JP5919859B2 - Oriented electrical steel sheet and manufacturing method thereof - Google Patents
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- 238000004519 manufacturing process Methods 0.000 title claims description 15
- 229910000976 Electrical steel Inorganic materials 0.000 title claims description 6
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 89
- 229910052742 iron Inorganic materials 0.000 claims description 41
- 229910000831 Steel Inorganic materials 0.000 claims description 38
- 239000010959 steel Substances 0.000 claims description 38
- 238000010894 electron beam technology Methods 0.000 claims description 28
- 229910001224 Grain-oriented electrical steel Inorganic materials 0.000 claims description 27
- 238000000576 coating method Methods 0.000 claims description 15
- 239000011248 coating agent Substances 0.000 claims description 14
- 238000005096 rolling process Methods 0.000 claims description 13
- 230000001133 acceleration Effects 0.000 claims description 12
- 239000000161 steel melt Substances 0.000 claims description 2
- 230000004907 flux Effects 0.000 description 27
- 230000000694 effects Effects 0.000 description 14
- 230000005381 magnetic domain Effects 0.000 description 13
- 230000008018 melting Effects 0.000 description 13
- 238000002844 melting Methods 0.000 description 13
- 238000000034 method Methods 0.000 description 12
- 230000006866 deterioration Effects 0.000 description 7
- 239000013078 crystal Substances 0.000 description 6
- 230000009467 reduction Effects 0.000 description 6
- 229910052839 forsterite Inorganic materials 0.000 description 5
- 238000013467 fragmentation Methods 0.000 description 5
- 238000006062 fragmentation reaction Methods 0.000 description 5
- 230000006872 improvement Effects 0.000 description 5
- HCWCAKKEBCNQJP-UHFFFAOYSA-N magnesium orthosilicate Chemical compound [Mg+2].[Mg+2].[O-][Si]([O-])([O-])[O-] HCWCAKKEBCNQJP-UHFFFAOYSA-N 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- 239000000155 melt Substances 0.000 description 5
- 230000015572 biosynthetic process Effects 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 239000002344 surface layer Substances 0.000 description 4
- 230000008859 change Effects 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 230000001678 irradiating effect Effects 0.000 description 3
- 238000005259 measurement Methods 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 229910052787 antimony Inorganic materials 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 229910052802 copper Inorganic materials 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 230000004927 fusion Effects 0.000 description 2
- 238000011835 investigation Methods 0.000 description 2
- 229910052750 molybdenum Inorganic materials 0.000 description 2
- 229910052698 phosphorus Inorganic materials 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- 229910052718 tin Inorganic materials 0.000 description 2
- 229910019142 PO4 Inorganic materials 0.000 description 1
- NJFMNPFATSYWHB-UHFFFAOYSA-N ac1l9hgr Chemical compound [Fe].[Fe] NJFMNPFATSYWHB-UHFFFAOYSA-N 0.000 description 1
- 238000009825 accumulation Methods 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 238000004453 electron probe microanalysis Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 230000035515 penetration Effects 0.000 description 1
- 230000035699 permeability Effects 0.000 description 1
- NBIIXXVUZAFLBC-UHFFFAOYSA-K phosphate Chemical compound [O-]P([O-])([O-])=O NBIIXXVUZAFLBC-UHFFFAOYSA-K 0.000 description 1
- 239000010452 phosphate Substances 0.000 description 1
- 230000021715 photosynthesis, light harvesting Effects 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000004804 winding Methods 0.000 description 1
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- Manufacturing Of Steel Electrode Plates (AREA)
Description
本発明は、変圧器の鉄心などの用途に使用される方向性電磁鋼板およびその製造方法に関し、特に熱歪み導入型の磁区細分化に際し、磁束密度の劣化を招くことなしに、鉄損特性の有利な向上を図ろうとするものである。 The present invention relates to a grain-oriented electrical steel sheet used for applications such as transformer iron cores and a method for producing the grain-oriented electrical steel sheet. It is intended to make an advantageous improvement.
変圧器などに使用される方向性電磁鋼板には、高磁束密度を始めとして、低鉄損、高透磁率、低騒音など、多岐にわたる特性が求められる。特に、低鉄損化と高磁束密度化が従来から追求され続けてきた。 Directional electrical steel sheets used for transformers and the like are required to have various characteristics such as high magnetic flux density, low iron loss, high magnetic permeability, and low noise. In particular, low iron loss and high magnetic flux density have been continuously pursued.
方向性電磁鋼板の鉄損を低減する方法としては、これまで素材の組織や化学組成の調整の他に、鋼板への線状溝の形成、レーザ、プラズマ炎、電子ビームの照射などによる磁区細分化が知られている（例えば特許文献１など）。
上記した方法のうち、線状溝の形成は、鉄損の改善効果が大きいことが知られているが、磁束密度を劣化させるという欠点がある。
一方、レーザやプラズマ炎、電子ビーム照射による磁区細分化は、鉄損を劇的に改善することができるだけでなく、鋼板の磁束密度はほとんど劣化しないために、高磁束密度と低鉄損が両立できるとされてきた。しかしながら、磁区細分化処理前の鋼板の改善による磁束密度の向上効果が飽和傾向を示し、0.005Ｔの磁束密度向上が非常に大きな技術的進歩と考えられる中、熱歪み導入型の磁区細分化によってわずかに減少する鋼板の磁束密度を如何に抑制するかが重要な問題になっている。
In order to reduce the iron loss of grain-oriented electrical steel sheets, in addition to adjusting the structure and chemical composition of the material, magnetic domain subdivision by forming linear grooves on the steel sheet, laser, plasma flame, electron beam irradiation, etc. (For example, Patent Document 1).
Among the methods described above, the formation of the linear groove is known to have a large effect of improving the iron loss, but has a drawback of deteriorating the magnetic flux density.
On the other hand, magnetic domain fragmentation by laser, plasma flame, or electron beam irradiation can not only dramatically improve iron loss, but also the magnetic flux density of the steel plate hardly deteriorates, so both high magnetic flux density and low iron loss are compatible. It was supposed to be possible. However, the improvement effect of the magnetic flux density by the improvement of the steel plate before the magnetic domain subdivision treatment shows a saturation tendency, and the improvement of the magnetic flux density of 0.005T is considered to be a very big technological advance. An important issue is how to suppress the magnetic flux density of the steel sheet, which decreases slightly.
方向性電磁鋼板を高磁束密度化させる技術については、従来から多くの検討がなされており、電磁鋼板の結晶方位をGoss方位へ集積させることによって向上させることができるとされる。例えば特許文献２には、1.97Ｔを超える磁束密度Ｂ8を有する方向性電磁鋼板の製造方法が示されている。 Many studies have been made on techniques for increasing the magnetic flux density of grain-oriented electrical steel sheets, and it can be improved by accumulating the crystal orientation of the electrical steel sheets in the Goss orientation. For example, Patent Document 2 discloses a method for producing a grain-oriented electrical steel sheet having a magnetic flux density B 8 exceeding 1.97T.
一方、磁区細分化処理を施した鋼板の磁束密度の向上化に関しては、例えば特許文献３に示されるように溝形成法については数多くなされているものの、レーザや電子ビームなどを照射する熱歪み導入法については、ほとんどなされて来なかった。 On the other hand, regarding the improvement of the magnetic flux density of the steel plate subjected to the magnetic domain subdivision treatment, for example, as shown in Patent Document 3, although there are many groove forming methods, introduction of thermal strain that irradiates a laser or an electron beam is introduced. Little has been done about the law.
熱歪み導入法は、溝歪み導入法に比較して、地鉄の体積減少がないことから、導入前後における磁束密度の減少量が非常に小さい。しかしながら、熱歪み導入型においても、適切な条件を整えない場合には、磁束密度が大きく減少する。例えば、発明者らの実験では、圧延方向のＢ8が1.935Ｔの鋼板に、14.4mJのエネルギを、圧延直角方向に0.3mm間隔で、かつ圧延方向に５mm間隔で電子ビームにより照射した場合、鋼板の地鉄体積減少は認められなかったものの、照射後のＢ8は0.032Ｔ減少した。 Since the thermal strain introduction method does not reduce the volume of the ground iron compared to the groove strain introduction method, the amount of decrease in the magnetic flux density before and after the introduction is very small. However, even in the thermal strain introduction type, the magnetic flux density is greatly reduced if appropriate conditions are not prepared. For example, in our experiments, when the rolling direction B 8 are the steel 1.935T, the energy of 14.4MJ, at 0.3mm intervals in the direction perpendicular to the rolling direction, and was irradiated by electron beam at 5mm intervals in the rolling direction, Although no reduction in the volume of steel in the steel sheet was observed, B 8 after irradiation decreased by 0.032 T.
この問題に対し、発明者らは種々検討を重ねた結果、熱歪み導入法による磁束密度の変化は、熱導入時における、地鉄の結晶方位の変化によるものであると考えられた。
すなわち、鋼板に局所的に大きな熱を加えた場合、急激に加熱された照射部が塑性変形あるいは弾性的な結晶回転を起こして、結晶方位が変化することがＢ8の劣化要因の一つであると考えた。特に、照射部により多くの熱が蓄積した場合には、照射部が溶融し、再凝固時に元の結晶方位からずれた結晶方位になると考え、熱照射による照射部の地鉄溶融を抑制することができれば、磁束密度の劣化を抑制できるのではないかとの結論を得るに至った。
As a result of various studies by the inventors, it was considered that the change in magnetic flux density by the thermal strain introduction method was due to the change in the crystal orientation of the ground iron at the time of heat introduction.
That is, when a large amount of heat is locally applied to the steel sheet, one of the deterioration factors of B 8 is that the irradiated portion that is heated rapidly undergoes plastic deformation or elastic crystal rotation, and the crystal orientation changes. I thought it was. In particular, when a lot of heat accumulates in the irradiated area, the irradiated area melts and becomes a crystal orientation that deviates from the original crystal orientation during re-solidification. If it was possible, it came to the conclusion that deterioration of magnetic flux density could be suppressed.
従来技術（例えば、特許文献４）では、被膜損傷のない方向性電磁鋼板の製造方法が多く提案されている。被膜の損傷がなければ、地鉄溶融もないと考えられるが、このような従来技術では、ビームのエネルギ密度を低減する必要があるため、高エネルギ密度照射に比較して、トランス鉄損に大きな影響を及ぼすヒステリシス損と渦電流損の構成比を変化させたり、また処理能力を低下させてしまう傾向がある。さらに、被膜密着性などの被膜性状が異なれば、当然、損傷しないビーム照射条件は異なることから、このような照射技術は、製造安定性の観点からすると好ましくない。 In the prior art (for example, Patent Document 4), many methods for producing a grain-oriented electrical steel sheet without film damage have been proposed. If there is no damage to the coating, it is considered that there is no melting of the iron core. However, in such a conventional technique, it is necessary to reduce the energy density of the beam. There is a tendency to change the composition ratio of the hysteresis loss and the eddy current loss which influences, and to reduce the processing capability. Furthermore, if the film properties such as film adhesion are different, naturally, the beam irradiation conditions that do not damage are different, so such irradiation technique is not preferable from the viewpoint of manufacturing stability.
また、特許文献５などには、被膜損傷がある場合には、被膜が蒸発するときに鋼板に反力を及ぼし、磁区細分化に有利な応力を形成させるとも報告されている。 Further, Patent Document 5 and the like also report that when there is a film damage, a reaction force is exerted on the steel sheet when the film evaporates, and a stress advantageous for magnetic domain subdivision is formed.
上記のような理由から、被膜損傷を有する熱歪み導入型の方向性電磁鋼板の製造必要性は高い。本発明は、このような被膜損傷を有する熱歪み導入型方向性電磁鋼板のＢ8を高くすることについて検討したものである。
従来技術による方法によれば、レーザなどを鋼板表面上に照射すると、被膜が高温化し、さらに損傷するため、地鉄が表面にむき出しになる。すると、引続いて地鉄がさらに高温化するため、溶融してしまう。このような溶融を抑制するには、例えばビーム出力を低減すれば良いのであるが、この場合は十分な磁区細分化に必要な熱歪みが形成されず、鉄損低減効果が減少してしまう。
For the reasons described above, there is a high need for manufacturing a heat strain-introducing directional electrical steel sheet having film damage. The present invention investigates increasing B 8 of a heat strain-introducing directional electrical steel sheet having such film damage.
According to the method according to the prior art, when the surface of the steel plate is irradiated with a laser or the like, the coating film is heated and further damaged, so that the ground iron is exposed on the surface. Then, since the base iron is further heated to a higher temperature, it melts. In order to suppress such melting, for example, the beam output may be reduced, but in this case, the thermal strain necessary for sufficient magnetic domain fragmentation is not formed, and the iron loss reduction effect is reduced.
本発明は、上記の問題を有利に解決するもので、被膜損傷を伴う電子ビーム照射を行った場合に、十分な磁区細分化を達成されて満足のいく鉄損低減効果が得られるのは言うまでもなく、かような電子ビーム照射に伴う磁束密度の劣化が極めて小さい方向性電磁鋼板を、その有利な製造方法と共に提案することを目的とする。 The present invention advantageously solves the above problems, and it goes without saying that sufficient magnetic domain fragmentation is achieved and satisfactory iron loss reduction effects are obtained when electron beam irradiation with film damage is performed. In addition, an object of the present invention is to propose a grain-oriented electrical steel sheet with extremely small deterioration in magnetic flux density caused by electron beam irradiation, together with its advantageous manufacturing method.
ところで、従来の知見に基づいて、レーザ法と電子ビーム法による磁区細分化を比較すると、磁区細分化に必要な鋼板への総エネルギ照射量は後者の方が多い。
発明者らは、この事実などをヒントに実験を繰返すことによって、電子ビームの場合、照射した鋼板の内部で、表面に比べてより広範囲に広がる熱分布が形成されると推定した。従って、電子ビーム照射の場合は、鋼板内部の局所的な熱の蓄積が抑制されるため、地鉄溶融抑制に有利であると考えた。
By the way, when comparing the magnetic domain subdivision by the laser method and the electron beam method based on the conventional knowledge, the latter has a larger total energy irradiation amount to the steel plate necessary for the magnetic domain subdivision.
The inventors have repeated experiments with this fact as a hint to estimate that, in the case of an electron beam, a heat distribution that is spread over a wider area than the surface is formed inside the irradiated steel sheet. Therefore, in the case of electron beam irradiation, since local heat accumulation inside the steel sheet is suppressed, it was considered that it is advantageous for suppressing the melting of the steel.
さらに、このように、鋼板内部で熱影響部が拡大する理由は、電子ビームが地鉄表層からやや内部に侵入する特性があるためと考え、例えば、K. Kanaya and S. Okayamaらの理論によって計算すると、150kVの加速電圧で入射した電子は、鋼板表面から10μm程度内部でエネルギの散逸が最も大きいことが示された。
そこで、発明者らは、このような電子ビームの特長を最大限活用することを考え、加速電圧Ｖａ(kV)とビーム径ｄ(μm)との関係について、綿密な検討を重ねたところ、これらが所定の関係を満足するように制御することによって、被膜が損傷しても、地鉄の溶融が抑制され、その結果、磁束密度の劣化なしに十分な磁区細分化効果が発現することを見出した。
本発明は、上記の知見に立脚するものである。
Furthermore, the reason why the heat-affected zone expands inside the steel sheet is thought to be due to the property that the electron beam penetrates slightly from the surface layer of the steel. For example, according to the theory of K. Kanaya and S. Okayama et al. Calculations show that the electrons radiated at an acceleration voltage of 150 kV have the largest energy dissipation within about 10 μm from the steel plate surface.
Therefore, the inventors considered the maximum use of such characteristics of the electron beam, and conducted a thorough examination on the relationship between the acceleration voltage Va (kV) and the beam diameter d (μm). Is found to satisfy the predetermined relationship, and even if the coating is damaged, the melting of the ground iron is suppressed, and as a result, a sufficient magnetic domain fragmentation effect is exhibited without deterioration of the magnetic flux density. It was.
The present invention is based on the above findings.
すなわち、本発明の要旨構成は次のとおりである。
１．鋼板の圧延方向を横切る向きに延びる線状の歪を鋼板地鉄内部に有し、かつこの歪み存在領域上の被膜が少なくとも部分的に剥離した方向性電磁鋼板であって、
被膜剥離内部の表面SEM観察による二次電子像において、地鉄溶融痕がなく、鉄損Ｗ 17/50 が0.70W/kg以下であることを特徴とする方向性電磁鋼板。
That is, the gist configuration of the present invention is as follows.
1. It is a grain-oriented electrical steel sheet having a linear strain extending in the direction crossing the rolling direction of the steel sheet inside the steel sheet base iron, and the coating on the strain existing area is at least partially peeled off,
In the secondary electron image by decapsulated inner surface SEM observation, the grain-oriented electrical steel sheet, wherein the base steel melt marks rather name iron loss W 17/50 is not more than 0.70 W / kg.
２．請求項１に記載した方向性電磁鋼板を製造する方法であって、
上記の方向性電磁鋼板を製造するに当たり、加速電圧をＶａ(kV)、ビーム径をｄ(μm)とするとき、これらＶａおよびｄが、次式
ｄ＞0.007×Ｖａ2−2.72×Ｖａ＋474
の関係を満足する条件で電子ビームを照射して線状の歪みを導入することを特徴とする前記１に記載の方向性電磁鋼板の製造方法。
2. A method for producing the grain-oriented electrical steel sheet according to claim 1,
In manufacturing the grain-oriented electrical steel sheet, when the acceleration voltage is Va (kV) and the beam diameter is d (μm), these Va and d are expressed by the following formula: d> 0.007 × Va 2 −2.72 × Va + 474
2. The method for producing a grain-oriented electrical steel sheet according to 1 above, wherein linear distortion is introduced by irradiating an electron beam under a condition that satisfies the above relationship.
本発明に従う条件で電子ビームを照射することによって、照射に伴う磁束密度の劣化を極めて小さくすることができ、その結果、照射後に低鉄損と高磁束密度が両立した方向性電磁鋼板を得ることが可能になる。
従って、本発明の方向性電磁鋼板を、変圧器の鉄心などに使用した場合、従来に比べて変圧器のエネルギ使用効率を大幅に向上させることができ、産業上極めて有用である。
By irradiating the electron beam under the conditions according to the present invention, the deterioration of the magnetic flux density accompanying the irradiation can be made extremely small, and as a result, a grain-oriented electrical steel sheet having both low iron loss and high magnetic flux density after irradiation is obtained. Is possible.
Therefore, when the grain-oriented electrical steel sheet according to the present invention is used for an iron core of a transformer or the like, the energy use efficiency of the transformer can be greatly improved as compared with the conventional one, which is extremely useful industrially.
以下、本発明を具体的に説明する。
［被照射材］
本発明は、地鉄の上に絶縁被膜などがコーティングされている方向性電磁鋼板に適用される。
また、本発明の方向性電磁鋼板は、鋼板の圧延方向を横切る向きに延びる線状の歪を鋼板地鉄内部に有しており、かつこの歪み存在領域上で被膜が部分的に、あるいは全体的に剥離した領域を有する。ここで、被膜が剥離している状態とは、地鉄が表層に露出していることをいい、EPMAなどにより簡単に分析することができる。
Hereinafter, the present invention will be specifically described.
[Material to be irradiated]
The present invention is applied to a grain-oriented electrical steel sheet in which an insulating film or the like is coated on the ground iron.
Further, the grain-oriented electrical steel sheet of the present invention has a linear strain extending in a direction crossing the rolling direction of the steel sheet inside the steel plate, and the coating is partially or entirely on the strain existing area. Having a partially peeled area. Here, the state where the film is peeled means that the ground iron is exposed on the surface layer and can be easily analyzed by EPMA or the like.
さらに、本発明の方向性電磁鋼板は、被膜剥離内部の表面SEM観察による二次電子像において、地鉄溶融痕がないことを特徴とする。ここで、SEM観察条件は、表層被膜形態や地鉄が十分良く観察できるように適宜行えば良いが、本発明においては、加速電圧：５kV、倍率：3000を観察条件とした。
なお、本発明において、地鉄溶融痕があるとは、上記被膜剥離部の地鉄形状が、非被膜剥離部における被膜との界面の地鉄形状と顕著な違いがある場合を指す。すなわち、地鉄の上にフォルステライト被膜を有する方向性電磁鋼板の場合には、被膜との界面の地鉄形状はフォルステライトの構造を反映した凹凸形状になっており、SEMの二次電子像で観察した場合には、エッジ効果によって凹凸を反映した白黒のコントラストが生じ、網の目状のネットワーク構造が観察される。この網の目の間隔は通常５μm未満であるが、地鉄が溶融すれば溶融部の網の目構造は消失し、５μm以上の領域で網の目構造が観察されなくなる。従って、フォルステライト被膜を有する方向性電磁鋼板において、地鉄溶融痕があるとは、SEMの二次電子像において、５μm以上の地鉄露出領域でエッジ効果によって観察される網の目状のネットワーク構造が観察されないことを指すものとする。したがって、本発明では以上に定義した地鉄溶融痕を有しないことを特徴とするものである。
Furthermore, the grain-oriented electrical steel sheet according to the present invention is characterized in that there is no trace of molten iron in the secondary electron image obtained by surface SEM observation inside the film peeling. Here, the SEM observation conditions may be appropriately set so that the surface layer form and the ground iron can be observed sufficiently well. In the present invention, the observation conditions were acceleration voltage: 5 kV and magnification: 3000.
In the present invention, the presence of a ground metal melting mark refers to the case where the shape of the iron strip of the coating film peeling portion is significantly different from the shape of the iron core at the interface with the coating film in the non-coating peeling portion. In other words, in the case of grain-oriented electrical steel sheets having a forsterite coating on the ground iron, the shape of the ground iron at the interface with the coating is uneven, reflecting the structure of the forsterite. In the case of observing with (1), a black and white contrast reflecting the unevenness is generated by the edge effect, and a net-like network structure is observed. The interval between the meshes is usually less than 5 μm. However, if the base iron melts, the mesh structure of the melted portion disappears, and the mesh structure is not observed in the region of 5 μm or more. Therefore, in a grain-oriented electrical steel sheet having a forsterite coating, the presence of a ground iron melt mark is a mesh-like network observed by an edge effect in an exposed area of a ground iron of 5 μm or more in a secondary electron image of SEM. It shall indicate that no structure is observed. Therefore, the present invention is characterized in that it does not have the above-mentioned ground metal melting mark.
図１および図２にそれぞれ、溶融痕が有る被膜損傷部と溶融痕がない被膜損傷部の二次電子像写真を示す。
各図において、上側の黒い部分は被膜であり、その下部に見られる領域が地鉄の露出部である。
図１では、地鉄が溶融した後に凝固した滑らかな曲線状の組織を呈しているのに対し、図２の地鉄組織は、より細かい不連続な凹凸状になっており、フォルステライト被膜が生成したときの形状が残存した凹凸の形状、すなわち、網の目状のネットワーク構造となっているのが分かる。
FIG. 1 and FIG. 2 show secondary electron image photographs of a film damage part having a melting mark and a film damage part having no melting mark, respectively.
In each figure, the black part on the upper side is a film, and the area seen in the lower part is the exposed part of the ground iron.
FIG. 1 shows a smooth curved structure that solidifies after the base iron melts, whereas the base iron structure of FIG. 2 has finer discontinuous irregularities, and the forsterite coating is It can be seen that the shape when generated is an uneven shape, that is, a net-like network structure.
［ビーム照射手法］
図２に示したような地鉄組織は、以下に示す照射条件にて、方向性電磁鋼板に電子ビームを照射することによって得ることが可能である。
電子ビームは、鋼板を横切るように、鋼板の幅端部からもう一方の幅端部まで、その方向が鋼板の圧延方向から60〜120°の角度になるように、鋼板表面を走査させる。この範囲から逸脱した場合には、磁区細分化効果が弱く、照射後の鉄損が十分に低減しない。また、走査は、一方向に直線状でも、曲線状でも良い。さらに、照射を要する領域の長さが大きい場合には、複数の照射源を用いて照射しても良い。
[Beam irradiation method]
The base iron structure as shown in FIG. 2 can be obtained by irradiating the grain-oriented electrical steel sheet with an electron beam under the following irradiation conditions.
The electron beam scans the surface of the steel sheet so as to cross the steel sheet from the width end of the steel sheet to the other width end so that the direction is an angle of 60 to 120 ° from the rolling direction of the steel sheet. When deviating from this range, the magnetic domain refinement effect is weak and the iron loss after irradiation is not sufficiently reduced. The scanning may be linear or curved in one direction. Further, when the length of the region requiring irradiation is large, irradiation may be performed using a plurality of irradiation sources.
また、ビームは、鋼板表面の走査線に沿って、ビームの照射時間が、長時間（ｓ1）と短時間（ｓ2）を繰返すようにして行うが、通常、ｓ1に比較してｓ2は十分小さいため、ｓ1の逆数を照射周波数と定義することができる。また、この繰返しの距離周期をドットピッチと呼ぶ。
ここで、照射周波数は、20〜1000kHzとすることが好ましい。照射周波数が20kHz未満では、１ドットでの照射時間が過度に長くなるため、地鉄が溶融しやすくなり、一方1000kHz超では照射時間が短すぎて十分な熱量を投入することができず、鉄損が低減しない。
また、ドットピッチは、0.1mm以上0.5mm以下とすることが望ましい。0.1mmよりも小さい場合は、ビームの走査速度が遅くなって、照射材の生産効率が悪くなる。一方、0.5mmよりも大きい場合には、磁区細分化効果が弱く、鉄損が十分には低減しない。
さらに、上記の鋼板の端部から端部までの走査は、圧延方向に２〜10mmの間隔を隔てて繰り返し行う。この間隔が過度に短いと、生産能力が過度に減少してしまうため、２mm以上とするのが好ましい。また、過度に長いと、磁区細分化効果が十分発揮されないため、10mm以下とすることが好ましい。
Further, the beam along a scan line of the steel sheet surface, the irradiation time of the beam, is performed so as to repeat a long time (s 1) and short (s 2), usually, as compared to s 1 s Since 2 is sufficiently small, the reciprocal of s 1 can be defined as the irradiation frequency. This repeated distance period is called a dot pitch.
Here, the irradiation frequency is preferably 20 to 100 kHz. If the irradiation frequency is less than 20 kHz, the irradiation time for one dot will be excessively long, and the iron will be easily melted. On the other hand, if it exceeds 1000 kHz, the irradiation time is too short to supply a sufficient amount of heat. Loss is not reduced.
The dot pitch is preferably 0.1 mm or more and 0.5 mm or less. If it is smaller than 0.1 mm, the beam scanning speed becomes slow, and the production efficiency of the irradiated material becomes poor. On the other hand, when it is larger than 0.5 mm, the magnetic domain subdivision effect is weak and the iron loss is not sufficiently reduced.
Further, the scanning from the end portion to the end portion of the steel plate is repeatedly performed at intervals of 2 to 10 mm in the rolling direction. If this interval is excessively short, the production capacity will be excessively reduced. Further, if it is excessively long, the magnetic domain fragmentation effect is not sufficiently exhibited.
そして、本発明においては、上記した条件での電子ビームの照射に際し、電子ビームの加速電圧Ｖａ(kV)とビーム径ｄ(μm)について、次式
ｄ＞0.007×Ｖａ2−2.72×Ｖａ＋474
の関係を満足させることが重要である。
In the present invention, the electron beam acceleration voltage Va (kV) and the beam diameter d (μm) when the electron beam is irradiated under the above-described conditions are expressed by the following equation: d> 0.007 × Va 2 −2.72 × Va + 474
It is important to satisfy this relationship.
図３に、電子ビームの加速電圧とビーム径を種々に変化させた場合における、照射部の地鉄溶融痕の有無について調査した結果を示す。また、横軸０の位置には、レーザ照射に際してビーム径を種々に変化させた場合の調査結果を併記する。なお、その他の電子ビームの照射条件は、ドットピッチ：0.4mm、照射周波数：100kHzである。また、レーザ照射は40m/sの走査速度の連続レーザによって行った。
同図に示したとおり、電子ビーム照射の場合に、地鉄における溶融痕を抑制するには、電子ビームの加速電圧Ｖａ(kV)とビーム径ｄ(μm)について、上記の関係式を満足させる必要があることが分かる。これに対し、レーザ照射の場合には、ビーム径を500μmまで拡大させても溶融痕をなくすことはできなかった。
なお、溶融痕の生成を抑制した場合は、照射による磁束密度の劣化が極めて小さく、図３中に○印で示した鋼板は、いずれも磁束密度の減少量ΔＢ8は0.001Ｔ以下であった。
FIG. 3 shows the results of investigating the presence or absence of a ground metal melt mark in the irradiated area when the acceleration voltage and beam diameter of the electron beam are variously changed. Further, at the position of the horizontal axis 0, the investigation results when the beam diameter is variously changed during laser irradiation are also shown. Other electron beam irradiation conditions are dot pitch: 0.4 mm and irradiation frequency: 100 kHz. Laser irradiation was performed with a continuous laser having a scanning speed of 40 m / s.
As shown in the figure, in the case of electron beam irradiation, the above relational expression is satisfied with respect to the acceleration voltage Va (kV) and the beam diameter d (μm) of the electron beam in order to suppress melting marks in the ground iron. I understand that it is necessary. On the other hand, in the case of laser irradiation, melting marks could not be eliminated even if the beam diameter was expanded to 500 μm.
Note that if suppressing the formation of traces of melting, deterioration is extremely small in magnetic flux density due to irradiation, steel plates shown in ○ mark in Fig. 3, both reduction .DELTA.B 8 of the magnetic flux density was less than 0.001T .
上記の関係式により、溶融痕が支配されることに関して、その詳細は明確に解明されたわけではないが、発明者らは次のように考えている。
加速電圧は高い方が、地鉄の照射内部にまで電子が侵入し、熱影響領域が拡大して、局所的な地鉄の高温化が抑制されるため、溶融しにくいと考えられる。また、ビーム径は大きい方が、ビームのエネルギ密度が減少し、同様に局所的な地鉄の高温化が抑制されるため、地鉄が溶融しにくいと考えられる。従って、これらを適切に制御することによって、溶融痕の生成が効果的に抑制され、その結果、十分な低鉄損化が磁束密度の劣化なしに達成できたものと考えられる。
なお、ビームの照射表層でエネルギが吸収されるレーザ照射の場合には、本条件の下、ビーム径の調整だけでは、溶融痕の抑制は難しい。
The details of the fact that the melt mark is governed by the above relational expression have not been clearly clarified, but the inventors consider as follows.
A higher acceleration voltage is considered to be difficult to melt because electrons penetrate into the irradiation of the steel and the heat-affected area is expanded to prevent local high temperature of the steel. In addition, it is considered that the larger the beam diameter, the lower the energy density of the beam, and similarly the local increase in the temperature of the ground iron is suppressed. Therefore, it is considered that by appropriately controlling these, the formation of melting marks is effectively suppressed, and as a result, a sufficiently low iron loss can be achieved without deterioration of the magnetic flux density.
In the case of laser irradiation in which energy is absorbed by the irradiation surface layer of the beam, it is difficult to suppress melting marks only by adjusting the beam diameter under this condition.
本発明において、電子ビームの加速電圧Ｖａは40〜300kV程度とすることが望ましい。というのは、加速電圧Ｖａが40kVに満たないと鋼板内部への侵入深さが過度に小さくなって、局所的に熱が蓄積して地鉄が溶融しやすくなってしまい、一方300kVを超えると照射するビーム電流の絶対値が小さくなって、高精度の制御ができなくなるからである。
また、ビーム径ｄは200〜500μm程度とすることが望ましい。というのは、ビーム径ｄが200μmに満たないと照射熱が局所的に蓄積して地鉄が溶融しやすくなり、一方500μmを超えると格子歪みの形成領域の体積が過度に大きくなって、鉄損、特にヒステリシス損が劣化するからである。
また、ビーム径はビームプロファイル（ビーム強度の空間分布）を測定し、ピーク強度値の1/e2(〜13.5％)の強度を有する部分の径として定義した。
In the present invention, the acceleration voltage Va of the electron beam is preferably about 40 to 300 kV. This is because if the acceleration voltage Va is less than 40 kV, the penetration depth into the steel sheet will be excessively small, and heat will accumulate locally and the steel will be easily melted, whereas if it exceeds 300 kV. This is because the absolute value of the beam current to be irradiated becomes small and high-precision control cannot be performed.
The beam diameter d is preferably about 200 to 500 μm. This is because if the beam diameter d is less than 200 μm, the irradiation heat accumulates locally and the steel is easily melted. On the other hand, if it exceeds 500 μm, the volume of the lattice strain formation region becomes excessively large. This is because the loss, particularly the hysteresis loss, deteriorates.
The beam diameter was defined as the diameter of a portion having an intensity of 1 / e 2 (˜13.5%) of the peak intensity value by measuring the beam profile (spatial distribution of beam intensity).
本発明を実施するために最良なその他の電子ビーム照射条件として、照射エネルギなどは、ＷＤ（ワーキングディスタンス）、真空度などの条件によって調整範囲、適正値が異なるため、従来知見に基づき適宜調整を行えば良い。 As the other best electron beam irradiation conditions for carrying out the present invention, the adjustment range and appropriate values of irradiation energy and the like vary depending on conditions such as WD (working distance) and the degree of vacuum. Just do it.
［鉄損および磁束密度の評価］
長さ（圧延方向）：280mm、幅（圧延直角方向）：100mmの試料を用い、JIS C2556に準拠して、単板磁気試験装置による磁気測定を行った。
[Evaluation of iron loss and magnetic flux density]
Using a sample having a length (rolling direction) of 280 mm and a width (perpendicular to the rolling direction) of 100 mm, magnetic measurement was performed using a single plate magnetic test apparatus in accordance with JIS C2556.
［素材の成分組成］
本発明が適用される方向性電磁鋼板の素材の成分組成としては、例えば以下の元素が挙げられる。
Si：2.0〜8.0質量％
Siは、鋼の電気抵抗を高め、鉄損を改善するのに有効な元素であるが、含有量が2.0質量％に満たないと十分な鉄損低減効果が達成できず、一方8.0質量％を超えると加工性が著しく低下し、また磁束密度も低下するため、Si量は2.0〜8.0質量％の範囲とすることが好ましい。
[Component composition of the material]
Examples of the component composition of the material of the grain-oriented electrical steel sheet to which the present invention is applied include the following elements.
Si: 2.0 to 8.0 mass%
Si is an element effective in increasing the electrical resistance of steel and improving iron loss. However, if the content is less than 2.0% by mass, a sufficient iron loss reduction effect cannot be achieved, while 8.0% by mass is achieved. When it exceeds, workability will fall remarkably and magnetic flux density will also fall, Therefore It is preferable to make Si amount into the range of 2.0-8.0 mass%.
Ｃ：50質量ppm以下
Ｃは、熱延板組織の改善のために添加を行うが、最終製品では磁気時効の起こらない50質量ppm以下までＣを低減することが好ましい。
C: 50 mass ppm or less C is added to improve the hot-rolled sheet structure, but it is preferable to reduce C to 50 mass ppm or less where magnetic aging does not occur in the final product.
Mn：0.005〜1.0質量％
Mnは、熱間加工性を良好にする上で必要な元素であるが、含有量が0.005質量％未満ではその添加効果に乏しく、一方1.0質量％を超えると製品板の磁束密度が低下するため、Mn量は0.005〜1.0質量％の範囲とすることが好ましい。
Mn: 0.005 to 1.0 mass%
Mn is an element necessary for improving the hot workability. However, if the content is less than 0.005% by mass, the effect of addition is poor, whereas if it exceeds 1.0% by mass, the magnetic flux density of the product plate decreases. The amount of Mn is preferably in the range of 0.005 to 1.0 mass%.
上記の基本成分以外に、磁気特性改善成分として、次に述べる元素を適宜含有させることができる。
Ni：0.03〜1.50質量％、Sn：0.01〜1.50質量％、Sb：0.005〜1.50質量％、Cu：0.03〜3.0質量％、Ｐ：0.03〜0.50質量％、Mo：0.005〜0.10質量％およびCr：0.03〜1.50質量％のうちから選んだ少なくとも１種
Niは、熱延板組織を改善して磁気特性を向上させるために有用な元素である。しかしながら、含有量が0.03質量％未満では磁気特性の向上効果が小さく、一方1.50質量％を超えると二次再結晶が不安定になり磁気特性が劣化する。そのため、Ni量は0.03〜1.50質量％の範囲とするのが好ましい。
また、Sn，Sb，Cu，Ｐ，MoおよびCrはそれぞれ、磁気特性の向上に有用な元素であるが、いずれも上記した各成分の下限に満たないと磁気特性の向上効果が小さく、一方上記した各成分の上限量を超えると二次再結晶粒の発達が阻害されるため、それぞれ上記の範囲で含有させることが好ましい。
なお、上記成分以外の残部は、製造工程において混入する不可避的不純物およびFeである。
In addition to the above basic components, the following elements can be appropriately contained as magnetic property improving components.
Ni: 0.03-1.50 mass%, Sn: 0.01-1.50 mass%, Sb: 0.005-1.50 mass%, Cu: 0.03-3.0 mass%, P: 0.03-0.50 mass%, Mo: 0.005-0.10 mass% and Cr: At least one selected from 0.03 to 1.50 mass%
Ni is an element useful for improving the magnetic properties by improving the hot-rolled sheet structure. However, if the content is less than 0.03% by mass, the effect of improving the magnetic properties is small. On the other hand, if it exceeds 1.50% by mass, the secondary recrystallization becomes unstable and the magnetic properties deteriorate. Therefore, the amount of Ni is preferably in the range of 0.03 to 1.50 mass%.
Sn, Sb, Cu, P, Mo, and Cr are elements that are useful for improving the magnetic properties. However, if the lower limit of each component is not satisfied, the effect of improving the magnetic properties is small. If the upper limit amount of each component is exceeded, the development of secondary recrystallized grains is hindered.
The balance other than the above components is inevitable impurities and Fe mixed in the manufacturing process.
フォルステライト被膜およびリン酸塩系の張力被膜をそなえる板厚：0.23mmの方向性電磁鋼板に対して、表１に示す条件で、電子ビーム照射を行った。電子ビームの照射条件は、ドットピッチ：0.4mm、照射周波数：100kHz、圧延方向の照射線間隔：５mmとした。
なお、得られた被膜はいずれも、φ30mmの丸棒に巻き付けたときに、巻きの内側に被膜損傷が生じる剥離特性を有するものであった。ビーム照射後に、照射部のＳＥＭ観察および磁気測定を行った。磁気測定は圧延方向280mm×圧延直角方向100mmの試料にて、JIS C 2556に準拠した単板磁気試験装置（ＳＳＴ装置）を用いて行った。
得られた結果を、表１に示す。
Electron beam irradiation was performed under the conditions shown in Table 1 on a directional electromagnetic steel sheet having a forsterite film and a phosphate-based tensile film having a thickness of 0.23 mm. The electron beam irradiation conditions were a dot pitch: 0.4 mm, an irradiation frequency: 100 kHz, and an irradiation line interval in the rolling direction: 5 mm.
All of the obtained coatings had a peeling property that caused coating damage inside the winding when wound around a round rod of φ30 mm. After the beam irradiation, SEM observation and magnetic measurement of the irradiated part were performed. Magnetic measurement was performed using a single-plate magnetic test apparatus (SST apparatus) based on JIS C 2556 on a sample with a rolling direction of 280 mm and a rolling perpendicular direction of 100 mm.
The obtained results are shown in Table 1.
同表に示したとおり、本発明に従って電子ビームを照射することにより、被膜損傷部に地鉄溶融が認められない方向性電磁鋼板を得ることができる。
しかも、本発明に従い得られた方向性電磁鋼板は、照射後の鉄損Ｗ17/50が0.70W/kg以下であり、しかも照射による磁束密度の低減量ΔＢ8が0.001Ｔ以下という高磁束密度を兼ね備えていた。
As shown in the table, by directing an electron beam according to the present invention, it is possible to obtain a grain-oriented electrical steel sheet in which no molten iron is recognized in the damaged part of the film.
Moreover, the grain- oriented electrical steel sheet obtained according to the present invention has a high magnetic flux density in which the iron loss W 17/50 after irradiation is 0.70 W / kg or less, and the reduction amount ΔB 8 of the magnetic flux density by irradiation is 0.001 T or less. Had both.
Claims (2)
被膜剥離内部の表面SEM観察による二次電子像において、地鉄溶融痕がなく、鉄損Ｗ 17/50 が0.70W/kg以下であることを特徴とする方向性電磁鋼板。 It is a grain-oriented electrical steel sheet having a linear strain extending in the direction crossing the rolling direction of the steel sheet inside the steel sheet base iron, and the coating on the strain existing area is at least partially peeled off,
In the secondary electron image by decapsulated inner surface SEM observation, the grain-oriented electrical steel sheet, wherein the base steel melt marks rather name iron loss W 17/50 is not more than 0.70 W / kg.
上記の方向性電磁鋼板を製造するに当たり、加速電圧をＶａ(kV)、ビーム径をｄ(μm)とするとき、これらＶａおよびｄが、次式
ｄ＞0.007×Ｖａ2−2.72×Ｖａ＋474
の関係を満足する条件で電子ビームを照射して線状の歪みを導入することを特徴とする方向性電磁鋼板の製造方法。 A method for producing the grain-oriented electrical steel sheet according to claim 1,
In manufacturing the grain-oriented electrical steel sheet, when the acceleration voltage is Va (kV) and the beam diameter is d (μm), these Va and d are expressed by the following formula: d> 0.007 × Va 2 −2.72 × Va + 474
Method for producing oriented electrical steel sheets towards you, characterized in that under the conditions satisfying the relationship introducing distortion of the electron beam is irradiated linear.
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