JP2013227649A - Steel plate for high output reluctance motor iron core, method of manufacturing the steel plate, rotor for reluctance motor and stator using the steel plate as raw material, and reluctance motor - Google Patents
Steel plate for high output reluctance motor iron core, method of manufacturing the steel plate, rotor for reluctance motor and stator using the steel plate as raw material, and reluctance motor Download PDFInfo
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Abstract
Description
本発明は、電気自動車やハイブリッド自動車或いは工作機械など広範囲な用途に使用されるスイッチトリラクタンスモータおよび/またはシンクロナスリラクタンスモータを初めとするリラクタンストルクを活用するモータ（以下これらを総称してリラクタンスモータと記す）の鉄心用鋼板とその製造方法、これを素材とするリラクタンスモータ用ロータ、ステータおよびリラクタンスモータに関する。 The present invention relates to a motor using a reluctance torque such as a switched reluctance motor and / or a synchronous reluctance motor used in a wide range of applications such as an electric vehicle, a hybrid vehicle, or a machine tool (hereinafter collectively referred to as a reluctance motor). And a manufacturing method thereof, a rotor for a reluctance motor using the same, a stator, and a reluctance motor.
リラクタンスモータは、高価な永久磁石を必ずしも必要としないため、永久磁石を大量に使用するＰＭモータと比較して高トルクが得にくいものの、安価かつ高速回転領域での効率に優れており、ハイブリッド自動車及び電気自動車の駆動用モータ及び発電用モータ、家電製品、並びに各種の工作機械や産業機械用のモータ等、広範囲な用途への適用が期待されている。 Reluctance motors do not necessarily require expensive permanent magnets, so although it is difficult to obtain high torque compared to PM motors that use a large amount of permanent magnets, they are inexpensive and have excellent efficiency in the high-speed rotation region. In addition, it is expected to be applied to a wide range of applications such as electric motor drive motors and power generation motors, home appliances, and motors for various machine tools and industrial machines.
リラクタンスモータの鉄心は、固定子（ステータ）と回転子（ロータ）とに分けられる。ステータ側の鉄心には巻線を通じて交流磁界が直接付与されるので、効率を高くするために高透磁率であると同時に、体積抵抗率を高めて鉄損を低減できることが要求される。
このため、一般にステータ側の鉄心には、極低炭素鋼にＳｉを添加して軟磁気特性を改善したいわゆる電磁鋼板が用いられる（例えば、特許文献１を参照）。
The iron core of a reluctance motor is divided into a stator (stator) and a rotor (rotor). Since an AC magnetic field is directly applied to the stator-side iron core through the winding, it is required to have high magnetic permeability in order to increase efficiency, and at the same time, to increase the volume resistivity and to reduce iron loss.
For this reason, a so-called electromagnetic steel sheet in which soft magnetic properties are improved by adding Si to an extremely low carbon steel is generally used for the iron core on the stator side (see, for example, Patent Document 1).
ロータ側の鉄心にはステータ側から発生する磁界による吸引力に基づき高トルクを得るため、高透磁率かつ高磁束密度であることが望ましい。また、ステータのみに電磁鋼板を使用すると電磁鋼板の製品歩留りが低下して、モータの製造コストが高くなるので、通常はロータ側の鉄心にもステータ側と同じ電磁鋼板が用いられる（特許文献１を参照）。 It is desirable that the rotor side iron core has a high magnetic permeability and a high magnetic flux density in order to obtain a high torque based on an attractive force generated by a magnetic field generated from the stator side. In addition, when the electromagnetic steel sheet is used only for the stator, the product yield of the electromagnetic steel sheet is reduced and the manufacturing cost of the motor is increased. See).
また、ロータおよびまたはステータの鉄心材として、ＳｉとＡｌを合計で０．２％未満の構造用鋼であるＳＰＣＣ極薄材を用いる電動機が特許文献２に開示されている。ＳＰＣＣ材は、ＳｉやＡｌ含有量が電磁鋼板と比べて低いことから、いわゆる電磁鋼板よりも磁束密度が高くなり、少ない磁力で高い磁束密度となると考えられ、高効率化に有効である。
Further,
しかしながら、特許文献２では、ＳｉおよびＡｌ含有量を制限することで素材の磁束密度の向上を図っているが、いわゆるＳＰＣＣ材では、Ｃ，Ｍｎ等の不純物元素が多く含まれるため、飽和磁束密度の向上は必ずしも十分ではなく、また、一般的なＳＰＣＣ材では、結晶粒径は平均で２５μｍ以下の細かい粒径しか得られず、低磁場側での磁束密度も極低炭素で不可避的な不純物含有量も少ない電磁鋼板と比べ、必ずしも十分な磁束密度の高さは得られない。
However, although
従って、本発明は、上記のような課題を解決するためになされたものであり、リラクタンスモータの鉄心として用いるときに、出力トルクをより大きくでき、最大回転数をより高くできる鋼板を提供することを目的とする。
また、本発明は、そのようなリラクタンスモータの鉄心用鋼板の製造方法を提供することも目的とする。
さらに、本発明は、前記鋼板を鉄心として使用したリラクタンスモータのロータおよびリラクタンスモータを提供することも目的とする。
なお、リラクタンスモータとは、一般にスイッチトリラクタンスモータやシンクロナスリラクタンスモータのことを意味する場合が多いが、本発明ではリラクタンストルクを活用するモータであれば良く、ＩＰＭモータを含むあらゆる種類のリラクタンストルクを活用するモータの鉄心への適用が可能である。
Therefore, the present invention has been made to solve the above-described problems, and provides a steel sheet that can increase the output torque and increase the maximum rotational speed when used as an iron core of a reluctance motor. With the goal.
Another object of the present invention is to provide a method for producing a steel sheet for an iron core of such a reluctance motor.
Another object of the present invention is to provide a reluctance motor rotor and a reluctance motor using the steel plate as an iron core.
The reluctance motor generally means a switched reluctance motor or a synchronous reluctance motor. However, in the present invention, any reluctance torque may be used as long as it uses a reluctance torque, and includes any IPM motor. It can be applied to the iron core of motors that utilize
そこで、本発明者らは、上記課題を解決すべく、種々検討した結果、磁束密度が高く、リラクタンスモータの高出力化に有効な鋼板およびその製造方法を見出した。また、これら種々の鋼板を素材としてリラクタンスモータを試作し、モータの性能評価を行った結果、電磁鋼板を素材とした場合と比べて、高出力、高効率が得られることを見出した。
即ち、本発明は、磁界の強さが５００Ａ／ｍの時の磁束密度Ｂ５００の値が１．００Ｔ以上かつ５０００Ａ／ｍの時の磁束密度Ｂ５０００の値が１．７０Ｔ以上であることを特徴とするリラクタンスモータの鉄心用鋼板およびその製造方法、更にはこれを素材としたリラクタンスモータのロータ、ステータおよびリラクタンスモータを開示するものである。
Accordingly, as a result of various studies to solve the above-mentioned problems, the present inventors have found a steel plate having a high magnetic flux density and effective for increasing the output of a reluctance motor, and a method for manufacturing the same. Moreover, as a result of making a reluctance motor as a prototype using these various steel plates and evaluating the performance of the motor, it was found that higher output and higher efficiency can be obtained compared to the case of using electromagnetic steel plates.
That is, according to the present invention, the value of the magnetic flux density B 500 when the magnetic field strength is 500 A / m is 1.00 T or more and the value of the magnetic flux density B 5000 when the magnetic field strength is 5000 A / m is 1.70 T or more. The present invention discloses a reluctance motor iron core steel plate and a manufacturing method thereof, and a reluctance motor rotor, stator, and reluctance motor using the same.
本発明によれば、リラクタンスモータの鉄心として用いるときに、電磁鋼板を素材としたリラクタンスモータの出力トルクをより大きくでき、最大回転数をより高くできる鋼板を提供することができる。 ADVANTAGE OF THE INVENTION According to this invention, when using as an iron core of a reluctance motor, the steel plate which can enlarge the output torque of the reluctance motor which used the electromagnetic steel plate as a raw material, and can make a maximum rotation speed higher can be provided.
本発明のリラクタンスモータの鉄心用鋼板は、磁界の強さが５００Ａ／ｍの時の磁束密度Ｂ５００の値が１．００Ｔ以上かつ５０００Ａ／ｍの時の磁束密度Ｂ５０００の値が１．７０Ｔ以上であることを特徴とするリラクタンスモータの鉄心用鋼板およびその製造方法を特徴とするものである。 Core steel sheet for reluctance motor of the present invention, the value of the magnetic flux density B 5000 when the value is 1.00T or more and 5000A / m of the magnetic flux density B 500 when the intensity of the magnetic field 500A / m is 1.70T The present invention is characterized by the iron core steel sheet for a reluctance motor and the method for manufacturing the same.
磁気特性を限定する理由は以下の通りである。
＜磁界の強さが５００Ａ／ｍの時の磁束密度Ｂ５００の値が１．００Ｔ以上かつ５０００Ａ／ｍの時の磁束密度Ｂ５０００の値が１．７０Ｔ以上＞
磁界の強さが５０００Ａ／ｍの時の磁束密度Ｂ５０００の値を１．７０Ｔ以上としているのは、高速回転させる際にｄ軸とｑ軸でのインダクタンスの値の差（突極比）に基づくリラクタンストルクを有効に活用し、とくに従来の電磁鋼板よりも高トルク、高出力化を図るためである。一般に、リラクタンストルクを有効に活用するには、５０００Ａ／ｍ以上の高磁場における磁束密度が高いことが有効であり、本発明では、磁界の強さが５０００Ａ／ｍの時の磁束密度Ｂ５０００の値が１．７０Ｔ以上とする。また、低磁場における磁束密度を高めると比較的低トルク域での効率にも有利となるので、磁界の強さが５００Ａ／ｍの時の磁束密度Ｂ５００の値が１．００Ｔ以上とすることが好ましい。
The reason for limiting the magnetic properties is as follows.
<The value of the magnetic flux density B 500 when the magnetic field strength is 500 A / m is 1.00 T or more and the value of the magnetic flux density B 5000 when the magnetic field strength is 5000 A / m is 1.70 T or more>
The value of the magnetic flux density B 5000 when the magnetic field strength is 5000 A / m is set to 1.70 T or more because of the difference in inductance value (saliency ratio) between the d-axis and the q-axis when rotating at high speed. This is to make effective use of the reluctance torque based thereon, and in particular to achieve higher torque and higher output than conventional electromagnetic steel sheets. In general, in order to effectively utilize the reluctance torque, it is effective that the magnetic flux density is high in a high magnetic field of 5000 A / m or more. In the present invention, the magnetic flux density B 5000 when the magnetic field strength is 5000 A / m is effective. The value is 1.70T or more. In addition, increasing the magnetic flux density in a low magnetic field is also advantageous for efficiency in a relatively low torque region, so the value of magnetic flux density B 500 when the magnetic field strength is 500 A / m should be 1.00 T or more. Is preferred.
板厚を限定する理由は以下の通りである。
＜板厚＞
板厚が厚くなると、渦電流損が増大しモータ効率が低下する。ロータ鉄心材としてはその影響を受けにくいため、０．５ｍｍ以下とすることが好ましい。一方、ステータ鉄心材としては、その影響が大きくなるため、鉄損抑制の観点から板厚は０．２ｍｍ以下であることが好ましい。
The reason for limiting the plate thickness is as follows.
<Thickness>
As the plate thickness increases, eddy current loss increases and motor efficiency decreases. Since it is hard to receive the influence as a rotor iron core material, it is preferable to set it as 0.5 mm or less. On the other hand, since the influence becomes large as a stator iron core material, it is preferable that plate | board thickness is 0.2 mm or less from a viewpoint of iron loss suppression.
金属組織を限定する理由は以下の通りである。
＜不可避的に含まれる介在物を除く金属組織がフェライト単相、平均の結晶粒径：２５μｍ以上＞
金属組織を高い飽和磁束密度を有するフェライト単相組織とすることで高磁場における磁束密度を高くすることが可能となる。また、結晶粒径を大きくすることで、磁壁の移動が容易になることに起因して、低磁場側の磁束密度も同時に高くすることが可能となる。
本発明では、磁界の強さが５００Ａ／ｍの時の磁束密度Ｂ５００の値を安定して１．００Ｔ以上とするためには、フェライト結晶粒径は２５μｍ以上にすることが好ましい。
The reason for limiting the metal structure is as follows.
<Metal structure excluding inclusions inevitably contained is a ferrite single phase, average crystal grain size: 25 μm or more>
By making the metal structure a ferrite single-phase structure having a high saturation magnetic flux density, the magnetic flux density in a high magnetic field can be increased. In addition, by increasing the crystal grain size, it becomes possible to simultaneously increase the magnetic flux density on the low magnetic field side due to the easy movement of the domain wall.
In the present invention, the ferrite crystal grain size is preferably 25 μm or more in order to stably set the magnetic flux density B 500 value when the magnetic field strength is 500 A / m to 1.00 T or more.
本発明の鋼板は、Ｃ：０．０１０質量％以下、Ｓｉ：０質量％〜１．０質量％、Ｍｎ：０質量％〜０．５質量％、Ｐ：０．１０質量％以下、Ｓ：０．０１０質量％以下、酸可溶Ａｌ：０．００５質量％以下、Ｎ：０．００５％以下、Ｏ：０．０２０質量％以下、残部がＦｅ及び不可避的不純物からなる成分組成を有することが好ましい。また、鋼材の成分の内、Ｓｉ：０．０１％質量以下であるほうがより好ましく、Ｔｉ、Ｎｂ及びＶからなる群から選択される１種以上の成分を合計して０．００５質量％〜０．０２０質量％さらに含有してもよい。また、Ｃｕ：０．０３質量％〜０．２質量％及びＮｉ：０質量％〜０．２質量％からなる群から選択される１種以上の成分をさらに含有してもよい。 The steel plate of the present invention has C: 0.010 mass% or less, Si: 0 mass% to 1.0 mass%, Mn: 0 mass% to 0.5 mass%, P: 0.10 mass% or less, S: 0.010% by mass or less, acid-soluble Al: 0.005% by mass or less, N: 0.005% or less, O: 0.020% by mass or less, and the balance is composed of Fe and inevitable impurities Is preferred. Further, among the components of the steel material, Si is more preferably 0.01% by mass or less, and a total of one or more components selected from the group consisting of Ti, Nb and V is 0.005% by mass to 0%. Further, it may be contained in an amount of .020 mass%. Moreover, you may further contain 1 or more types of components selected from the group which consists of Cu: 0.03- mass 0.2% and Ni: 0 mass-0.2 mass%.
鋼材の成分組成を限定する理由は以下の通りである。
＜Ｃ：０．０１０質量％以下＞
Ｃは、鋼中に固溶して鋼中の転位等の格子欠陥へ集積したり、炭化物として析出する等により、磁壁の移動を抑制するため、とくに低磁場側の磁束密度を低下させる元素であり、できるだけ少なくすることが好ましい。低磁場側での磁束密度を確保する観点からは、０．０１０質量％までは許容できるので、上限を０．０１０質量％とする。
The reason for limiting the component composition of the steel is as follows.
<C: 0.010 mass% or less>
C is an element that lowers the magnetic flux density especially on the low magnetic field side in order to suppress the domain wall movement by solid solution in the steel and accumulating in lattice defects such as dislocations in the steel or by precipitation as carbides. Yes, it is preferable to reduce as much as possible. From the viewpoint of securing the magnetic flux density on the low magnetic field side, up to 0.010% by mass is acceptable, so the upper limit is made 0.010% by mass.
＜Ｓｉ：０質量％〜１．０質量％＞
Ｓｉは体積抵抗率を高め、渦電流損を小さくするのに有効な他、磁気異方性や磁歪の改善を通じて、低磁場側の磁束密度の向上に有効な元素である。しかし、一方で添加量の増加に伴い飽和磁束密度を低下させ、高磁場側では不利となる。本発明ではＳｉは無添加とし、０．０１質量％以下とすることが望ましいが、渦電流損改善の観点からＳｉを添加する場合、５０００Ａ／ｍにおける磁束密度確保の観点から１．０質量％以下にすることが好ましい。
<Si: 0% by mass to 1.0% by mass>
Si is an element effective for increasing the volume resistivity and reducing the eddy current loss, and for improving the magnetic flux density on the low magnetic field side by improving the magnetic anisotropy and magnetostriction. However, on the other hand, the saturation magnetic flux density is lowered as the addition amount increases, which is disadvantageous on the high magnetic field side. In the present invention, Si is not added and is preferably 0.01% by mass or less, but when Si is added from the viewpoint of improving eddy current loss, 1.0% by mass from the viewpoint of securing a magnetic flux density at 5000 A / m. The following is preferable.
＜Ｍｎ：０質量％〜０．５質量％＞
Ｍｎは、体積抵抗率を高め、渦電流損を小さくするのに有効な元素である。しかし、一方で添加量の増加に伴い、Ｓｉと同様に飽和磁束密度を低下させ、高磁場側では不利となる。本発明では添加しなくてもよいが、添加する場合は、０．５質量％以下にすることが好ましい。
<Mn: 0% by mass to 0.5% by mass>
Mn is an element effective for increasing volume resistivity and reducing eddy current loss. On the other hand, however, the saturation magnetic flux density is lowered in the same manner as Si as the addition amount increases, which is disadvantageous on the high magnetic field side. Although it is not necessary to add in this invention, when adding, it is preferable to make it 0.5 mass% or less.
＜Ｐ：０．１０質量％以下＞
Ｐは、微量の添加で高強度化に有効な元素であり、降伏比を高め、打抜き加工の際に、打抜き端面のダレによる塑性変形の抑制に有効な元素である。この効果を得るためには、０．０１質量％以上添加することが望ましい。一方、０．１０質量％を超えて添加しても、降伏比を増加させる効果は飽和するばかりか、低温での靭性を劣化させるようになるため、上限を０．１０質量％とする。なお、Ｐは他の元素と比べ、少ない添加量で高強度化が可能であり、飽和磁束密度の低下も効果的に抑制することができる。
<P: 0.10% by mass or less>
P is an element effective for increasing strength by adding a small amount, and is an element effective for increasing the yield ratio and suppressing plastic deformation due to sagging of the punched end face during punching. In order to obtain this effect, it is desirable to add 0.01% by mass or more. On the other hand, even if added over 0.10% by mass, the effect of increasing the yield ratio is not only saturated, but also the toughness at low temperatures is deteriorated, so the upper limit is made 0.10% by mass. In addition, compared with other elements, P can be increased in strength with a small addition amount, and a decrease in saturation magnetic flux density can also be effectively suppressed.
＜Ｓ：０．０１０質量％以下＞
Ｓは、高温脆化を引き起こす元素であり、大量に含有させると、熱間圧延時に表面欠陥を生じ、表面品質を劣化させる。また、ＭｎＳ、ＴｉＳ等の介在物として析出すると、磁壁の移動を妨げるため、とくに低磁場側での磁束密度には有害である。したがって、できるだけ低減することが望まれる。０．０１０質量％までは許容できるため、上限を０．０１０質量％とする。
<S: 0.010 mass% or less>
S is an element that causes high-temperature embrittlement. If it is contained in a large amount, S causes surface defects during hot rolling and degrades the surface quality. Further, if it precipitates as inclusions such as MnS and TiS, the movement of the domain wall is hindered, which is harmful to the magnetic flux density particularly on the low magnetic field side. Therefore, it is desired to reduce as much as possible. Since 0.010 mass% is acceptable, the upper limit is set to 0.010 mass%.
＜酸可溶Ａｌ：０．００５質量％以下＞
一般的に、Ａｌは脱酸剤として添加されるほか、Ｓｉと同様に鋼の体積抵抗率を上昇させるのに有効な元素である。しかし、酸可溶Ａｌとして０．００５％を超えて含有させると、鋼中に微細なＡｌＮが析出してフェライトの粒成長が抑制され、これらの結果として、磁壁の移動が抑制され、低磁場側での磁束密度の低下を招く。
<Acid-soluble Al: 0.005% by mass or less>
In general, Al is added as a deoxidizer, and is an element effective for increasing the volume resistivity of steel, similar to Si. However, when it is contained in excess of 0.005% as acid-soluble Al, fine AlN precipitates in the steel, and ferrite grain growth is suppressed. As a result, the domain wall movement is suppressed, and the low magnetic field is reduced. The magnetic flux density on the side is reduced.
＜Ｎ：０．００５％以下＞
Ｎは、Ｃと同様に鋼中に固溶して鋼中の転位等の格子欠陥へ集積する等により、磁壁の移動を抑制するため、とくに低磁場側の磁束密度を低下させる元素であり、できるだけ少なくすることが好ましい。リラクタンスモータのロータ鉄心として用いるのに適した磁束密度を確保する観点からは、０．００５質量％までは許容できるので、上限を０．００５質量％とする。
<N: 0.005% or less>
N is an element that lowers the magnetic flux density especially on the low magnetic field side in order to suppress the movement of the domain wall by, for example, solid solution in steel and accumulating in lattice defects such as dislocations in the steel as in C. It is preferable to reduce as much as possible. From the viewpoint of securing a magnetic flux density suitable for use as a rotor core of a reluctance motor, 0.005 mass% is acceptable, so the upper limit is set to 0.005 mass%.
＜Ｏ：０．０２０質量％以下＞
Ｏは、Ａｌ，Ｓｉ，Ｍｎ，Ｆｅ等と酸化物系介在物として鋼中に晶出し、磁壁の移動を抑制するため、できるだけ低減することが好ましい。しかし、Ｔｉ，Ａｌ等の析出物と比べ比較的粗大で、磁壁の移動の抑制効果は大きくなく、０．０２０質量％までは許容できる。したがって、上限を０．０２０％とする。
<O: 0.020 mass% or less>
O is preferably reduced as much as possible in order to crystallize in the steel as oxide inclusions such as Al, Si, Mn, Fe and the like and suppress the movement of the domain wall. However, it is relatively coarse as compared with precipitates such as Ti and Al, and the effect of suppressing the domain wall movement is not large, and is acceptable up to 0.020% by mass. Therefore, the upper limit is made 0.020%.
＜Ｔｉ、Ｎｂ及びＶの１種以上：０．００５質量％〜０．０２０質量％＞
Ｔｉ、Ｎｂ及びＶは、鋼中で窒化物を形成し固溶Ｎを固定するのに有効である。その効果を得るためには、０．００５質量％以上の添加が必要である。しかし、０．０２０質量％を超えて添加すると、Ｎを固定するのに必要な量を超え、ＴｉやＮｂおよびＶ系の微細な炭化物が析出し、磁壁の移動を抑制して、低磁場側での磁束密度の低下を招く。
<One or more of Ti, Nb and V: 0.005 mass% to 0.020 mass%>
Ti, Nb and V are effective in forming nitrides in steel and fixing solute N. In order to acquire the effect, 0.005 mass% or more needs to be added. However, if added over 0.020% by mass, it exceeds the amount necessary to fix N, Ti, Nb and V-based fine carbides precipitate, suppress the domain wall movement, and lower the magnetic field side. Causes a decrease in magnetic flux density.
＜Ｃｕ：０．０３質量％〜０．２質量％及びＮｉ：０質量％〜０．２質量％からなる群から選択される１種以上＞
Ｃｕは、鋼中に固溶してＣｕＳとして析出するが、ＭｎＳやＴｉＳ等の他の硫化物とくらべ比較的粗大なため、磁壁の移動の障害になり難く、低磁場側での磁束密度の向上に有効である。この効果を得るためには少なくとも０．０３質量％以上の添加が必要である。
しかし、０．２質量％を超えて添加してもその効果は飽和するとともに、製造コストの増大を招く。一方、Ｃｕを単独で添加すると、熱間圧延時に耳割れ等の表面欠陥を生じやすくなる。Ｎｉは、Ｃｕによる熱間圧延時の表面欠陥発生を抑制するのに有効な元素である。Ｎｉの添加は必ずしも必須ではないが、本発明では０．２質量％を超えて添加しても、その効果は飽和するととともに製造コストの増加を招く。
<One or more selected from the group consisting of Cu: 0.03% by mass to 0.2% by mass and Ni: 0% by mass to 0.2% by mass>
Cu dissolves in steel and precipitates as CuS, but it is relatively coarse compared to other sulfides such as MnS and TiS, so it is difficult to obstruct the domain wall movement, and the magnetic flux density on the low magnetic field side is low. It is effective for improvement. In order to obtain this effect, it is necessary to add at least 0.03% by mass or more.
However, even if added over 0.2% by mass, the effect is saturated and the manufacturing cost is increased. On the other hand, when Cu is added alone, surface defects such as ear cracks are likely to occur during hot rolling. Ni is an element effective for suppressing the occurrence of surface defects during hot rolling with Cu. The addition of Ni is not necessarily essential, but even if added in excess of 0.2% by mass in the present invention, the effect is saturated and the manufacturing cost is increased.
＜絶縁皮膜の形成＞
本発明では、高速回転域でより優れた効率を図る場合には、渦電流損の低減を目的として、鋼板の少なくとも片方の表面に、有機材料からなる絶縁皮膜、無機材料からなる絶縁皮膜及び有機・無機複合材料からなる絶縁皮膜を形成することが好ましい。
<Formation of insulation film>
In the present invention, when aiming at higher efficiency in a high-speed rotation region, for the purpose of reducing eddy current loss, an insulating film made of an organic material, an insulating film made of an inorganic material, and an organic material are formed on at least one surface of the steel plate. -It is preferable to form an insulating film made of an inorganic composite material.
次に、本発明のリラクタンスモータの鉄心用鋼板の製造方法について説明する。
本発明によるリラクタンスモータの鉄心用鋼板の製造方法は、前述の成分組成を有するスラブを連続鋳造し、１１００℃以上の温度に加熱した加熱炉に挿入して加熱後、８００℃以上の温度で仕上圧延を行い、７００℃以下の温度で巻取って熱間圧延コイルとした後、酸洗によりスケールを除去し、１回または中間焼鈍を含む２回以上の冷間圧延にて板厚：０．１〜０．５ｍｍの冷延鋼板とし、７００〜９００℃の温度まで加熱して再結晶焼鈍を施し、必要に応じて、得られた冷延鋼板に伸び率：０．５％以下の条件で、テンションレベラーおよび／またはスキンパス圧延を施すことを特徴とする。また、必要に応じて得られた冷延鋼板の少なくとも片方の表面に、有機材料からなる絶縁皮膜、無機材料からなる絶縁皮膜又は有機・無機複合材料からなる絶縁皮膜を形成することをも特徴とする。
Next, the manufacturing method of the steel sheet for iron cores of the reluctance motor of this invention is demonstrated.
The method for manufacturing a steel sheet for an iron core of a reluctance motor according to the present invention is a method of continuously casting a slab having the above-described composition, inserting it into a heating furnace heated to a temperature of 1100 ° C. or higher, and heating it to a temperature of 800 ° C. or higher. After rolling and winding at a temperature of 700 ° C. or less to form a hot rolling coil, the scale is removed by pickling, and the sheet thickness is set to 0. 1 or 2 cold rollings including intermediate annealing. A cold-rolled steel sheet of 1 to 0.5 mm is heated to a temperature of 700 to 900 ° C. and subjected to recrystallization annealing. If necessary, the resulting cold-rolled steel sheet has an elongation of 0.5% or less. , Tension leveler and / or skin pass rolling. Further, it is also characterized in that an insulating film made of an organic material, an insulating film made of an inorganic material, or an insulating film made of an organic / inorganic composite material is formed on at least one surface of a cold-rolled steel sheet obtained as necessary. To do.
＜熱間圧延／加熱温度：１１００℃以上、仕上圧延温度：８００℃以上、巻取温度：５５０〜７００℃＞
熱間圧延における加熱温度は、１１００℃以上でないと８００℃以上の仕上圧延温度の確保が困難である。仕上圧延温度は、低くなりすぎると変形抵抗が大きくなり、製造性が劣化する。８００℃までは許容できるため、本発明では８００℃以上に限定する。また、巻取温度はＴｉ、Ｎｂ、Ｖを添加した場合には析出物の粗大化を図るため、できるだけ高温とすることが好ましいが、高くなりすぎるとスケール厚さが増大し、製造性が劣化する。析出物の粗大化およびスケール厚さの観点から、巻取温度は５５０℃〜７００℃とすることが好ましい。
<Hot rolling / heating temperature: 1100 ° C. or higher, finish rolling temperature: 800 ° C. or higher, winding temperature: 550 to 700 ° C.>
If the heating temperature in hot rolling is not 1100 ° C. or higher, it is difficult to ensure a finish rolling temperature of 800 ° C. or higher. If the finish rolling temperature is too low, the deformation resistance increases and the manufacturability deteriorates. Since it can tolerate up to 800 ° C., it is limited to 800 ° C. or higher in the present invention. In addition, when Ti, Nb, and V are added, the coiling temperature is preferably as high as possible in order to coarsen the precipitates. However, if it is too high, the scale thickness increases and the productivity deteriorates. To do. From the viewpoint of coarsening of precipitates and scale thickness, the winding temperature is preferably 550 ° C to 700 ° C.
＜冷間圧延、冷間圧延後の板厚：０．１〜０．５ｍｍ＞
冷間圧延条件は、特に規定する必要は無く、通常の方法に従い実施すればよい。また、冷間圧延後の板厚は、渦電流損の低減の観点からはできるだけ薄くすることが好ましく、上限を０．５ｍｍとする。しかし、０．１ｍｍを超えて薄くすると生産性が大幅に劣化する。したがって、板圧の下限は、０．１ｍｍとする。
なお、ロータおよびステータ鉄心は打抜き加工により製造されることが一般的であるが、打抜き加工性の観点からは、冷間圧延ままで降伏比が高く、硬質な方が打抜き端面のダレやバリの発生が抑制でき有利である。したがって、鋼帯の製造工程では最終焼鈍を施さずに冷間圧延ままの状態で絶縁皮膜を塗布し、ロータまたはステータ形状に打抜き加工後に再結晶焼鈍を施すことが打抜き性の観点からより好ましい。また、こうすることで打抜きに歪による低磁場側での磁気特性の劣化も防止することが可能となる。
<Cold rolling, thickness after cold rolling: 0.1 to 0.5 mm>
The cold rolling conditions do not need to be specified in particular, and may be performed according to a normal method. The sheet thickness after cold rolling is preferably as thin as possible from the viewpoint of reducing eddy current loss, and the upper limit is set to 0.5 mm. However, if the thickness exceeds 0.1 mm, the productivity is greatly deteriorated. Therefore, the lower limit of the plate pressure is 0.1 mm.
In general, the rotor and stator core are manufactured by punching. However, from the viewpoint of punching workability, the yield ratio is high as it is cold-rolled, and the harder one is more prone to sag and burrs on the punched end face. The generation can be advantageously suppressed. Therefore, in the steel strip manufacturing process, it is more preferable from the viewpoint of punchability to apply the insulating film in the state of cold rolling without performing the final annealing and to perform the recrystallization annealing after the punching process into the rotor or stator shape. In addition, by doing so, it is possible to prevent the deterioration of magnetic characteristics on the low magnetic field side due to punching distortion.
＜焼鈍加熱温度：７００〜９００℃＞
低磁場側での磁束密度を確保するためには、フェライトを完全に再結晶させる必要がある。このため、７００℃以上の加熱が必要である。しかし、９００℃を超える温度まで加熱すると製造コストが増大するため、本発明では、上限を９００℃とする。なお、焼鈍はバッチ焼鈍、連続焼鈍のいずれでも構わないが、生産性やコストの観点から連続焼鈍を施す場合、加熱温度の下限温度は、８００℃以上とすることが好ましい。
<Annealing heating temperature: 700 to 900 ° C.>
In order to secure the magnetic flux density on the low magnetic field side, it is necessary to completely recrystallize the ferrite. For this reason, heating at 700 ° C. or higher is necessary. However, since the manufacturing cost increases when heated to a temperature exceeding 900 ° C., the upper limit is set to 900 ° C. in the present invention. In addition, although annealing may be either batch annealing or continuous annealing, the lower limit temperature of the heating temperature is preferably set to 800 ° C. or higher when continuous annealing is performed from the viewpoint of productivity and cost.
＜伸び率：０．５％以下のテンションレベラーおよび／またはスキンパス圧延＞
リラクタンスモータのロータおよびステータは、鋼板を積層して形成されるため、素材となる鋼板には良好な板形状であることが要求され、良好な板形状を確保するためには、テンションレベラーやスキンパス圧延が有効である。一方、テンションレベラーやスキンパス圧延等による形状修正では、僅かながら鋼中に格子欠陥が導入され、低磁場側での磁束密度には有害となる。したがって、連続焼鈍における張力制御等のみで良好な板形状を得ることが好ましいが、テンションレベラーやスキンパス圧延を付与する場合、伸び率が０．５％までは許容できるため、伸び率の上限は０．５％とする。
<Elongation: 0.5% or less tension leveler and / or skin pass rolling>
Since the rotor and stator of a reluctance motor are formed by laminating steel plates, the steel plate used as the material is required to have a good plate shape. To ensure a good plate shape, a tension leveler or skin path is required. Rolling is effective. On the other hand, in the shape correction by tension leveler, skin pass rolling or the like, lattice defects are slightly introduced in the steel, which is harmful to the magnetic flux density on the low magnetic field side. Therefore, it is preferable to obtain a good plate shape only by tension control or the like in continuous annealing. However, when a tension leveler or skin pass rolling is applied, the elongation is allowed up to 0.5%, so the upper limit of elongation is 0. .5%.
＜絶縁皮膜の形成＞
本発明では、渦電流損の低減を目的として、鋼板の少なくとも片方の表面に、有機材料からなる絶縁皮膜、無機材料からなる絶縁皮膜及び有機・無機複合材料からなる絶縁皮膜を形成することが好ましい。無機材料からなる絶縁皮膜の例としては、六価クロムのような有害物質を含まず、リン酸二水素アルミニウムを含有する無機質系水溶液が挙げられるが、良好な絶縁が得られれば、有機材料からなる絶縁皮膜又は有機・無機複合材料からなる絶縁皮膜を用いてもよい。絶縁被膜は、上記で例示した材料を鋼板の表面に塗布することにより形成することができる。
<Formation of insulation film>
In the present invention, for the purpose of reducing eddy current loss, it is preferable to form an insulating film made of an organic material, an insulating film made of an inorganic material, and an insulating film made of an organic / inorganic composite material on at least one surface of the steel sheet. . Examples of the insulating film made of an inorganic material include an inorganic aqueous solution that does not contain a harmful substance such as hexavalent chromium and contains aluminum dihydrogen phosphate. An insulating film made of an organic / inorganic composite material may be used. The insulating coating can be formed by applying the material exemplified above to the surface of the steel plate.
＜実施例１＞
表１に示す化学組成を有する鋼を真空溶解し、これらの鋳片を１２５０℃に加熱し、９５０℃で仕上圧延して５６０℃で巻取り、板厚１．６ｍｍの熱間圧延鋼板を得た。これらの熱間圧延鋼板を酸洗後、1回の冷間圧延にて０．２ｍｍ厚まで圧延を施し、連続焼鈍ラインにて８５０℃で６０ｓ均熱する熱サイクルにて再結晶焼鈍を施した。なお、連続焼鈍における冷却はガスジェット冷却とし、ライン内の張力を制御して良好な板形状が得られるように通板した。その後、連続塗装ラインに通板して、Ｃｒ系酸化物およびＭｇ酸化物を含有する半有機組成の約１μｍ厚さの絶縁皮膜を鋼板の両面に形成した。
<Example 1>
Steel having the chemical composition shown in Table 1 is melted in vacuum, these slabs are heated to 1250 ° C., finish-rolled at 950 ° C. and wound at 560 ° C. to obtain a hot-rolled steel plate having a thickness of 1.6 mm. It was. After pickling these hot-rolled steel sheets, rolling was performed to a thickness of 0.2 mm by one cold rolling, and recrystallization annealing was performed in a thermal cycle that was soaked at 850 ° C. for 60 s in a continuous annealing line. . The cooling in the continuous annealing was gas jet cooling, and the plate was passed so as to obtain a good plate shape by controlling the tension in the line. Thereafter, the sheet was passed through a continuous coating line, and an insulating film having a semi-organic composition containing Cr-based oxide and Mg oxide and having a thickness of about 1 μm was formed on both surfaces of the steel sheet.
得られた鋼帯からＪＩＳ５号試験片を切り出し、引張試験に供した。また、圧延方向および圧延方向と直角方向から、幅：１０ｍｍ、長さ：１００ｍｍの短冊状の試験片を各１０枚づつ打抜き加工により採取し、ＪＩＳ Ｃ ２５５０に規定されたエプスタイン試験枠を小型に設計した小型のエプスタイン試験枠を用い、直流磁化測定に供した。各サンプルの降伏強さ、引張強さ、降伏比（ＹＲ）を求めた他、磁化測定では、消磁後の初磁化曲線を測定し、初磁化曲線において、磁界の強さが５００Ａ／ｍのときの磁束密度（Ｂ５００）と５０００Ａ／ｍのときの磁束密度（Ｂ５０００）を測定し、それぞれ表２に示した。 A JIS No. 5 test piece was cut out from the obtained steel strip and subjected to a tensile test. In addition, a strip-shaped test piece having a width of 10 mm and a length of 100 mm was sampled by punching from the rolling direction and a direction perpendicular to the rolling direction, and the Epstein test frame specified in JIS C 2550 was made compact. The designed small Epstein test frame was used for DC magnetization measurement. In addition to obtaining the yield strength, tensile strength, and yield ratio (YR) of each sample, in the magnetization measurement, the initial magnetization curve after demagnetization is measured, and when the magnetic field strength is 500 A / m in the initial magnetization curve The magnetic flux density (B 500 ) and the magnetic flux density (B 5000 ) at 5000 A / m were measured and shown in Table 2, respectively.
表２からわかるように、Ｃ，Ｓ，Ａｌ，Ｎ，Ｏ等の不純物元素が本発明範囲を超えるＮｏ．５、Ｎｏ．１０〜１３鋼およびＴｉやＮｂが本発明範囲を超えて添加されたＮｏ．２０、２１、２２鋼では、析出物、介在物の影響により、結晶粒径の微細化も相まって磁界の強さが５００Ａ／ｍのときの磁束密度Ｂ５００の値が１．００Ｔよりも低くなることがわかる。また、ＳｉやＭｎが本発明範囲を超えるＮｏ．８、９、２２鋼では、磁界の強さが５０００Ａ／ｍのときの磁束密度Ｂ５０００が、１．７０Ｔよりも低くなる。一方、本発明範囲の化学成分を有する鋼では、低磁場から高磁場までの広い範囲で良好な磁束密度を示す。 As can be seen from Table 2, no. 5, no. No. 10-13 steel and Ti and Nb added beyond the scope of the present invention. In Steel Nos. 20, 21, and 22, due to the influence of precipitates and inclusions, the magnetic flux density B 500 is lower than 1.00 T when the magnetic field strength is 500 A / m, coupled with the refinement of the crystal grain size. I understand that. Moreover, Si and Mn are No. exceeding the scope of the present invention. The 8,9,22 steel, the strength of the magnetic field flux density B 5000 in the case of 5000A / m, lower than 1.70T. On the other hand, steel having chemical components in the range of the present invention exhibits good magnetic flux density in a wide range from a low magnetic field to a high magnetic field.
＜実施例２＞
表１に示す化学組成を有する鋼の中で、鋼Ｎｏ．３およびＮｏ．１５の鋳片を１１５０℃に加熱し、８１０℃で仕上圧延して５００℃、６００℃、７００℃と巻取温度を３水準変化させ、板厚２．３ｍｍの熱間圧延鋼帯を得た。得られた熱間圧延鋼帯を酸洗後、一旦０．６ｍｍまで冷間圧延を行い、８００℃で６０ｓ均熱処理する中間焼鈍を施し、更に０．５ｍｍ厚まで圧延を施した後、６５０℃、７５０℃および８５０℃で６０ｓ均熱する連続焼鈍を施した。なお、連続焼鈍における冷却はガスジェット冷却とし、ライン内の張力を制御して良好な板形状が得られるように通板した。その後、連続塗装ラインに通板して、Ｃｒ系酸化物およびＭｇ酸化物を含有する半有機組成の約１μｍ厚さの絶縁皮膜を鋼板の両面に形成した。
<Example 2>
Among the steels having the chemical composition shown in Table 1, steel no. 3 and no. 15 slabs were heated to 1150 ° C. and finish-rolled at 810 ° C., and the coiling temperature was changed to three levels of 500 ° C., 600 ° C. and 700 ° C. to obtain a hot-rolled steel strip having a plate thickness of 2.3 mm . After pickling the obtained hot-rolled steel strip, it is once cold-rolled to 0.6 mm, subjected to an intermediate annealing that is soaked at 800 ° C. for 60 s, further rolled to a thickness of 0.5 mm, and then 650 ° C. Continuous annealing was performed at 750 ° C. and 850 ° C. for 60 s. The cooling in the continuous annealing was gas jet cooling, and the plate was passed so as to obtain a good plate shape by controlling the tension in the line. Thereafter, the sheet was passed through a continuous coating line, and an insulating film having a semi-organic composition containing Cr-based oxide and Mg oxide and having a thickness of about 1 μm was formed on both surfaces of the steel sheet.
得られた鋼帯からＪＩＳ５号試験片を切り出し、引張試験に供した。また、圧延方向および圧延方向と直角方向から、幅：１０ｍｍ、長さ：１００ｍｍの短冊状の試験片を各１０枚づつ打抜き加工により採取し、ＪＩＳ Ｃ ２５５０に規定されたエプスタイン試験枠を小型に設計した小型のエプスタイン試験枠（１次巻線：２４０ターン、２次巻線：４００ターン）を用いて直流磁化測定に供した。各サンプルの降伏強さ、引張強さ、降伏比（ＹＲ）を求めた他、磁化測定では、消磁後の初磁化曲線を測定し、初磁化曲線において、磁界の強さが５００Ａ／ｍのときの磁束密度（Ｂ５００）と５０００Ａ／ｍのときの磁束密度（Ｂ５０００）を測定し、それぞれ表３に示した。 A JIS No. 5 test piece was cut out from the obtained steel strip and subjected to a tensile test. In addition, a strip-shaped test piece having a width of 10 mm and a length of 100 mm was sampled by punching from the rolling direction and a direction perpendicular to the rolling direction, and the Epstein test frame specified in JIS C 2550 was made compact. The designed small Epstein test frame (primary winding: 240 turns, secondary winding: 400 turns) was used for DC magnetization measurement. In addition to obtaining the yield strength, tensile strength, and yield ratio (YR) of each sample, in the magnetization measurement, the initial magnetization curve after demagnetization is measured, and when the magnetic field strength is 500 A / m in the initial magnetization curve The magnetic flux density (B 500 ) and the magnetic flux density (B 5000 ) at 5000 A / m were measured and are shown in Table 3, respectively.
表３からわかるように、焼鈍温度が６５０℃の比較例では、再結晶が不十分で結晶粒径が小さい上、未再結晶組織となるため、磁界の強さが１００Ａ／ｍのときの磁束密度Ｂ500の値が１．０Ｔよりも低くなることがわかる。また、熱間圧延における巻取温度が５００℃の場合、Ｔｉ添加のＮｏ．１５鋼においては、微細なＴｉＣの析出に起因して、磁界の強さが１００Ａ／ｍのときの磁束密度Ｂ５００が、１．００Ｔよりも低くなる。一方、本発明範囲の熱間圧延条件および焼鈍温度で製造すると、低磁場から高磁場までの広い範囲で良好な磁束密度を示すことがわかる。 As can be seen from Table 3, in the comparative example where the annealing temperature is 650 ° C., recrystallization is insufficient, the crystal grain size is small, and an unrecrystallized structure is formed. Therefore, the magnetic flux when the magnetic field strength is 100 A / m. It can be seen that the value of the density B500 is lower than 1.0T. Further, when the coiling temperature in hot rolling is 500 ° C., the Ti addition No. In Steel No. 15, due to the precipitation of fine TiC, the magnetic flux density B 500 when the magnetic field strength is 100 A / m is lower than 1.00 T. On the other hand, when manufactured under the hot rolling conditions and annealing temperature within the range of the present invention, it can be seen that a good magnetic flux density is exhibited in a wide range from a low magnetic field to a high magnetic field.
＜実施例３＞
実施例２で製造したＮｏ．３鋼の６００℃巻取、８５０℃焼鈍した鋼帯について、オフラインにて伸び率：０．２％、０．５％および１．０％のスキンパス（ＳＫＰ）圧延を施した。得られた鋼帯からＪＩＳ５号試験片を切り出し、引張試験に供した。また、圧延方向および圧延方向と直角方向から、幅：１０ｍｍ、長さ：１００ｍｍの短冊状の試験片を各１０枚づつ打抜き加工により採取し、ＪＩＳ Ｃ ２５５０に規定されたエプスタイン試験枠を小型に設計した小型のエプスタイン試験枠（１次巻線：２４０ターン、２次巻線：４００ターン）を用いて直流磁化測定に供した。各サンプルの降伏強さ、引張強さ、降伏比（ＹＲ）を求めた他、磁化測定では、消磁後の初磁化曲線を測定し、初磁化曲線において、磁界の強さが１００Ａ／ｍのときの磁束密度（Ｂ５００）と５０００Ａ／ｍのときの磁束密度（Ｂ５０００）を測定し、それぞれ表４に示した。
<Example 3>
No. manufactured in Example 2 Three steel strips rolled up at 600 ° C. and annealed at 850 ° C. were subjected to skin pass (SKP) rolling with an elongation of 0.2%, 0.5%, and 1.0% offline. A JIS No. 5 test piece was cut out from the obtained steel strip and subjected to a tensile test. In addition, a strip-shaped test piece having a width of 10 mm and a length of 100 mm was sampled by punching from the rolling direction and a direction perpendicular to the rolling direction, and the Epstein test frame specified in JIS C 2550 was made compact. The designed small Epstein test frame (primary winding: 240 turns, secondary winding: 400 turns) was used for DC magnetization measurement. In addition to obtaining the yield strength, tensile strength, and yield ratio (YR) of each sample, in the magnetization measurement, the initial magnetization curve after demagnetization is measured, and when the magnetic field strength is 100 A / m in the initial magnetization curve The magnetic flux density (B 500 ) and the magnetic flux density (B 5000 ) at 5000 A / m were measured and are shown in Table 4, respectively.
表４からわかるように、スキンパスにおける伸び率が０．５％を超えると、磁界の強さが５００Ａ／ｍのときの磁束密度Ｂ５００の値が１．００Ｔよりも低くなるが、スキンパスにおける伸び率が０．５％以下の場合、低磁場から高磁場までの広い範囲で良好な磁束密度を示すことがわかる。 As can be seen from Table 4, when the elongation rate in the skin pass exceeds 0.5%, the value of the magnetic flux density B 500 when the magnetic field strength is 500 A / m is lower than 1.00 T. It can be seen that when the rate is 0.5% or less, a good magnetic flux density is exhibited in a wide range from a low magnetic field to a high magnetic field.
＜実施例４＞
実施例１で製造した鋼Ｎｏ．３鋼、Ｎｏ．８鋼およびＮｏ.２２鋼の冷延鋼板および市販の無方向性電磁鋼板（３５Ａ３００）をロータおよびステータ鉄心の素材として、図１の模式図に示す固定子１２極、回転子８極のＳＲモータを試作し、モータ性能評価を行った。なお、試作したＳＲモータは、鉄心の積高さ：４０ｍｍ、ステータ外径：１３６ｍｍ、ロータ外径：８３．２ｍｍ、ギャップは０．２ｍｍとした。なお、固定子の鉄心には市販の無方向性電磁鋼板（３５Ａ３００）を使用した。直流電源からインバータを介して試作したモータを回転させ、２０００ｒｐｍ、３０００ｒｐｍおよび４０００ｒｐｍの時の最大トルクを測定し、モータの性能評価とした。評価結果を表６に示す。
<Example 4>
Steel No. manufactured in Example 1 3 steel, no. SR motor with 12 poles of stator and 8 poles of rotor shown in the schematic diagram of FIG. 1, using cold rolled steel sheet of No. 8 steel and No. 22 steel and commercially available non-oriented electrical steel sheet (35A300) as material of rotor and stator core Was prototyped and the motor performance was evaluated. The prototype SR motor had an iron core stack height of 40 mm, a stator outer diameter of 136 mm, a rotor outer diameter of 83.2 mm, and a gap of 0.2 mm. A commercially available non-oriented electrical steel sheet (35A300) was used for the iron core of the stator. A prototype motor was rotated from a DC power source via an inverter, and the maximum torque at 2000 rpm, 3000 rpm, and 4000 rpm was measured to evaluate the performance of the motor. The evaluation results are shown in Table 6.
表５からわかるように、本発明範囲の高い磁束密度を有するＮｏ．３の鋼板をロータおよび／またはステータの鉄心材に適用したモータでは、比較のＮｏ．８鋼、Ｎｏ．２２鋼をロータ、ステータのいずれかまたは両方に適用した場合と比べ、高トルク（出力）が得られている他、ロータおよびステータの鉄心材に市販の電磁鋼板（３５Ａ３００）を適用した場合と比べても、高トルク（出力）が得られることがわかる。 As can be seen from Table 5, No. 1 having a high magnetic flux density within the range of the present invention. No. 3 was applied to the motor in which the steel plate of No. 3 was applied to the rotor and / or stator core. No. 8 steel, no. Compared to the case where 22 steel is applied to either or both of the rotor and the stator, high torque (output) is obtained, and compared to the case where a commercially available electrical steel sheet (35A300) is applied to the core material of the rotor and stator. However, it can be seen that high torque (output) can be obtained.
１ 固定子
２ 回転子
1
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