The magnetic material for iron core of the present invention defines the coercive force to be less than 40 A / m. This is because if the coercive force exceeds 40 A / m, it cannot be said that the excitation characteristics are good, and an increase in hysteresis loss is promoted, making it difficult to obtain a desired total iron loss.
次に全鉄損について説明する。
全鉄損：１１Ｗ／ｋｇ未満
本発明の鉄心用磁性材は、動作磁束密度を１Ｔとし動作周波数４００Ｈｚにおける全鉄損を１１Ｗ／ｋｇ未満と規定する。これは、回転機用として一般的な鉄心用磁性材である公知の無方向性電磁鋼板（板厚１００〜２００μｍ）の、動作磁束密度を１Ｔとし動作周波数４００Ｈｚにおける全鉄損が約１１Ｗ／ｋｇとなるからである。
全鉄損が１１Ｗ／ｋｇを超えると、高いＢｓによる、回転機等の高い出力が得られても、回転機等における損失が大きくなり、その効率を低下させるためである。
Next, the total iron loss will be described.
Total iron loss: less than 11 W / kg The magnetic material for iron core of the present invention defines the total magnetic loss as less than 11 W / kg at an operating magnetic flux density of 1 T and an operating frequency of 400 Hz. This is a known non-oriented electrical steel sheet (plate thickness 100-200 μm), which is a general magnetic material for iron cores for use in rotating machines, and the total magnetic loss at an operating magnetic frequency density of 1 T and an operating frequency of 400 Hz is about 11 W / kg. Because it becomes.
This is because when the total iron loss exceeds 11 W / kg, even if a high output of a rotating machine or the like due to high Bs is obtained, the loss in the rotating machine or the like becomes large and the efficiency is lowered.
次に本発明の鉄心用磁性材を得るための製造方法について説明する。
先ず、上記の組成に調整した熱間圧延材素材を用意する。熱間圧延材を作製する工程は、以降の工程を進め易くするための鋼片を得る目的であり、熱間圧延の加熱温度は１０００〜１１５０℃であることが望ましい。
該熱間圧延材を作製した後、γ変態温度以上に加熱した後、急冷を行う熱処理工程を行う。ここで、熱処理温度をγ変態温度以上に規定した理由は、冷間圧延時の脆化問題を避け、且つ、良好な励磁特性及び鉄損特性を安定して得るためである。本発明の鉄心用磁性材に係る合金の場合、γ変態温度は約９１０〜９３０℃の範囲である。そのため、実際の熱処理温度としては９５０℃以上であることが望ましい。また、表面酸化の過度な進行や熱処理にかかるエネルギーを低減するために、上限は１２００℃以下とすることが望ましい。
また、γ変態温度以上に加熱した後の冷却速度は、常温下での冷間圧延性が得られれば良く、水冷以上の冷却速度が望ましい。なお、固溶化熱処理工程の後に、酸化スケールの除去工程を行うことが望ましい。
Next, a manufacturing method for obtaining the magnetic material for iron core of the present invention will be described.
First, a hot rolled material adjusted to the above composition is prepared. The step of producing the hot rolled material is for the purpose of obtaining a steel slab for facilitating the subsequent steps, and the heating temperature of the hot rolling is preferably 1000 to 1150 ° C.
After producing the hot-rolled material, it is heated to a temperature equal to or higher than the γ transformation temperature, and then subjected to a heat treatment step for rapid cooling. Here, the reason why the heat treatment temperature is specified to be equal to or higher than the γ transformation temperature is to avoid embrittlement problems during cold rolling and to stably obtain good excitation characteristics and iron loss characteristics. In the case of the alloy according to the magnetic material for iron core of the present invention, the γ transformation temperature is in the range of about 910 to 930 ° C. Therefore, the actual heat treatment temperature is desirably 950 ° C. or higher. Further, the upper limit is desirably set to 1200 ° C. or less in order to reduce the excessive amount of surface oxidation and the energy required for heat treatment.
Further, the cooling rate after heating to the γ transformation temperature or higher is only required to obtain cold rollability at room temperature, and a cooling rate higher than water cooling is desirable. In addition, it is desirable to perform the removal process of an oxide scale after a solution heat treatment process.
上記の熱処理工程の後、９０％以上の圧延率で冷間圧延を行って板厚を２００μｍ以下の冷間圧延材とする工程を行う。
圧延率を９０％以上に規定した理由は、素材に冷間加工歪を蓄積させ、以降の磁性焼鈍時に、より結晶粒の成長を促し、良好な励磁特性及び鉄損特性を安定して得るのに効果があるためである。
次に、上記の冷間圧延材を８００〜９００℃で磁性焼鈍を行い、平均結晶粒径：３０μｍ以上にする熱処理工程を行う。
磁性焼鈍は、冷間圧延組織を再結晶または二次再結晶組織とすることで、加工歪の除去及び結晶粒を粗大化させることができる。磁性焼鈍温度は、低過ぎると、十分な結晶粒の成長が成されず、良好な励磁特性及び鉄損特性を安定して得られないため、８００℃以上であることが必要である。一方、γ変態温度を超えると、粒界近傍にα‐γ変態に伴う部分的な微細粒が形成され、逆に励磁特性及び鉄損特性が低下するため、磁性焼鈍の上限は９００℃以下とする。好ましくは、８４０〜８９０℃の範囲である。
なお、磁性焼鈍は表面酸化などを避けるため、真空中または水素雰囲気下で行うことが望ましい。
上述した工程により、保磁力：４０Ａ／ｍ未満、動作磁束密度を１Ｔとし動作周波数４００Ｈｚにおける全鉄損：１１Ｗ／ｋｇ未満の特性を安定して得ることができる。
After the heat treatment step, cold rolling is performed at a rolling rate of 90% or more to obtain a cold rolled material having a plate thickness of 200 μm or less.
The reason why the rolling rate is specified to be 90% or more is that cold working strain is accumulated in the material, and during subsequent magnetic annealing, the growth of crystal grains is further promoted, and good excitation characteristics and iron loss characteristics can be stably obtained. This is because it is effective.
Next, the cold-rolled material is subjected to a magnetic annealing at 800 to 900 ° C. to perform a heat treatment step to make the average crystal grain size: 30 μm or more.
In the magnetic annealing, the cold-rolled structure is recrystallized or secondary recrystallized structure, so that the processing strain can be removed and the crystal grains can be coarsened. If the magnetic annealing temperature is too low, sufficient crystal grain growth cannot be achieved, and good excitation characteristics and iron loss characteristics cannot be stably obtained. Therefore, the magnetic annealing temperature needs to be 800 ° C. or higher. On the other hand, when the γ transformation temperature is exceeded, partial fine grains associated with the α-γ transformation are formed in the vicinity of the grain boundary, and conversely, the excitation characteristics and iron loss characteristics deteriorate, so the upper limit of magnetic annealing is 900 ° C. or less. To do. Preferably, it is the range of 840-890 degreeC.
The magnetic annealing is preferably performed in a vacuum or in a hydrogen atmosphere in order to avoid surface oxidation.
Through the above-described steps, it is possible to stably obtain characteristics of coercive force: less than 40 A / m, operating magnetic flux density of 1 T, and total iron loss at operating frequency of 400 Hz: less than 11 W / kg.
本発明では上述した製造方法により、鉄心用磁性材を得ることができる。なお、鉄心用磁性材を本発明に係る鉄心（コア）として用いる場合は、例えば、プレス加工等により所望の形状に成形する。
所望の形状への成形は、生産性を考慮すると、磁性焼鈍後に所望の形状に成形しても良いが、磁気特性の劣化が心配されるため、冷間圧延材を用いて所望の形状に加工を行い、その後に磁性焼鈍を行うと良い。
In the present invention, a magnetic material for an iron core can be obtained by the manufacturing method described above. In addition, when using the magnetic material for iron cores as the iron core (core) which concerns on this invention, it shape | molds in a desired shape by press work etc., for example.
In consideration of productivity, the desired shape may be formed into a desired shape after magnetic annealing. However, since there is a concern about the deterioration of magnetic properties, it is processed into a desired shape using a cold-rolled material. It is good to perform magnetic annealing after that.
（実施例１）
続いて、本発明に係る鉄心用磁性材を製造して、その鉄心用磁性材としての特性を評価した結果について説明する。
表１に示す組成に質量調整した原料を真空溶解し、鋳型に鋳造して溶製材素材を得た。
得られた溶製材素材を１０００〜１１５０℃に加熱して鍛伸した後、１０００〜１１５０℃に加熱して熱間圧延を行い、板厚が２．５ｍｍ（Ｎｏ．７のみ板厚１．４ｍｍ）の熱間圧延材を作製した。
その後、熱間圧延材を７００〜１０５０℃に加熱して、−０．５℃以下の氷塩水中に浸漬させて急速冷却とする熱処理を行った。次いで、酸洗い後、グラインダー加工で酸化皮膜の除去を行い、冷間圧延で厚さ０．１５ｍｍまでの薄板化が可能か、冷間圧延性の調査を行った。なお、溶製材のγ変態温度は９１０〜９３０℃である。
表１に、各温度で固溶化熱処理を行った後の、Ｎｏ．１〜Ｎｏ．１６までの冷間圧延性を示す。冷間圧延で厚さ０．１５ｍｍまでの薄板化が可能であったものを「○」、割れがひどく、以降の工程に進めなかったものを「×」とした。なお、未評価材は「−」として示した。
Ｎｏ．１〜１６のうち、本発明の成分範囲内にある合金は、Ｎｏ．５、Ｎｏ．９〜Ｎｏ．１１、Ｎｏ．１３及びＮｏ．１６の合金である。
Example 1
Then, the magnetic material for iron cores concerning this invention is manufactured, and the result of having evaluated the characteristic as the magnetic material for iron cores is demonstrated.
The raw material whose mass was adjusted to the composition shown in Table 1 was melted in vacuum, and cast into a mold to obtain a molten material.
The obtained melted material is heated to 1000 to 1150 ° C. and forged, then heated to 1000 to 1150 ° C. and hot rolled, and the thickness is 2.5 mm (only No. 7 is 1.4 mm thick). ) Was produced.
Thereafter, the hot-rolled material was heated to 700 to 1050 ° C. and immersed in ice-salt water at −0.5 ° C. or lower to perform rapid cooling. Next, after pickling, the oxide film was removed by grinder processing, and whether or not it was possible to reduce the thickness to 0.15 mm by cold rolling was investigated for cold rollability. The γ transformation temperature of the melted material is 910 to 930 ° C.
Table 1 shows the No. after solution heat treatment at each temperature. 1-No. A cold rollability of up to 16. “○” indicates that the sheet can be thinned to a thickness of 0.15 mm by cold rolling, and “X” indicates that the crack was severe and the subsequent process could not proceed. In addition, the unevaluated material is indicated as “−”.
No. Among the alloys 1 to 16, the alloys within the component range of the present invention are No. 1 to No. 16. 5, no. 9-No. 11, no. 13 and no. 16 alloys.
なお、溶製材素材におけるＮｏ．１〜６は、冷間圧延性に及ぼすＶ添加量の影響を調査するため、Ｖ量を無添加〜２．０２％の範囲で変えたものである。
Ｖ量が無添加のＮｏ．１は、全ての熱処理温度において、冷間圧延が不可能であった。Ｖ量が１．７０％未満のＮｏ．２〜４は、規則化温度（約７３０℃）以上、１０００℃未満の比較的に低い熱処理温度では、冷間圧延が可能であったものの、１０００℃以上の高温域では、冷間圧延が不可能であった。
Ｖ量が１．７０％以上のＮｏ．５、Ｎｏ．６は、規則化温度（約７３０℃）以上の、何れの熱処理温度においても冷間圧延が可能であり、量産時の脆化問題をより安定して回避できることが確認できた。また、Ｖ量が１．７０％以上のＮｏ．７〜１６については、冷間圧延で厚さ０．１５ｍｍまでの薄板化が、特に問題なく可能であった。
In addition, No. in the melted lumber material. Nos. 1 to 6 are obtained by changing the V amount in the range of no addition to 2.02% in order to investigate the influence of the V addition amount on the cold rolling property.
No. with no added amount of V. In No. 1, cold rolling was impossible at all heat treatment temperatures. No. V amount of less than 1.70%. In Nos. 2 to 4, although cold rolling was possible at a relatively low heat treatment temperature of not less than the ordering temperature (about 730 ° C.) and less than 1000 ° C., cold rolling was not possible in a high temperature region of 1000 ° C. or more. It was possible.
No. with V amount of 1.70% or more. 5, no. No. 6 was able to be cold-rolled at any heat treatment temperature not lower than the ordering temperature (about 730 ° C.) and confirmed that the embrittlement problem during mass production could be avoided more stably. In addition, No. having a V amount of 1.70% or more. About 7-16, the thickness reduction to thickness 0.15mm was possible without the problem in particular by cold rolling.
表１に示す冷間圧延が可能であったものの中で、Ｎｏ．７〜１６までの冷間圧延材から鉄心用磁性材の製品形状とする場合を模擬して、外径４５ｍｍ、内径３３ｍｍのＪＩＳリングを打ち抜き加工によって採取した。その後、冷間加工歪の除去及び結晶粒の粗大化を目的に、水素雰囲気中、加熱温度８５０℃で保持時間３ｈｒと、加熱温度８８０℃で保持時間１０ｈｒの磁性焼鈍を施して鉄心用磁性材とした。
また、複数枚のＪＩＳリングを、絶縁を目的とした層間紙を間に挟みながら積層し、プラスチック製のリングケースに納めてから、一次巻線２００回、二次巻線５０回の巻線を巻いて、励磁（直流磁気）特性及び鉄損特性を測定した。
Among those in which the cold rolling shown in Table 1 was possible, No. A JIS ring having an outer diameter of 45 mm and an inner diameter of 33 mm was sampled by punching, simulating the case where the product shape of a magnetic material for iron core was changed from a cold rolled material of 7 to 16. Thereafter, for the purpose of removing cold working strain and coarsening of crystal grains, magnetic annealing is performed in a hydrogen atmosphere at a heating temperature of 850 ° C. for a holding time of 3 hours and at a heating temperature of 880 ° C. for a holding time of 10 hours. It was.
In addition, a plurality of JIS rings are stacked with interlayer paper for insulation between them and placed in a plastic ring case, and then 200 primary windings and 50 secondary windings are formed. Winding and measuring the excitation (DC magnetism) characteristics and the iron loss characteristics.
表２に、測定した励磁（直流磁気）特性及び鉄損特性を示す。
励磁（直流磁気）特性については、鉄心用磁性材として重要な全鉄損（ヒステリシス損失）に大きな影響を及ぼす保磁力Ｈｃ（単位はＡ／ｍ）と、飽和磁束密度の代わりに、磁束密度としてほぼ飽和している印加磁場４０００Ａ／ｍにおける磁束密度（Ｂ４０００≒Ｂｓ、単位はＴ）を測定した。加えて、鉄損特性についても、動作磁束密度を１Ｔとし動作周波数４００Ｈｚにおける全鉄損（Ｗ１０／４００、単位はＷ／ｋｇ）を測定した。
なお、未評価項目は「−」とした。ここで、保磁力４０Ａ／ｍ未満、Ｂ４０００が２．０Ｔ以上、且つ、動作磁束密度を１Ｔとし動作周波数４００Ｈｚにおける全鉄損が１１Ｗ／ｋｇ未満を満たす特性を具備するものが、鉄心用磁性材として好適である。
Table 2 shows the measured excitation (DC magnetism) characteristics and iron loss characteristics.
As for the excitation (DC magnetism) characteristics, instead of the coercive force Hc (unit: A / m) and the saturation magnetic flux density, which greatly affects the total iron loss (hysteresis loss), which is important as a magnetic material for iron cores, the magnetic flux density Magnetic flux density (B4000≈Bs, unit is T) was measured at an applied magnetic field of 4000 A / m, which was almost saturated. In addition, as for the iron loss characteristics, the total magnetic loss (W10 / 400, the unit is W / kg) was measured at an operating frequency of 400 Hz with an operating magnetic flux density of 1T.
The unassessed item was “−”. Here, the magnetic material for the iron core has the characteristics that the coercive force is less than 40 A / m, B4000 is 2.0 T or more, the operating magnetic flux density is 1 T, and the total iron loss at the operating frequency of 400 Hz is less than 11 W / kg. It is suitable as.
本発明で規定する成分範囲、熱処理工程及び板厚を満足する本発明例のＮｏ．９〜１１、Ｎｏ．１３、Ｎｏ．１６Ｂ、Ｎｏ．１６Ｃは、磁性焼鈍温度が８５０℃、８８０℃の何れも、平均結晶粒径が３０μｍ以上であり、Ｂ４０００が２．０Ｔ以上、且つ、保磁力が４０Ａ／ｍ未満であり、高いＢｓを損なわず、且つ、良好な励磁特性を安定して得られることが確認できた。
また、上記の本発明例の鉄損測定を実施した結果、磁性焼鈍温度が８５０℃、８８０℃の何れも、動作磁束密度を１Ｔとし動作周波数４００Ｈｚにおける全鉄損Ｗ１０／４００が１１Ｗ／ｋｇ未満と良好な鉄損特性も得られることが確認できた。
No. of the example of the present invention satisfying the component range, heat treatment step and plate thickness specified in the present invention. 9-11, no. 13, no. 16B, no. 16C has a magnetic annealing temperature of 850 ° C. and 880 ° C., the average crystal grain size is 30 μm or more, B4000 is 2.0 T or more, the coercive force is less than 40 A / m, and high Bs is not impaired. In addition, it was confirmed that good excitation characteristics can be stably obtained.
In addition, as a result of conducting the iron loss measurement of the above-described example of the present invention, as for the magnetic annealing temperatures of 850 ° C. and 880 ° C., the total magnetic loss W10 / 400 at an operating magnetic flux density of 1T and an operating frequency of 400 Hz is less than 11 W / kg. It was confirmed that good iron loss characteristics were also obtained.
一方、比較例Ｎｏ．７は、０．０１５％のＣと２．０８％のＶを含有し、且つ、固溶化熱処理温度を８５０℃とするもので、磁性焼鈍温度が８５０℃において、平均結晶粒径が１６．２μｍと小さく、保磁力が５９．５Ａ／ｍと、良好な励磁特性が得られなかった。また、動作磁束密度を１Ｔとし動作周波数４００Ｈｚにおける全鉄損Ｗ１０／４００が１１．７Ｗ／ｋｇと良好な鉄損特性も得られなかった。これは、Ｃ、Ｖの添加量が過多であり、且つ、固溶化熱処理温度がγ変態温度以下と低いため、多数の微細なＶ系炭化物がマトリックス中に分散し、該磁性焼鈍温度における結晶粒の成長を抑制したためと考えられる。
さらに、Ｎｏ．７はＶとＭｎの総量が２．１９％と高く、磁性焼鈍温度が８８０℃においても、保磁力が５１．０Ａ／ｍと、良好な励磁特性が得られなかった。
これは、Ｖ＋Ｍｎ量が２．１５％を超えて添加されているため、γ変態温度が低下し、該磁性焼鈍温度において、金属組織が不安定になったためと考えられる。
On the other hand, Comparative Example No. No. 7 contains 0.015% C and 2.08% V, and the solution heat treatment temperature is 850 ° C. The average crystal grain size is 16.2 μm at the magnetic annealing temperature of 850 ° C. However, the coercive force was 59.5 A / m, and good excitation characteristics could not be obtained. Moreover, the total magnetic loss W10 / 400 was 11.7 W / kg at an operating magnetic flux density of 1T and an operating frequency of 400 Hz, and good iron loss characteristics were not obtained. This is because the amount of addition of C and V is excessive, and the solution heat treatment temperature is as low as the γ transformation temperature or less, so a large number of fine V-based carbides are dispersed in the matrix, and the crystal grains at the magnetic annealing temperature This is thought to be due to the suppression of growth.
Furthermore, no. No. 7 had a high total amount of V and Mn of 2.19%, and even when the magnetic annealing temperature was 880 ° C., the coercive force was 51.0 A / m, and good excitation characteristics could not be obtained.
This is presumably because the V + Mn content was added in excess of 2.15%, so the γ transformation temperature was lowered and the metal structure became unstable at the magnetic annealing temperature.
比較例Ｎｏ．８は、質量％の比で７．０のＭｎ／Ｓの組成とするもので、磁性焼鈍温度が８５０℃において、Ｍｎ添加による不純物Ｓの固定の効果が乏しく、保磁力が４１．１Ａ／ｍと、良好な励磁特性が得られなかった。
なお、Ｎｏ．８は磁性焼鈍温度が８８０℃において、平均結晶粒径が５８．８μｍ、保磁力が３１．６Ａ／ｍと、良好な励磁特性が得られ、且つ、動作磁束密度を１Ｔとし動作周波数４００Ｈｚにおける全鉄損Ｗ１０／４００が１１．７Ｗ／ｋｇと良好な鉄損特性を得られるが、僅か３０℃の磁性焼鈍温度の違いによって保磁力が大きく変化してしまい、良好な励磁特性および鉄損特性を安定して得るのは困難であった。
Comparative Example No. No. 8 has a composition of Mn / S of 7.0 by mass ratio. At a magnetic annealing temperature of 850 ° C., the effect of fixing impurities S by addition of Mn is poor, and the coercive force is 41.1 A / m. Good excitation characteristics could not be obtained.
In addition, No. No. 8 has a magnetic annealing temperature of 880 ° C., an average crystal grain size of 58.8 μm, a coercive force of 31.6 A / m and good excitation characteristics, and an operating magnetic flux density of 1 T and an operating frequency of 400 Hz. The iron loss W10 / 400 is 11.7 W / kg and good iron loss characteristics can be obtained, but the coercive force changes greatly due to the difference in magnetic annealing temperature of only 30 ° C. It was difficult to obtain stably.
比較例Ｎｏ．１２は、０．５１％のＭｎと、２．３１％のＶ＋Ｍｎ量の組成とするもので、磁性焼鈍温度が８８０℃において、金属組織が不安定となり、平均結晶粒径が１８．８μｍと小さく、保磁力が７８．６Ａ／ｍと、良好な励磁特性が得られなかった。また、動作磁束密度を１Ｔとし動作周波数４００Ｈｚにおける全鉄損Ｗ１０／４００が１３．０Ｗ／ｋｇと良好な鉄損特性も得られなかった。なお、Ｎｏ．１２は、磁性焼鈍温度が８５０℃において、平均結晶粒径が３５．４μｍ、保磁力が３９．１Ａ／ｍと、良好な励磁特性が得られ、且つ、動作磁束密度を１Ｔとし動作周波数４００Ｈｚにおける全鉄損Ｗ１０／４００が９．８Ｗ／ｋｇと良好な鉄損特性を得られるが、僅か３０℃の磁性焼鈍温度の違いによって保磁力が大きく変化してしまい、良好な励磁特性および鉄損特性を安定して得るのは困難であった。 Comparative Example No. No. 12 has a composition of 0.51% Mn and 2.31% V + Mn. When the magnetic annealing temperature is 880 ° C., the metal structure becomes unstable and the average grain size is as small as 18.8 μm. The coercive force was 78.6 A / m, and good excitation characteristics could not be obtained. Moreover, the total magnetic loss W10 / 400 at an operating magnetic frequency density of 1T and an operating frequency of 400 Hz was 13.0 W / kg, and good iron loss characteristics were not obtained. In addition, No. No. 12 has a magnetic annealing temperature of 850 ° C., an average crystal grain size of 35.4 μm, a coercive force of 39.1 A / m and good excitation characteristics, and an operating magnetic flux density of 1 T and an operating frequency of 400 Hz. Good iron loss characteristics with a total iron loss W10 / 400 of 9.8 W / kg can be obtained, but the coercive force changes greatly due to the difference in magnetic annealing temperature of only 30 ° C., and good excitation characteristics and iron loss characteristics It was difficult to stably obtain
比較例Ｎｏ．１４、及び、Ｎｏ．１５Ａ〜Ｎｏ．１５Ｃは、Ｃをそれぞれ、０．０１４％、０．００９％含有する。そのため、磁性焼鈍温度が８５０℃において、多数の微細なＶ系炭化物がマトリックス中に分散し、該磁性焼鈍温度における結晶粒の成長を抑制してしまい、保磁力がそれぞれ、４５．５Ａ／ｍ、５１．０Ａ／ｍ、４６．８Ａ／ｍ、４３．３Ａ／ｍと、良好な励磁特性を得られないことが確認できた。また、比較例Ｎｏ．１５Ａ〜Ｎｏ．１５Ｃは、動作磁束密度を１Ｔとし動作周波数４００Ｈｚにおける全鉄損Ｗ１０／４００がそれぞれ、１２．１Ｗ／ｋｇ、１１．３Ｗ／ｋｇ、１１．７Ｗ／ｋｇと良好な鉄損特性も得られなかった。
なお、比較例Ｎｏ．１４、及び、Ｎｏ．１５Ａ〜Ｎｏ．１５Ｃは、磁性焼鈍温度が８８０℃において、保磁力がそれぞれ、３０．５Ａ／ｍ、２９．５Ａ／ｍ、３１．３Ａ／ｍ、３１．２Ａ／ｍと、良好な励磁特性が得られ、且つ、動作磁束密度を１Ｔとし動作周波数４００Ｈｚにおける全鉄損Ｗ１０／４００がそれぞれ、９．０Ｗ／ｋｇ、９．６Ｗ／ｋｇ、９．９Ｗ／ｋｇ、９．７Ｗ／ｋｇと良好な鉄損特性も得られるが、僅か３０℃の磁性焼鈍温度の違いによって保磁力が大きく変化してしまい、良好な励磁特性および鉄損特性を安定して得るのは困難であった。
以上の結果から、本発明で規定する成分範囲外となる合金では、僅かな磁性焼鈍の変化により、大きく保磁力が変化してしまい、工業的な量産を行なう場合、励磁特性および鉄損特性が不安定となる危険性があることが分る。
Comparative Example No. 14 and No. 15A-No. 15C contains 0.014% and 0.009% of C, respectively. Therefore, when the magnetic annealing temperature is 850 ° C., a large number of fine V-based carbides are dispersed in the matrix, suppressing the growth of crystal grains at the magnetic annealing temperature, and the coercive force is 45.5 A / m, 51.0 A / m, 46.8 A / m, and 43.3 A / m, confirming that good excitation characteristics cannot be obtained. Comparative Example No. 15A-No. In 15C, the operating magnetic flux density was 1T, and the total iron loss W10 / 400 at an operating frequency of 400 Hz was 12.1 W / kg, 11.3 W / kg, 11.7 W / kg, respectively, and good iron loss characteristics were not obtained. .
Comparative Example No. 14 and No. 15A-No. 15C has good excitation characteristics such as 30.5 A / m, 29.5 A / m, 31.3 A / m, and 31.2 A / m, respectively, at a magnetic annealing temperature of 880 ° C., and The total iron loss W10 / 400 at an operating frequency of 400 Hz with an operating magnetic flux density of 1 T is 9.0 W / kg, 9.6 W / kg, 9.9 W / kg, and 9.7 W / kg, respectively. Although it was obtained, the coercive force greatly changed due to the difference in magnetic annealing temperature of only 30 ° C., and it was difficult to stably obtain good excitation characteristics and iron loss characteristics.
From the above results, in an alloy that falls outside the component range specified in the present invention, the coercive force greatly changes due to a slight change in magnetic annealing. It turns out that there is a risk of instability.
Ｎｏ．１６は、本発明で規定する成分を満たす合金である。
しかし、Ｎｏ．１６Ａ（比較例）は、冷間圧延前の固溶化熱処理温度を８５０℃とするもので、磁性焼鈍温度が８５０℃において、平均結晶粒径が２６．６μｍ、保磁力が４３．４Ａ／ｍと、良好な励磁特性を得られず、且つ、動作磁束密度を１Ｔとし動作周波数４００Ｈｚにおける全鉄損Ｗ１０／４００が１１．０Ｗ／ｋｇと良好な鉄損特性も得られなかった。これは、熱処理温度がγ変態温度未満であるため、多数の微細なＶ系炭化物がマトリックス中に分散し易くなり、磁性焼鈍温度における結晶粒の成長を抑制したためと考えられる。
なお、Ｎｏ．１６Ａにおいても、磁性焼鈍温度が８８０℃において、平均結晶粒径が５８．８μｍ、保磁力が３０．０Ａ／ｍと、良好な励磁特性が得られ、且つ、動作磁束密度を１Ｔとし動作周波数４００Ｈｚにおける全鉄損Ｗ１０／４００が９．３Ｗ／ｋｇと良好な鉄損特性も得られるが、固溶化熱処理工程の加熱温度が不十分であるため、僅か３０℃の磁性焼鈍温度の違いによって、保磁力が大きく変化してしまい、良好な励磁特性および鉄損特性を安定して得るのは困難であった。
このことから、適切に成分調整を行なったとしても、固溶化熱処理工程の加熱温度を適正としないと、良好な励磁特性および鉄損特性を安定して得るのは困難であることが分る。
No. 16 is an alloy satisfying the components defined in the present invention.
However, no. 16A (Comparative Example) is a solution heat treatment temperature before cold rolling of 850 ° C., the magnetic annealing temperature is 850 ° C., the average crystal grain size is 26.6 μm, and the coercive force is 43.4 A / m. In addition, good excitation characteristics could not be obtained, and the total iron loss W10 / 400 was 11.0 W / kg at an operating magnetic flux density of 1T and an operating frequency of 400 Hz, and good iron loss characteristics could not be obtained. This is probably because the heat treatment temperature is lower than the γ transformation temperature, so that many fine V-based carbides are easily dispersed in the matrix and suppress the growth of crystal grains at the magnetic annealing temperature.
In addition, No. Even at 16A, the magnetic annealing temperature was 880 ° C., the average crystal grain size was 58.8 μm, the coercive force was 30.0 A / m, and good excitation characteristics were obtained. The operating magnetic flux density was 1 T, and the operating frequency was 400 Hz. The total iron loss W10 / 400 is 9.3 W / kg, but good iron loss characteristics can be obtained. However, since the heating temperature of the solution heat treatment process is insufficient, the difference in magnetic annealing temperature is only 30 ° C. The magnetic force has changed greatly, and it has been difficult to stably obtain good excitation characteristics and iron loss characteristics.
From this, it can be understood that even if the components are appropriately adjusted, it is difficult to stably obtain good excitation characteristics and iron loss characteristics unless the heating temperature in the solution heat treatment step is appropriate.
Ｎｏ．１６Ｄ及び１６Ｅは、板厚が本発明で規定する範囲より厚いものである。
Ｎｏ．１６Ｄ（比較例）は、板厚が２５０μｍである。そのため、板厚の厚いＮｏ．１６Ｄでは、磁性焼鈍温度が８５０℃において、平均結晶粒径が４０．１μｍ、保磁力が３７．６Ａ／ｍと、良好な励磁特性を得られたが、動作磁束密度を１Ｔとし動作周波数４００Ｈｚにおける全鉄損Ｗ１０／４００が１２．４Ｗ／ｋｇと良好な鉄損特性が得られなかった。
これは、２００μｍを超える板厚としたことで、励磁特性の向上によるヒステリシス損失の低減よりも、板厚の増加による渦電流損失の増加の方が大きな影響を及ぼしたためと考えられる。
このことから、成分、製造プロセスの適正化により、励磁特性の向上を成しても、板厚が厚くなり過ぎると、良好な鉄損特性を安定して得るのは困難であることが分る。
No. 16D and 16E are thicker than the range defined in the present invention.
No. 16D (comparative example) has a plate thickness of 250 μm. Therefore, the thick plate No. In 16D, the magnetic annealing temperature was 850 ° C., the average crystal grain size was 40.1 μm, the coercive force was 37.6 A / m, and good excitation characteristics were obtained, but the operating magnetic flux density was 1 T and the operating frequency was 400 Hz. The total iron loss W10 / 400 was 12.4 W / kg, and good iron loss characteristics were not obtained.
This is presumably because the increase in eddy current loss due to the increase in plate thickness had a greater effect than the reduction in hysteresis loss due to the improvement in excitation characteristics because the plate thickness exceeded 200 μm.
From this, it can be seen that even if the excitation characteristics are improved by optimizing the components and the manufacturing process, it is difficult to stably obtain good iron loss characteristics if the plate thickness becomes too thick. .
Ｎｏ．１６Ｅ（比較例）は、冷間圧延率を８６．０％、板厚を３５０μｍとするもので、磁性焼鈍温度が８５０℃において、保磁力が４１．１Ａ／ｍと、良好な励磁特性が得られなかった。さらに、動作磁束密度を１Ｔとし動作周波数４００Ｈｚにおける全鉄損Ｗ１０／４００が１７．３Ｗ／ｋｇと著しく増加し、良好な鉄損特性も得られなかった。
これは、冷間圧延率を９０％未満としたことで、該磁性焼鈍温度における結晶粒の成長が促進されなかったために、良好な励磁特性が得られなかったものと思われる。加えて、２００μｍを超える板厚としたことで、板厚の増加による渦電流損失の増加が引き起こされ、動作磁束密度を１Ｔとし動作周波数４００Ｈｚにおける全鉄損Ｗ１０／４００の著しい増加をまねいたと思われる。
このことから、適切に成分調整を行なったとしても、冷間圧延の圧延率が低く、また、板厚が厚くなり過ぎると、良好な励磁特性および鉄損特性を安定して得るのは困難であることが分る。
No. 16E (Comparative Example) has a cold rolling rate of 86.0% and a plate thickness of 350 μm, and a magnetic annealing temperature of 850 ° C. and a coercive force of 41.1 A / m provide good excitation characteristics. I couldn't. Furthermore, the total magnetic loss W10 / 400 at an operating magnetic flux density of 1T and an operating frequency of 400 Hz significantly increased to 17.3 W / kg, and good iron loss characteristics were not obtained.
This is presumably because when the cold rolling rate was less than 90%, the growth of crystal grains at the magnetic annealing temperature was not promoted, so that good excitation characteristics could not be obtained. In addition, the plate thickness exceeding 200 μm caused an increase in eddy current loss due to the increase in plate thickness, which caused a significant increase in total iron loss W10 / 400 at an operating frequency of 400 Hz with an operating magnetic flux density of 1T. Seem.
For this reason, even if the components are appropriately adjusted, it is difficult to stably obtain good excitation characteristics and iron loss characteristics when the rolling ratio of cold rolling is low and the plate thickness becomes too thick. I know that there is.
次に、本発明例Ｎｏ．９〜Ｎｏ．１１、Ｎｏ．１３、Ｎｏ．１６Ｂ及びＮｏ．１６Ｃと、比較例Ｎｏ．７、実施例Ｎｏ．１２、Ｎｏ．１５Ａ〜Ｎｏ．１５Ｃ及びＮｏ．１６Ａの磁気特性比較を図１示す。また、本発明例は何れも磁性焼鈍温度８５０℃及び８８０℃における両磁気特性、比較例Ｎｏ．７、Ｎｏ．１５Ａ〜Ｎｏ．１５Ｃ及びＮｏ．１６Ａは磁性焼鈍温度８５０℃、比較例Ｎｏ．１２は磁性焼鈍温度８８０℃の磁気特性である。
なお、横軸に保磁力（Ｈｃ）、縦軸に全鉄損（Ｗ１０／４００）をとり、本発明例は「○」、比較例は「×」とした。
図１の結果から、本発明の鉄心用磁性材では、成分範囲、製造プロセス条件を最適化し、保磁力を４０Ａ／ｍ未満とした効果により、上記最適化を行わず、保磁力が４０Ａ／ｍ以上となる比較例に比べて、良好な全鉄損（Ｗ１０／４００）が得られることが分かる。
Next, Invention Example No. 9-No. 11, no. 13, no. 16B and No. 16C and Comparative Example No. 7, Example No. 12, no. 15A-No. 15C and No. A comparison of the magnetic properties of 16A is shown in FIG. In addition, both examples of the present invention have both magnetic characteristics at magnetic annealing temperatures of 850 ° C. and 880 ° C. 7, no. 15A-No. 15C and No. 16A is a magnetic annealing temperature of 850 ° C. Reference numeral 12 denotes magnetic characteristics at a magnetic annealing temperature of 880 ° C.
The coercive force (Hc) is taken on the horizontal axis, the total iron loss (W10 / 400) is taken on the vertical axis, and “O” in the present invention example and “X” in the comparative example.
From the results of FIG. 1, in the magnetic material for iron core of the present invention, the coercive force is 40 A / m without performing the above optimization due to the effect of optimizing the component range and manufacturing process conditions and setting the coercive force to less than 40 A / m. It can be seen that better total iron loss (W10 / 400) can be obtained as compared with the comparative example described above.
図２に、本発明例Ｎｏ．１６Ｃと、比較例Ｎｏ．１６Ｄ、Ｎｏ．１６Ｅの、磁性焼鈍温度８５０℃における磁気特性比較を示す。横軸に板厚、縦軸に全鉄損（Ｗ１０／４００）をとり、本発明例は「○」、比較例は「×」とした。
本発明の鉄心用磁性材では、板厚を２００μｍ以下とする効果により、板厚が２００μｍを超える比較例に比べて、良好な全鉄損（Ｗ１０／４００）が得られることが分かる。
In FIG. 16C and Comparative Example No. 16D, no. 16E shows a comparison of magnetic properties at a magnetic annealing temperature of 850 ° C. The plate thickness is taken on the horizontal axis, and the total iron loss (W10 / 400) is taken on the vertical axis. The example of the present invention is “◯” and the comparative example is “x”.
In the magnetic material for iron core of the present invention, it can be seen that a good total iron loss (W10 / 400) can be obtained by the effect of setting the plate thickness to 200 μm or less as compared with the comparative example in which the plate thickness exceeds 200 μm.
次に、本発明例Ｎｏ．９〜Ｎｏ．１１、Ｎｏ．１３、Ｎｏ．１６Ｂ及びＮｏ．１６Ｃと、比較例Ｎｏ．１４、Ｎｏ．１５Ｂ及びＮｏ．１５Ｃの、磁性焼鈍温度が８５０℃における磁気特性比較を図３に示す。横軸にＣ量、縦軸に保磁力（Ｈｃ）をとったものである。なお、本発明例は「○」、比較例は「×」とした。
本発明の鉄心用磁性材では、Ｃ量を、質量％で、０．００８％以下とする効果により、Ｃ量のみが０．００８％を超え、本発明の範囲から外れる比較例と比べて、良好な励磁特性が得られることが分かる。
Next, Invention Example No. 9-No. 11, no. 13, no. 16B and no. 16C and Comparative Example No. 14, no. 15B and No. FIG. 3 shows a comparison of magnetic characteristics of 15C at a magnetic annealing temperature of 850 ° C. The horizontal axis represents the amount of C, and the vertical axis represents the coercive force (Hc). In addition, the example of this invention was set as "(circle)" and the comparative example was set as "*".
In the magnetic material for iron core of the present invention, the amount of C is 0.008% or less in mass%, so that only the amount of C exceeds 0.008%, compared with a comparative example that deviates from the scope of the present invention. It can be seen that good excitation characteristics can be obtained.
図４に、本発明例Ｎｏ．９〜Ｎｏ．１１、Ｎｏ．１３、Ｎｏ．１６Ｂ及びＮｏ．１６Ｃと、比較例Ｎｏ．７、Ｎｏ．１２の、磁性焼鈍温度が８８０℃における磁気特性比較を示す。横軸にＶ＋Ｍｎ量、縦軸に保磁力（Ｈｃ）をとったものである。なお、本発明例は「○」、比較例は「×」とした。
本発明の鉄心用磁性材では、Ｖ＋Ｍｎ量を、質量％で、２．１５％以下とする効果により、Ｖ＋Ｍｎ量がこの範囲を外れる比較例と比べて、良好な励磁特性が得られることが分かる。
In FIG. 9-No. 11, no. 13, no. 16B and no. 16C and Comparative Example No. 7, no. 12 shows a comparison of magnetic characteristics at a magnetic annealing temperature of 880 ° C. The horizontal axis represents the amount of V + Mn, and the vertical axis represents the coercive force (Hc). In addition, the example of this invention was set as "(circle)" and the comparative example was set as "*".
In the magnetic material for iron core of the present invention, it can be seen that, due to the effect that the amount of V + Mn is 2.15% or less in mass%, excellent excitation characteristics can be obtained as compared with the comparative example in which the amount of V + Mn is out of this range. .
図５に、本発明例Ｎｏ．９〜Ｎｏ．１１、Ｎｏ．１３、Ｎｏ．１６Ｂ及びＮｏ．１６Ｃと、比較例Ｎｏ．８及びＮｏ．１２の、磁性焼鈍温度が８５０℃における磁気特性比較を示す。横軸にＭｎ／Ｓ（質量％の比）、縦軸に保磁力（Ｈｃ）をとったものである。なお、本発明例は「○」、比較例は「×」とした。加えて、比較例Ｎｏ．１２の、磁性焼鈍温度が８５０℃におけるＭｎ／Ｓと保磁力（Ｈｃ）との関係も、参考までに「△」として記載した。
本発明の鉄心用磁性材では、Ｍｎ／Ｓを、質量％の比で、１０〜１００とする効果により、Ｍｎ／Ｓがこの範囲を外れる比較例と比べて、良好な励磁特性が得られることが分かる。
In FIG. 9-No. 11, no. 13, no. 16B and No. 16C and Comparative Example No. 8 and no. 12 shows a comparison of magnetic characteristics at a magnetic annealing temperature of 850 ° C. The horizontal axis represents Mn / S (ratio by mass%), and the vertical axis represents coercive force (Hc). In addition, the example of this invention was set to "(circle)", and the comparative example was set to "x". In addition, Comparative Example No. 12, the relationship between Mn / S and the coercive force (Hc) at a magnetic annealing temperature of 850 ° C. is also indicated as “Δ” for reference.
In the magnetic material for iron core of the present invention, excellent excitation characteristics can be obtained compared to the comparative example in which Mn / S is out of this range due to the effect of setting Mn / S to 10 to 100 by mass ratio. I understand.
図６に、Ｎｏ．９〜Ｎｏ．１１、Ｎｏ．１３、Ｎｏ．１６Ｂ及びＮｏ．１６Ｃと、比較例Ｎｏ．７、Ｎｏ．１２、Ｎｏ．１５Ａ及びＮｏ．１６Ａの磁気特性比較を示す。また、本発明例は何れも磁性焼鈍温度８５０℃及び８８０℃における両磁気特性、比較例Ｎｏ．７、Ｎｏ．１５Ａ及びＮｏ．１６Ａは磁性焼鈍温度８５０℃、比較例Ｎｏ．１２は磁性焼鈍温度８８０℃の磁気特性である。なお、横軸に平均結晶粒径、縦軸に保磁力（Ｈｃ）をとり、本発明例は「○」、比較例は「×」とした。
本発明の鉄心用磁性材では、平均結晶粒径を３０μｍ以上とする効果により、平均結晶粒径が３０μｍ未満の比較例と比べて、良好な励磁特性が得られることが分かる。
なお、図７にＮｏ．７（比較例）、図８にＮｏ．１６Ａ（比較例）、図９にＮｏ．１６Ｂ（本発明例）及び図１０にＮｏ．１６Ｃ（本発明例）の、加熱温度が８５０℃の磁性焼鈍を行った後の光学顕微鏡による断面ミクロ組織写真を示す。組織観察は全て、乾式のフラットミリング（Ａｒイオンによる逆スパッタ）仕上にて実施した。
本発明の鉄心用磁性材が、比較例と比べて、結晶粒径が大きいことが確認できた。
In FIG. 9-No. 11, no. 13, no. 16B and No. 16C and Comparative Example No. 7, no. 12, no. 15A and No. The magnetic characteristic comparison of 16A is shown. In addition, both examples of the present invention have both magnetic characteristics at magnetic annealing temperatures of 850 ° C. and 880 ° C. 7, no. 15A and No. 16A is a magnetic annealing temperature of 850 ° C. Reference numeral 12 denotes magnetic characteristics at a magnetic annealing temperature of 880 ° C. The horizontal axis represents the average crystal grain size, the vertical axis represents the coercive force (Hc), and the example of the present invention was “◯” and the comparative example was “x”.
In the magnetic material for iron core of the present invention, it can be seen that excellent excitation characteristics can be obtained by the effect of setting the average crystal grain size to 30 μm or more as compared with the comparative example having an average crystal grain size of less than 30 μm.
In FIG. 7 (comparative example) and FIG. 16A (comparative example), FIG. 16B (example of the present invention) and FIG. The cross-sectional microstructure photograph by the optical microscope after performing the magnetic annealing of heating temperature 850 degreeC of 16C (invention example) is shown. All the structure observations were performed by dry flat milling (reverse sputtering with Ar ions) finish.
It was confirmed that the magnetic material for iron core of the present invention had a larger crystal grain size than the comparative example.
図１１に、本発明例Ｎｏ．１６Ｂ、Ｎｏ．１６Ｃと、比較例Ｎｏ．１６Ａの、磁性焼鈍温度が８５０℃における磁気特性比較を示す。横軸に固溶化熱処理温度、縦軸に保磁力（Ｈｃ）をとったものである。なお、本発明例は「○」、比較例は「×」とした。
本発明の鉄心用磁性材では、固溶化熱処理温度をγ変態温度以上とする効果により、γ変態温度未満の比較例と比べて、良好な励磁特性が得られることが分かる。
なお、図１２にＮｏ．１６Ａ（比較例）、図１３にＮｏ．１６Ｂ（本発明例）及び図１４にＮｏ．１６Ｃ（本発明例）の、固溶化熱処理を行った後の光学顕微鏡による断面ミクロ組織写真を示す。ここで、組織観察は全て、薬液による腐食にて実施した。
図１２に示すＮｏ．１６Ａ（比較例）は、α（フェライト）単相組織を呈しており、加熱温度が８５０℃の固溶化熱処理において、γ変態温度未満の加熱であることが確認できた。
図１３に示すＮｏ．１６Ｂ（本発明例）は、二相組織を呈しており、加熱温度が９５０℃の固溶化熱処理において、α（フェライト）−γ（オーステナイト）二相組織を有する、γ変態温度以上まで加熱されていることが確認できた。
図１４に示すＮｏ．１６Ｃ（本発明例）は、結晶粒の乱れた単相組織を呈しており、加熱温度が１０５０℃の固溶化熱処理において、γ単相組織を有する、γ変態温度以上まで加熱されていることが確認できた。
In FIG. 16B, no. 16C and Comparative Example No. 16A shows a comparison of magnetic characteristics at a magnetic annealing temperature of 850 ° C. The horizontal axis represents the solution heat treatment temperature, and the vertical axis represents the coercive force (Hc). In addition, the example of this invention was set to "(circle)", and the comparative example was set to "x".
In the magnetic material for iron core of the present invention, it can be seen that, due to the effect that the solution heat treatment temperature is equal to or higher than the γ transformation temperature, excellent excitation characteristics can be obtained as compared with the comparative example having a temperature lower than the γ transformation temperature.
In FIG. 16A (comparative example), FIG. 16B (invention example) and FIG. The cross-sectional microstructure photograph by the optical microscope after performing solution heat treatment of 16C (invention example) is shown. Here, all the structure observations were carried out by corrosion with a chemical solution.
No. 1 shown in FIG. 16A (Comparative Example) exhibited an α (ferrite) single-phase structure, and it was confirmed that the heating was less than the γ transformation temperature in the solution heat treatment at a heating temperature of 850 ° C.
No. 1 shown in FIG. 16B (Example of the present invention) has a two-phase structure, and is heated to a temperature equal to or higher than the γ transformation temperature, which has an α (ferrite) -γ (austenite) two-phase structure in a solution heat treatment at a heating temperature of 950 ° C. It was confirmed that
No. 1 shown in FIG. 16C (Example of the present invention) exhibits a single-phase structure with disordered crystal grains, and is heated to a temperature equal to or higher than the γ transformation temperature having a γ single-phase structure in a solution heat treatment at a heating temperature of 1050 ° C. It could be confirmed.
図１５に、本発明例Ｎｏ．１６Ｃと、比較例Ｎｏ．１６Ｅの、磁性焼鈍温度が８５０℃における磁気特性比較を示す。横軸に冷間圧延率、縦軸に保磁力（Ｈｃ）をとったものである。なお、本発明例は「○」、比較例は「×」とした。加えて、比較例Ｎｏ．１６Ｄの、磁性焼鈍温度が８５０℃における冷間圧延率と保磁力（Ｈｃ）との関係も、参考までに「△」として記載した。
本発明の鉄心用磁性材では、冷間圧延率を９０％以上とする効果により、冷間圧延率が９０％未満の比較例と比べて、良好な励磁特性が得られることが分かる。
In FIG. 16C and Comparative Example No. 16E shows a comparison of magnetic characteristics at a magnetic annealing temperature of 850 ° C. The horizontal axis represents the cold rolling rate and the vertical axis represents the coercive force (Hc). In addition, the example of this invention was set to "(circle)", and the comparative example was set to "x". In addition, Comparative Example No. The relationship between the cold rolling rate and the coercive force (Hc) of 16D at a magnetic annealing temperature of 850 ° C. is also indicated as “Δ” for reference.
In the magnetic material for iron cores of the present invention, it can be seen that, due to the effect of setting the cold rolling rate to 90% or more, excellent excitation characteristics can be obtained as compared with the comparative example having a cold rolling rate of less than 90%.
図１６に、Ｎｏ．９〜Ｎｏ．１１、Ｎｏ．１３、Ｎｏ．１６Ｂ及びＮｏ．１６Ｃと、比較例Ｎｏ．７、Ｎｏ．８、Ｎｏ．１２、Ｎｏ．１４、Ｎｏ．１５Ａ〜Ｎｏ．１５Ｃ及びＮｏ．１６Ａの磁気特性比較を示す。横軸に磁性焼鈍温度、縦軸に保磁力（Ｈｃ）をとったものである。なお、本発明例は「○」、比較例は「×」とした。
本発明の鉄心用磁性材では、成分範囲、製造プロセス条件を最適化することで、最適化の成されていない比較例と比べて、８００〜９００℃の磁性焼鈍温度によらず、良好な励磁特性を得られることが分かる。
In FIG. 9-No. 11, no. 13, no. 16B and No. 16C and Comparative Example No. 7, no. 8, no. 12, no. 14, no. 15A-No. 15C and No. The magnetic characteristic comparison of 16A is shown. The horizontal axis represents the magnetic annealing temperature, and the vertical axis represents the coercive force (Hc). In addition, the example of this invention was set as "(circle)" and the comparative example was set as "*".
In the magnetic material for iron core of the present invention, by optimizing the component range and manufacturing process conditions, excellent excitation can be achieved regardless of the magnetic annealing temperature of 800 to 900 ° C. as compared with the comparative example which is not optimized. It can be seen that the characteristics can be obtained.
（実施例２）
続いて、本発明に係る鉄心用磁性材を鉄心として、回転機のステータに適用した場合の効果をＣＡＥ解析により評価した結果について説明する。
このＣＡＥ解析においては、表２に示す本発明例Ｎｏ．１６Ｃと、比較例Ｎｏ、１５Ａの鉄心用磁性材（磁気焼鈍温度はいずれも８５０°）を鉄心として、図１７に示す回転機１のステータ２に適用した場合に、それぞれのモータトルク、モータ損失をＣＡＥ解析（電磁界解析ソフトウェア）により計算した。
(Example 2)
Then, the result of having evaluated the effect at the time of applying to the stator of a rotary machine by making the magnetic material for iron cores which concerns on this invention into an iron core by a CAE analysis is demonstrated.
In this CAE analysis, the present invention example No. When applied to the stator 2 of the rotating machine 1 shown in FIG. 17 using the magnetic material for iron core of 16C and Comparative Examples No. 15A (magnetic annealing temperatures are all 850 °) as the iron core, the respective motor torque and motor loss. Was calculated by CAE analysis (electromagnetic field analysis software).
なお、このＣＡＥによる解析条件の概要は次の通りである。
ステータ、ロータの形状 ： 自動車用モータの形状と同一のモデルを作成
（ステータ、ロータ、コイル、磁石、空気部）
材料 ： 各部位に材料特性の定義
（ＢＨ特性、鉄損特性、電気抵抗値、密度）
モータ損失 ： ロータの鉄損とステータの鉄損の和
The outline of the analysis conditions by CAE is as follows.
Stator and rotor shapes: Create the same model as the motor motor shape
(Stator, rotor, coil, magnet, air part)
Material: Definition of material properties for each part
(BH characteristics, iron loss characteristics, electrical resistance, density)
Motor loss: Sum of rotor iron loss and stator iron loss
上記した解析条件で実施したＣＡＥ解析の結果を表３に示す。表３に示すように、モータトルクについては、本発明例Ｎｏ．１６Ｃ、比較例Ｎｏ、１５Ａともに１２４（Ｎ・ｍ）と同一の値が得られた。これに対して、モータ損失（ロータの鉄損とステータの鉄損の和）については、本発明例Ｎｏ．１６Ｃの鉄心用磁性材は、比較例Ｎｏ、１５Ａと比較して２２．２％のモータ損失が向上することが確認された。
上記したＣＡＥ解析の結果により、本発明に係る鉄心用磁性材を用いた鉄心を、回転機のステータ本体、ロータ本体、トランスのコア、リアクトルのコアとして適用すると、良好な効率向上が可能となると判断できる。なお、本発明に係る鉄心用磁性材をトランスのコアあるいはリアクトルのコアに適用した場合、一般的には前記したモータ等の電動回転機（モータ）よりも高い周波数環境で用いられる。周波数が高いときに発生する渦損は回転数に二乗で大きくなるため、鉄損の低い本発明の鉄心用磁性材の効果はより顕著となる。
Table 3 shows the results of CAE analysis performed under the analysis conditions described above. As shown in Table 3, for the motor torque, Example No. of the present invention. The same value as 124 (N · m) was obtained for both 16C and Comparative Examples No and 15A. On the other hand, regarding the motor loss (the sum of the iron loss of the rotor and the iron loss of the stator), the invention example No. It was confirmed that the 16C iron core magnetic material improved in 22.2% motor loss as compared with Comparative Examples No and 15A.
As a result of the above-described CAE analysis, when an iron core using the magnetic material for iron core according to the present invention is applied as a stator body of a rotating machine, a rotor body, a core of a transformer, and a core of a reactor, a favorable efficiency improvement can be achieved. I can judge. When the magnetic material for iron core according to the present invention is applied to a transformer core or a reactor core, it is generally used in a higher frequency environment than an electric rotating machine (motor) such as the motor described above. Since the vortex loss generated when the frequency is high is increased by the square of the number of revolutions, the effect of the magnetic material for iron core of the present invention having a low iron loss becomes more remarkable.
本発明の鉄心用磁性材は、小型・軽量化、高出力化及び高効率化が必要とされる回転機、トランスのコア、リアクトルのコア、等の鉄心（磁心材料）として使用するのに最も適した材料である。 The magnetic material for iron cores of the present invention is most suitable for use as iron cores (magnetic core materials) for rotating machines, transformer cores, reactor cores, etc. that require miniaturization, weight reduction, high output and high efficiency. Suitable material.
１ ：回転機
２ ：ステータ
２ａ：ヨーク部
２ｂ：ティース部
２ｃ：コイル
３ ：ロータ
３ａ：ロータヨーク
３ｂ：永久磁石
DESCRIPTION OF SYMBOLS 1: Rotating machine 2: Stator 2a: Yoke part 2b: Teeth part 2c: Coil 3: Rotor 3a: Rotor yoke 3b: Permanent magnet
Claims (3)
An iron core using the iron core magnetic material according to claim 1.
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| JP2010036995A JP2011174103A (en) | 2010-02-23 | 2010-02-23 | Magnetic material for iron core, method for producing the same, and iron core |
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| JP2010036995A JP2011174103A (en) | 2010-02-23 | 2010-02-23 | Magnetic material for iron core, method for producing the same, and iron core |
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Cited By (4)
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| JP2015508447A (en) * | 2011-12-16 | 2015-03-19 | アペラム | Method for producing a thin strip made of soft magnetic alloy and the resulting strip |
| CN105467347A (en) * | 2015-11-17 | 2016-04-06 | 国网浙江省电力公司电力科学研究院 | Voltage transformer excitation characteristic curve calculating method |
| CN105740569A (en) * | 2016-02-24 | 2016-07-06 | 国家电网公司 | Current transformer engineering model building method based on transient large current testing technology |
| WO2017017526A3 (en) * | 2015-07-28 | 2017-03-09 | Can As Sun, Inc. | Stator magnetic core brushless motor apparatus, system and methods |
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- 2010-02-23 JP JP2010036995A patent/JP2011174103A/en active Pending
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2015508447A (en) * | 2011-12-16 | 2015-03-19 | アペラム | Method for producing a thin strip made of soft magnetic alloy and the resulting strip |
| US10957481B2 (en) | 2011-12-16 | 2021-03-23 | Aperam | Process for manufacturing a thin strip made of soft magnetic alloy and strip obtained |
| US11600439B2 (en) | 2011-12-16 | 2023-03-07 | Aperam | Process for manufacturing a thin strip made of soft magnetic alloy and strip obtained |
| WO2017017526A3 (en) * | 2015-07-28 | 2017-03-09 | Can As Sun, Inc. | Stator magnetic core brushless motor apparatus, system and methods |
| CN105467347A (en) * | 2015-11-17 | 2016-04-06 | 国网浙江省电力公司电力科学研究院 | Voltage transformer excitation characteristic curve calculating method |
| CN105467347B (en) * | 2015-11-17 | 2018-04-10 | 国网浙江省电力公司电力科学研究院 | A kind of voltage transformer exciting characteristic curve acquiring method |
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