JPS6342331A - Production of low iron loss grain oriented electrical steel sheet - Google Patents
Production of low iron loss grain oriented electrical steel sheetInfo
- Publication number
- JPS6342331A JPS6342331A JP18345786A JP18345786A JPS6342331A JP S6342331 A JPS6342331 A JP S6342331A JP 18345786 A JP18345786 A JP 18345786A JP 18345786 A JP18345786 A JP 18345786A JP S6342331 A JPS6342331 A JP S6342331A
- Authority
- JP
- Japan
- Prior art keywords
- steel sheet
- iron loss
- oriented electrical
- electrical steel
- strain
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 229910001224 Grain-oriented electrical steel Inorganic materials 0.000 title claims abstract description 15
- 238000004519 manufacturing process Methods 0.000 title claims description 6
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 title abstract description 48
- 229910052742 iron Inorganic materials 0.000 title abstract description 24
- 238000010438 heat treatment Methods 0.000 claims abstract description 10
- 229910000831 Steel Inorganic materials 0.000 abstract description 22
- 239000010959 steel Substances 0.000 abstract description 22
- 238000000137 annealing Methods 0.000 abstract description 18
- 230000000694 effects Effects 0.000 abstract description 9
- 230000005381 magnetic domain Effects 0.000 abstract description 9
- 238000005096 rolling process Methods 0.000 abstract description 7
- 238000002791 soaking Methods 0.000 abstract description 4
- 230000011218 segmentation Effects 0.000 abstract description 3
- 230000003247 decreasing effect Effects 0.000 abstract 3
- 238000000034 method Methods 0.000 description 7
- 239000000919 ceramic Substances 0.000 description 4
- 239000013078 crystal Substances 0.000 description 4
- 238000005516 engineering process Methods 0.000 description 4
- 238000012545 processing Methods 0.000 description 3
- 238000007670 refining Methods 0.000 description 3
- 239000011248 coating agent Substances 0.000 description 2
- 238000000576 coating method Methods 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 230000001678 irradiating effect Effects 0.000 description 2
- 230000001603 reducing effect Effects 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 238000013459 approach Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000005284 excitation Effects 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000010304 firing Methods 0.000 description 1
- 230000004907 flux Effects 0.000 description 1
- 229910052839 forsterite Inorganic materials 0.000 description 1
- 239000003779 heat-resistant material Substances 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- HCWCAKKEBCNQJP-UHFFFAOYSA-N magnesium orthosilicate Chemical compound [Mg+2].[Mg+2].[O-][Si]([O-])([O-])[O-] HCWCAKKEBCNQJP-UHFFFAOYSA-N 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1294—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a localized treatment
Landscapes
- Engineering & Computer Science (AREA)
- Chemical & Material Sciences (AREA)
- Physics & Mathematics (AREA)
- Electromagnetism (AREA)
- Manufacturing & Machinery (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacturing Of Steel Electrode Plates (AREA)
Abstract
Description
【発明の詳細な説明】
(産業上の利用分野)
本発明は歪取焼鈍等の熱処理をしても鉄損改善効果が消
失することのない、低鉄損方向性電磁鋼板の製造方法に
関するものである。[Detailed Description of the Invention] (Industrial Application Field) The present invention relates to a method for manufacturing grain-oriented electrical steel sheets with low core loss, in which the core loss improvement effect does not disappear even after heat treatment such as stress relief annealing. It is.
方向性電磁鋼板は主として変圧器の鉄心として使用され
その磁気特性、特に鉄損が低いことが要求されている。Grain-oriented electrical steel sheets are mainly used as cores of transformers, and are required to have low magnetic properties, especially low iron loss.
鉄損を減少させるためには銅板を構成する二次再結晶粒
の結晶方位を(110)<001>方位、いわゆるゴス
方位に近づけること、鋼の不純物を減少させることが必
要とされ、これらの方法にて確かに鉄損は減少するが結
晶方位をゴス方位に近づけるに従って結晶粒が大きくな
り鉄損の低減は期待した程得られない。これは結晶粒が
大きくなるとそれに比例して磁区幅が広がり渦電流損が
増加するためである。In order to reduce iron loss, it is necessary to bring the crystal orientation of the secondary recrystallized grains that make up the copper plate closer to the (110) <001> orientation, the so-called Goss orientation, and to reduce impurities in the steel. This method does indeed reduce iron loss, but as the crystal orientation approaches the Goss orientation, the crystal grains become larger and the iron loss cannot be reduced as much as expected. This is because as the crystal grains become larger, the magnetic domain width expands in proportion to the size and eddy current loss increases.
(従来の技術)
この現象を解消し、鉄損の減少を図る技術としていわゆ
る磁区細分化技術が登場した。現在工業化されている例
では、特公昭57−2252号公報等に開示されている
、仕上焼鈍済の方向性電磁鋼板に圧延方向にほぼ直角方
向に線状にレーザービームを照射する技術がある。レー
ザービームの照射により鋼板に線状に高転位密度領域が
形成され磁区幅が細分化される。これ等の技術により鉄
損の大幅な減少が可能になった。(Prior Art) So-called magnetic domain refining technology has emerged as a technology to eliminate this phenomenon and reduce iron loss. A currently industrialized example is a technique disclosed in Japanese Patent Publication No. 57-2252, etc., in which a finish annealed grain-oriented electrical steel sheet is linearly irradiated with a laser beam in a direction substantially perpendicular to the rolling direction. By irradiating the laser beam, linear high dislocation density regions are formed in the steel sheet, and the magnetic domain width is subdivided. These technologies have made it possible to significantly reduce iron loss.
しかしながら上記の技術で得られた鋼板は鉄損減少効果
がレーザーにより導入された歪による磁区細分化による
ものであるため、鋼板を焼鈍すると鉄損改善効果が消失
する欠点を持っている。従って歪取焼鈍を必要とする巻
鉄心型変圧器には該鋼板は使用できない。一方歪取焼鈍
の可能な磁区細分化技術としては特開昭60−1031
24号公報等で鋼板に局所的に異物を配置する方法等が
開示されている。しかしこの場合製造方法が複雑で工業
化が難しくまたコスト増も避けられない。However, the iron loss reducing effect of the steel plate obtained by the above technique is due to magnetic domain refining due to the strain introduced by the laser, so the iron loss improving effect disappears when the steel plate is annealed. Therefore, this steel plate cannot be used in wound core type transformers that require stress relief annealing. On the other hand, as a magnetic domain refining technology that allows strain relief annealing, Japanese Patent Application Laid-Open No. 60-1031
Japanese Patent No. 24 and the like disclose a method of locally arranging foreign matter on a steel plate. However, in this case, the manufacturing method is complicated and industrialization is difficult, and an increase in cost is unavoidable.
(発明が解決しようとする問題点)
本発明は上掲従来技術におけるような欠点、不利を伴う
ことなくして、歪取焼鈍等の熱処理を行っても鉄損改善
効果が消失しない低鉄損方向性電磁鋼板を製造すること
を目的とする。(Problems to be Solved by the Invention) The present invention is directed toward a low core loss in which the core loss improvement effect does not disappear even after heat treatment such as strain relief annealing, without the drawbacks and disadvantages of the above-mentioned prior art. The purpose is to manufacture magnetic steel sheets.
(問題点を解決するための手段)
上記目的を達成するため多くの実験を行い検討した結果
仕上焼鈍された方向性電磁鋼板に、500℃以上の加熱
状態において局所的に塑性歪を加えることにより歪取焼
鈍を行っても消失しない鉄損改善効果が得られることを
新規に見出し本発明を完成した。(Means for solving the problem) In order to achieve the above objective, we conducted many experiments and studied the results by applying local plastic strain to finish annealed grain-oriented electrical steel sheets under heating conditions of 500°C or higher. We have newly discovered that an iron loss improvement effect that does not disappear even when strain relief annealing is performed has been newly discovered, and the present invention has been completed.
すなわち本発明は仕上焼純情の方向性電磁鋼板を500
℃以上の加熱状態において、該鋼板表面に局所的塑性歪
を付与することを特徴とする低鉄損方向性電磁鋼板の製
造方法である。In other words, the present invention uses 500 grain-oriented electrical steel sheets with a finish-sintered purity.
This is a method for producing a grain-oriented electrical steel sheet with low core loss, characterized in that local plastic strain is imparted to the surface of the steel sheet in a heated state at a temperature of .degree. C. or higher.
以下本発明を知見するに至った実験結果にもとづき詳細
に説明する。The present invention will be explained in detail below based on the experimental results that led to the discovery of the present invention.
円筒胴表面に円周ピッチ2〜50+r+mの間隔をおい
て円筒軸方向に沿ってのびる多数のナイフェツジ状の突
起を持つセラミックロールと同じくセラミック製の平ロ
ールを連続焼鈍炉均熱帯内に設け、仕上焼24後の方向
性電磁鋼板を該均熱帯内における加熱下に、上記ロール
間に通板させ突起との圧接による塑性歪の導入処理に供
した。かくして鋼板には圧延方向と直角方向にて線状の
塑性歪付与域が局部的に形成される。線状歪付与域の間
隔は上記の突起の円周ピッチに依存し、また塑性歪量は
ロール間の締めつけ程度を変えることにより可変である
。A ceramic roll having a large number of knife-like protrusions extending along the axial direction of the cylinder at a circumferential pitch of 2 to 50+r+m on the surface of the cylinder and a flat roll made of ceramic are installed in the soaking zone of a continuous annealing furnace and finished. The grain-oriented electrical steel sheet after baking 24 was heated in the soaking zone and passed between the rolls to introduce plastic strain through pressure contact with the protrusions. In this way, a linear plastic strain imparted region is locally formed in the steel plate in a direction perpendicular to the rolling direction. The interval between the linear strain applying regions depends on the circumferential pitch of the projections, and the amount of plastic strain can be varied by changing the degree of tightening between the rolls.
このようにして塑性歪が付与された鋼板は引続き冷却帯
を通り室温に至る。The steel plate to which plastic strain has been applied in this manner continues to pass through a cooling zone and reach room temperature.
冷却後の鋼板は800℃、3時間、N2ガス雰囲気中で
歪取焼鈍を行った後磁気特性の測定を行った。After cooling, the steel plate was subjected to strain relief annealing at 800° C. for 3 hours in an N2 gas atmosphere, and then its magnetic properties were measured.
第1図は塑性歪を加えた均熱温度が鉄損値の改善に及ぼ
す影響を示したものである。図のたて軸にとったW l
1/S Qは、磁束密度1.7テスラ、50ヘルツに
おける鉄損を示している。Figure 1 shows the influence of the soaking temperature to which plastic strain is applied on improving the iron loss value. W l taken on the vertical axis of the figure
1/S Q indicates iron loss at a magnetic flux density of 1.7 Tesla and 50 Hertz.
供試鋼板の板厚は0.23mmである。The thickness of the test steel plate is 0.23 mm.
この場合同一加工温度でも線状付与域の間隔と、塑性歪
量とによって効果は異なっていたが500℃未満ではい
ずれの条件でも加工歪を付与しない無処理とほぼ同等の
特性であり、一方500℃以上では特定はできないがい
ずれかの条件で鉄損の低減が認められた(第1図には鉄
損の低減力q忍められた条件のものを示しである)。In this case, even at the same processing temperature, the effect differed depending on the distance between the linear applied regions and the amount of plastic strain, but below 500°C, the properties were almost the same as those without processing without applying any processing strain, while at 500°C Although it was not possible to specify the temperature above ℃, a reduction in iron loss was observed under some conditions (Figure 1 shows the conditions under which the iron loss reduction force q was tolerated).
(作 用)
第1図に示した実験の効果に明らかなように加熱温度を
500℃以上にした場合比較材に較べて大幅な鉄損減少
があられれ、しかもこのように500℃以上での線状の
塑性歪導入によって、もはや歪取焼鈍を行っても消失す
ることのない鉄損減少効果が3忍められた。(Function) As is clear from the experimental effects shown in Figure 1, when the heating temperature is increased to 500°C or higher, there is a significant reduction in iron loss compared to the comparative material. By introducing linear plastic strain, an iron loss reducing effect that does not disappear even after strain relief annealing was introduced.
本発明に用いられる仕上焼純情の方向性電磁鋼板は公知
の方法で製造される。従って仕上焼純情の鋼板は通常フ
ォルステライト(2!、IgO・SlO□)被膜で覆わ
れておりその上にりん酸塩などを含む上塗りコーティン
グを施してもよく、そして本発明の高温での塑性歪付与
は、上塗りコーティングの前後を問わず、さらには上記
被膜のない裸鋼板に歪を与えても効果があることもたし
かめられている。The finish-sintered grain-oriented electrical steel sheet used in the present invention is manufactured by a known method. Therefore, the steel plate of finishing firing is usually covered with a forsterite (2!, IgO・SlO It has been confirmed that applying strain is effective regardless of whether it is applied before or after the top coating, or even when applying strain to a bare steel plate without the above-mentioned coating.
高温での塑性歪の付゛与は鋼板圧延方向と直角方向に線
状の塑性歪が導入されるようにするのが望ましいけれど
も一般的には直角方向よりも30°位までづれていても
良くまた塑性歪の導入は連続した線状とは限らず点線な
いし破線状であっても良いが、線状の塑性歪付与部の間
隔は3mm〜3Qmmが特に望ましい。When applying plastic strain at high temperatures, it is desirable to introduce linear plastic strain in a direction perpendicular to the rolling direction of the steel plate, but generally it may be deviated by up to 30° from the perpendicular direction. Further, the plastic strain is not necessarily introduced in a continuous linear manner, but may be in the form of a dotted line or a broken line, but it is particularly desirable that the interval between the linear plastic strain applying portions be 3 mm to 3 Q mm.
高温での塑性歪導入により鋼板表面に凹部の生じる場合
があり、この凹部の幅で1mmをこえまたは凹部の深さ
については0.1mmより深いと鉄損値は減少しても励
磁電流が大幅に増える傾向となるので凹部の形成は幅1
mm以内、深さO,1mm以内にすることが望ましい。Introducing plastic strain at high temperatures may cause recesses on the surface of the steel plate.If the width of the recess exceeds 1mm or the depth of the recess exceeds 0.1mm, the excitation current will increase significantly even if the iron loss value decreases. Therefore, the formation of the concave portion has a width of 1
It is desirable that the depth be within 1 mm and the depth O be within 1 mm.
歪の導入法は限定しないが炉内で突起つきロールと平ロ
ール間に通板することにより導入するのが簡単である。The method of introducing strain is not limited, but it is easy to introduce strain by passing the strain between a roll with protrusions and a flat roll in a furnace.
また加熱した鋼板にレーザ等のエネルギービームを照射
したり、耐熱材料を用いて罫書いたりして機械的に歪を
導入しても良い。Alternatively, strain may be introduced mechanically by irradiating the heated steel plate with an energy beam such as a laser or by marking it with a heat-resistant material.
実施例
0.23mm厚で300mm幅の上塗コーティング塗布
後の3.2%Si方向性電磁鋼板を常温(25℃)のば
か300℃、600℃、 800℃の各温度に加熱し
ながら圧延方向と直角方向に線状の塑性歪を導入した。Example: A 3.2% Si grain-oriented electrical steel sheet coated with a 0.23 mm thick and 300 mm wide top coat was heated at room temperature (25° C.) to temperatures of 300° C., 600° C., and 800° C. while rolling it in the rolling direction. Linear plastic strain was introduced in the orthogonal direction.
この塑性歪は鋼板を突起付セラミックロールと平ロール
間に通板して導入したがその線状塑性歪付与部の間隔は
5mmとした。用いたセラミックロールの突起はエツジ
幅0. Q5mm、ロール哨からの高さ0.92mmで
ある。This plastic strain was introduced by passing a steel plate between a ceramic roll with protrusions and a flat roll, and the interval between the linear plastic strain imparting parts was 5 mm. The protrusions of the ceramic roll used had an edge width of 0. Q5mm, height from roll guard 0.92mm.
このように処理した鋼板を800℃、3時間、N2ガス
中で歪取焼鈍を施し磁気特性を測定した。結果を表1に
示すがとくに500℃以上で塑性歪を局部導入すること
により大幅に鉄損が減少している。The thus treated steel plate was subjected to strain relief annealing at 800° C. for 3 hours in N2 gas, and its magnetic properties were measured. The results are shown in Table 1, and the iron loss is significantly reduced by locally introducing plastic strain especially at temperatures above 500°C.
第1表
高温で歪を導入することによって歪取焼鈍後においても
低鉄損が維持された理由は、磁区観察の結果高温で導入
された歪が歪取焼鈍によっても回復せずしてその歪の残
留によって磁区細分化が維持されていることが予想され
る。Table 1 The reason why low core loss was maintained even after strain relief annealing by introducing strain at high temperature is that the strain introduced at high temperature did not recover even after strain relief annealing as a result of magnetic domain observation. It is expected that magnetic domain segmentation is maintained by the residual of .
〈発明の効果)
本発明を用いれば歪取焼鈍を必要とする巻型鉄心の鉄損
を大幅に減少できる。<Effects of the Invention> By using the present invention, the iron loss of a wound core that requires stress relief annealing can be significantly reduced.
第1図は加熱中に歪を導入した時の加熱温度と歪取焼鈍
後の鉄損の関係を示すグラフである。FIG. 1 is a graph showing the relationship between heating temperature when strain is introduced during heating and iron loss after strain relief annealing.
Claims (1)
状態において、該鋼板表面に局所的塑性歪を付与するこ
とを特徴とする低鉄損方向性電磁鋼板の製造方法。1. A method for producing a grain-oriented electrical steel sheet with low core loss, which comprises applying local plastic strain to the surface of a finish-annealed grain-oriented electrical steel sheet in a state of heating to 500° C. or higher.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP18345786A JPS6342331A (en) | 1986-08-06 | 1986-08-06 | Production of low iron loss grain oriented electrical steel sheet |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP18345786A JPS6342331A (en) | 1986-08-06 | 1986-08-06 | Production of low iron loss grain oriented electrical steel sheet |
Publications (1)
Publication Number | Publication Date |
---|---|
JPS6342331A true JPS6342331A (en) | 1988-02-23 |
Family
ID=16136113
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP18345786A Pending JPS6342331A (en) | 1986-08-06 | 1986-08-06 | Production of low iron loss grain oriented electrical steel sheet |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS6342331A (en) |
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH02141817U (en) * | 1989-04-28 | 1990-11-29 | ||
JPH03138318A (en) * | 1989-07-19 | 1991-06-12 | Allegheny Internatl Inc | Method and device for subdividing the magnetic domain system of electromagnetic steel by local hot working for deformation thereof and its product |
CN1048040C (en) * | 1993-12-28 | 2000-01-05 | 川崎制铁株式会社 | Mono-orientational electro-magnetic steel plate with low iron loss and manufacture of same |
JP2010168615A (en) * | 2009-01-21 | 2010-08-05 | Nippon Steel Corp | Method for producing low iron loss single-oriented electromagnetic steel sheet |
-
1986
- 1986-08-06 JP JP18345786A patent/JPS6342331A/en active Pending
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH02141817U (en) * | 1989-04-28 | 1990-11-29 | ||
JPH03138318A (en) * | 1989-07-19 | 1991-06-12 | Allegheny Internatl Inc | Method and device for subdividing the magnetic domain system of electromagnetic steel by local hot working for deformation thereof and its product |
CN1048040C (en) * | 1993-12-28 | 2000-01-05 | 川崎制铁株式会社 | Mono-orientational electro-magnetic steel plate with low iron loss and manufacture of same |
JP2010168615A (en) * | 2009-01-21 | 2010-08-05 | Nippon Steel Corp | Method for producing low iron loss single-oriented electromagnetic steel sheet |
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