JPS6092479A - Grain oriented silicon steel sheet having low iron loss without deterioration of characteristic by stress relief annealing and its production - Google Patents

Abstract

PURPOSE:To provide a grain oriented silicon steel sheet having an excellent iron loss characteristic with which a plastic strain area is not observed in the surface layer part of the base iron and which is not deteriorated in characteristic even if the sheet is subjected to stress relief annealing by forming a different thickness region to the forsterite film in the surface layer part of the base iron. CONSTITUTION:A hot rolled steel sheet consisting of a silicic steel contg. about 2.0-4.0% Si is subjected to one pass or two passes of cold rolling including intermediate annealing to a final thickness. A separating agent for annealing consisting essentially of MgO is locally coated (so as to form the uncoated region of the separating agent) on the surface of the steel sheet having the final thickness. The steel sheet treated in such a way is subjected to secondary recrystallization and the high temp. purification annealing (final finish annealing) in succession thereto to form an ordinary forsterite film on the surface coated with the separating agent for annealing. More specifically, a reduced thickness region is formed between said film and the part where said agent is not coated. As a result, the grain oriented silicon steel sheet which is so formed that the actual record in segmentation of the magnetic domain width of the product is assured without deteriorating the characteristic even after stress relief annealing at a high temp. is obtd.

Description

【発明の詳細な説明】 技術分野 鉄損の低い方向性番プい素鋼板とその製造方法に関して
、この明細書に述べる技術内容は、とくに鋼板表面の被
膜に不均一性をイリりしｃ核表面に異　−張力の働く領
域を区画形成させることにより、鉄損を向上させること
に関連している。[Detailed Description of the Invention] Technical field The technical content described in this specification regarding grain-oriented steel sheets with low iron loss and their manufacturing methods is particularly focused on preventing unevenness in the coating on the surface of the steel sheets and c-nucleation. It is related to improving iron loss by forming areas on the surface where different tensions act.

背景技術 方向性けい素鋼板は主として変圧器その他の電気機器の
鉄心として利用され、その磁化特性が優れでいること、
とくに鉄損（Ｗ１７１５０で代表される）が低いことが
要求されている。BACKGROUND TECHNOLOGY Grain-oriented silicon steel sheets are mainly used as iron cores for transformers and other electrical equipment, and their magnetization properties are excellent.
In particular, low iron loss (represented by W17150) is required.

このためには、第一に鋼板中の２次再結晶粒の（００１
）粒方イずｌを圧延方向に高度に揃えることが必要であ
り、第二には、最終製品の鋼中に存在Ｊる不純物や析出
物をできるだけ減少させる必要がある。かかる配瞳の下
に製造される方向性（）い素鋼板は、今日まで多くの改
善努力によって、その鉄損値も４１を追って改善され、
最近では板厚０．３０ＩＩＩｌｌの製品でＷ１７１５０
の値が１．０５　Ｗ／ｋｇの低鉄損のものが１！ノられ
ている。For this purpose, firstly, the secondary recrystallized grains in the steel sheet (001
) It is necessary to highly align the grain orientation in the rolling direction, and secondly, it is necessary to reduce as much as possible the impurities and precipitates present in the final product steel. Through many improvement efforts to date, the iron loss value of the grain-oriented steel sheets manufactured under this pupil has been improved by 41.
Recently, W17150 is a product with a plate thickness of 0.30IIIll.
The one with low iron loss with a value of 1.05 W/kg is 1! Being beaten.

しかし、数年１）ｂの１″ネ、ルギー危機を境にして、
電力損失のＪ、り少４１い電気機器をめる傾向が一段と
強まり、それらの鉄芯材料として、ざらに鉄損の低い一
方向１ｊ口ノい素鋼板が要語されるようになっている。However, a few years ago, after the Rugi crisis,
There is a growing trend to install electrical equipment with low power loss, and unidirectional steel sheets with low iron loss are becoming popular as core materials for these devices. .

従来技術ど−その問題点 ところで、方向性りい素鋼板の鉄損を下げる手法として
は、３ｉ含イ、ＪＬＶｌを畠める、製品板厚を薄くする
、２次再結晶粒を細かくする、不純物含有ｍ　ヲ（ａ　
Ｍ　ｔ　ル、ソシＣ（１１０）　（００１）　方４ｆｔ
（１）２次再結晶粒をにり畠１．ＣＪ、に揃えるなど、
主に冶金学的方法が一般に知られているが、これらの手
法は、現行の生産手段の、ｌからはしは曽限界に達して
いて、これ以上の改ｊへは１〜めＵ　ｆｉｌ　Ｌ、　＜
、たとえ多少の改善が認められＩことしＣも、その努力
の割には鉄損改善の実効は僅かとなるに至っている。Conventional technology - Problems By the way, methods to reduce the iron loss of grain-oriented silicon steel sheets include increasing 3i content, increasing JLVl, reducing the thickness of the product sheet, and making secondary recrystallized grains finer. Contains impurities m wo (a
Mt Le, Soshi C (110) (001) 4ft
(1) Secondary recrystallized grains by Nirihata1. CJ, etc.,
Mainly metallurgical methods are generally known, but these methods have reached the limit of the current production means, and further changes cannot be achieved until 1~U fil L. , <
However, even though some improvement was recognized in IC this year, the effectiveness of iron loss improvement was small compared to the efforts made.

これらの方法とは別に、特公昭５４−２３６４７号公報
に開示きれ−（いるように、鋼板表面に２数百結晶阻止
Ｖ１域を形成さけることにより、２次再結晶粒を細粒化
させる方法が提案されている。Apart from these methods, as disclosed in Japanese Patent Publication No. 54-23647, there is a method of making secondary recrystallized grains finer by avoiding the formation of a few hundred crystal blocking V1 regions on the surface of a steel sheet. is proposed.

しかしながらこの方法は、２次再結晶粒径の制御が安定
していないため、実用的どは云いがたい。However, it is difficult to say that this method is practical because control of the secondary recrystallized grain size is not stable.

その他特公昭５８−５９６８号公報には、２次再結晶後
の鋼板の表面にボールペン状小球により、微小歪を鋼板
表層に導入することにより、磁区の幅を微細化し、鉄損
を低減する技術が、また、特公昭５７−２２５２号公報
には、最終製品板表面に、圧延方向にほぼ直角にレーザ
ービームを数■間隔に照射し、鋼板表層に高転位密度領
域を導入でることにより、磁区の幅を微細化し、鉄損を
低減する技術が提案されている。さらに、特開昭５７−
１８８８１０号公報には、放電加工により鋼板表層に微
小歪を導入し、磁区幅を微細化し、鉄損を低減Ｊる同様
の技術が提案されている。これら３種類の方法は、いず
れも２次再結晶後の鋼板の地鉄表層に微小な塑性歪を導
入リ−ることにより磁区幅を微細化し鉄損の低減を図る
もの′であって、均しく実用的であり、かつ鉄損低減効
果も優れているが、鋼板の打抜き加工、せん断加工、巻
き加工などの襖の歪取り焼鈍亡、Ｅ　−−Ｊインクの焼
イ１け処理の如ぎ熱処理によって、塑性歪導入による効
果が減殺される欠点を伴う。な（１３コーテイング処理
後に微小な塑性歪の導入を行う場合は、絶縁性を１１１
　Ｊ：ｊ−Ｊるために絶縁コーディングの再塗布を行わ
ねばなぎうＥｌ″計（・ｌ”Ｊ工程、再塗布■稈と、工
程の大幅増加になり、１ストノアツブをもたらり。In addition, Japanese Patent Publication No. 58-5968 discloses that micro-strain is introduced into the surface layer of the steel plate after secondary recrystallization using ballpoint pen-shaped small balls to refine the width of the magnetic domain and reduce iron loss. The technology is also disclosed in Japanese Patent Publication No. 57-2252, by irradiating the surface of the final product sheet with a laser beam at intervals of several inches approximately perpendicular to the rolling direction to introduce high dislocation density regions into the surface layer of the steel sheet. Techniques have been proposed to reduce iron loss by reducing the width of magnetic domains. Furthermore, JP-A-57-
A similar technique is proposed in Japanese Patent No. 188810, in which minute strain is introduced into the surface layer of a steel plate by electrical discharge machining, the magnetic domain width is made finer, and iron loss is reduced. These three methods all introduce minute plastic strain into the surface layer of the base metal of the steel sheet after secondary recrystallization, thereby refining the magnetic domain width and reducing iron loss. Although it is very practical and has an excellent iron loss reduction effect, it is similar to annealing to remove strain from sliding doors during punching, shearing, and winding of steel plates, and one-time annealing treatment of E--J ink. Heat treatment has the disadvantage that the effect of introducing plastic strain is reduced. (If introducing minute plastic strain after 13 coating treatment, increase the insulation property to 111)
J: In order to reapply the insulating coating, it is necessary to reapply the insulation coating.

発明の目的 この発明は、］記した先行技術とは発想を異にした磁区
幅の細分化り段を５って、高温における歪取り焼鈍の後
にＪ３いでも特性劣化を伴わずに、製品の磁区幅細分化
の実効を確保し得るようにした方向性りいメ・９鋼板を
ｊノえることを「目的とでる。Purpose of the Invention The present invention has a method of refining the magnetic domain width, which is different from the prior art mentioned above, to improve the quality of the product without deteriorating its characteristics even after strain relief annealing at high temperature. The objective is to produce a 9-dimensional steel plate with a directionality that ensures the effectiveness of magnetic domain width refinement.

メを明のナミ：；眉； このブで明は、／Ｊ　Ｍ　’ｌ’、ｌ：　ＩＪい桑鋼板
の表面被膜を構成ＪるフΔルスアライト被ｆｌｕにｄ３
いて厚みの異なる領域づなわち５１イ凡Ｊ領域の存在が
、製品の磁区幅の細分化に極めて右利に寄与Ｊることの
新規知見に立脚りる。The brightness of the eye is:; the eyebrows; the brightness in this block is /J M 'l', l: The surface coating of the IJ mulberry steel plate is d3 to the full-alite coated flu.
This is based on the new knowledge that the existence of regions with different thicknesses, that is, 51 regions, greatly contributes to the subdivision of the magnetic domain width of products.

解決手段の解明経緯 方向性けい素鋼板の製造工程において、最終板厚に冷間
圧延された鋼板は有害な炭素を取除くため通常脱炭焼鈍
が施される。かかる焼鈍によって鋼板は、内部に微細な
分散第２相からなる抑制剤を含有した１次再結晶集合組
織となるが、同時に鋼板表面層は微細なＳｉ　０２粒ゴ
が地畝内に分散したザブスケール構造となる。このｌ＞
Ｊ炭・１次再結晶板には、その表面にＭ（ｔｏを主成分
とする焼鈍分離剤を塗布したのち、２次再結晶焼鈍つい
で・でれに引き続き１２００℃前後での高温純化焼鈍が
施される。この２次再結晶焼鈍によって鋼板の結晶粒は
、（１ＨＩ）　（００１）方位の粗大な粒になる。Elucidation of the solution In the manufacturing process of grain- and grain-oriented silicon steel sheets, the steel sheets that have been cold-rolled to the final thickness are usually subjected to decarburization annealing to remove harmful carbon. Through such annealing, the steel sheet becomes a primary recrystallized texture containing an inhibitor consisting of a finely dispersed second phase, but at the same time, the surface layer of the steel sheet becomes a subscale structure in which fine Si02 grains are dispersed in the ground ridges. It becomes a structure. This l＞
After applying an annealing separator containing M(to as the main component) to the surface of the J coal/first recrystallization plate, secondary recrystallization annealing and subsequent high temperature purification annealing at around 1200°C are performed. Through this secondary recrystallization annealing, the crystal grains of the steel sheet become coarse grains with (1HI) (001) orientation.

また高ぺｉｉ　ＩＩ！’化焼鈍にＪ、って鋼板内部に存
在していた抑制剤の１部であるＳやＳｅヤ）Ｎ等は鋼板
地鉄外に除去される。Takapeii II! During annealing, S, Se, N, etc., which are part of the inhibitors present inside the steel sheet, are removed to the outside of the steel sheet.

さらに、この純化焼鈍において、鋼板表層のりブスケー
ル中のＳｉ　０２と表面に塗イ［］された焼鈍分離剤中
のＭｇＯが、次式、 ２Ｍ（ｌ　Ｏ＋Ｓｉ　０２→ＭｇｆＶＩｇ２　Ｓｉ　Ｏ
’４゜のように反応して鋼板表面に、フＡルステライト
（！ｖｌｏ　２　Ｓｉ　０４　）の多結晶からなる被膜
を形成する。このどき、余剰のＭｇＯは未反応物としで
、鋼板と鋼板との融着を防止する役割を果す。そして高
温純化焼鈍を終えた鋼板は未反応の焼鈍分離剤を取除き
、心間に応じて絶縁コーティングの上塗りやコイルレッ
トを取除くための処理を施して製品とな寸わけで゛ある
。Furthermore, in this purification annealing, the Si 02 in the steel plate surface layer glue scale and the MgO in the annealing separator coated on the surface are expressed by the following formula, 2M(l O + Si 02 → MgfVIg2 Si
The reaction occurs as shown in Figure 4, forming a film made of polycrystalline A-fulsterite (!vlo 2 Si 04 ) on the surface of the steel sheet. At this time, the excess MgO is treated as an unreacted substance and serves to prevent fusion between the steel plates. After high-temperature purification annealing, the steel plate is processed to remove unreacted annealing separator, and to remove the top coat of insulation coating and coillets depending on the center spacing, and then it is made into a finished product.

ところで発明名らは７Ａルスデライト被膜の役割を再調
査した結果、こ゛の被膜が張カイ１加型コーティングと
同様、鋼板に張力を付加し、磁区を細分化していること
、しかｔ）ＪＩｌＱ板の磁区幅の細分化効果は場所にＪ
、り微妙に異っていることを見出した。そこでさらに鋼
板の磁１メ幅の細分化傾向につぎ綿密な検問を加えた結
果、フォルステライト被膜の厚みが変化している場所で
磁区の細分化効果が著しいことが究明されたのである。By the way, as a result of re-investigating the role of the 7A Lusdellite coating, the inventors found that this coating applies tension to the steel plate and subdivides the magnetic domains, similar to the 7A Lusdellite coating. The effect of subdivision of magnetic domain width is J
, I found that there are some slight differences. Therefore, as a result of further detailed examination of the tendency of the magnetic domain width of the steel sheet to become finely divided, it was discovered that the effect of magnetic domain fragmentation is remarkable in places where the thickness of the forsterite coating changes.

発明の構成 この発明は、上２の知見に由来でるものである。Composition of the invention This invention is derived from the above two findings.

ずなわらこの発明は、地鉄表層部に塑性歪域がみられな
いフォルステライト被膜付きの方向性けい素鋼板ぐあっ
て、該フォルステライト被膜が層厚領域を有づることか
らなる、歪取り焼鈍によっても特性が劣化しない低鉄損
の方向性（）い素鋼板である。Zunawara This invention provides strain relief annealing for a grain-oriented silicon steel sheet with a forsterite coating in which no plastic strain region is observed in the surface layer of the steel, and in which the forsterite coating has a thick layer region. It is a grain-oriented steel sheet with low iron loss that does not deteriorate in properties even when exposed to heat.

この発明Ｃ′、素材鋼板につき、塑性歪域がみられない
ものに限定したのは、後）ホづるように、塑性歪の導入
による磁区の細分化方式では、歪取り焼鈍によって特性
の著しい劣化を１（３りから℃ある。In this invention C', the material steel plate is limited to those in which no plastic strain region is observed. The temperature is 1 (3°C).

またこの発明におけるフォルス７−ライ１〜被膜句ぎの
鋼板とは、表面被膜が７オルスアライト被膜単味のもの
に限らず、その上に重ねて一般の上塗り」−ティング被
膜をそなえるものも含むもの、とりる。In addition, the steel plate with a FORS 7-Lye 1~ coating in this invention is not limited to one in which the surface coating is a single 7-ORTHALITE coating, but also includes those with a general overcoating coating layered thereon. Take it.

以下この発明について具体的に説明覆る。This invention will be explained in detail below.

さて、発明者らは実験室的にフォルステライト被膜の厚
みを局所的に変化さし、その領域、形状厚み差、および
方位などが磁区の細分化に及ぼす影響につき、種々の検
問を加え、鉄Ｊｔｌどの関係について調査した。Now, the inventors locally changed the thickness of the forsterite film in the laboratory, conducted various tests to determine the influence of the region, shape thickness difference, orientation, etc. on the subdivision of magnetic domains. We investigated the relationship between JTL and JTL.

なおこの実験にＪ３い−Ｃ局所的に厚みを薄くりるには
、ＨＦ溶液を用いて化学的に）Ａルステライトを溶Ｆｉ
ｒ−ｔｌることにより、また厚みを大きくするには静電
塗装によってフＡルステライトを付加さけることにより
行った、。In addition, in order to locally reduce the thickness of J3-C in this experiment, HF solution is used to chemically dissolve A lusterite.
The thickness was increased by adding A-fulsterite by electrostatic coating.

その結果、フＡルスう一シ、（１−の１ｆｆｌ’？領域
の形状としては、第′１図（イ）に示したにうな連続的
または非運わ°Ｃ的の線状凹凸形状がとくに鉄損低減効
果にＪ３いＣイｊ効Ｃあることが認められた。ただし非
連続の線状凹凸領域に（１５いては、点と点との間隔が
０．５ｍｍ以１１．’、Ｉｆれるど効果はイ１（減した
。この点破線のように線の一部が少しづ′つ抜【］てい
る場合は、鉄損（Ｌ（ｉ戚効宋（まわｊｊ状の場合とは
ば同じであった。As a result, the shape of the 1ffl'? region of False (1-) is a continuous or non-carrying linear uneven shape as shown in Figure 1 (a). In particular, it was recognized that there is an effect of reducing iron loss.However, in discontinuous linear uneven regions (15), if the interval between points is 0.5 mm or more, If However, the effect is reduced by 1 (decreased). If a part of the line is gradually removed like this dotted line, the iron loss (L) is It was the same.

次に］Ａルメ））イ１〜被膜の層厚領域の方向について
は、ｆｆｉ　’Ｉ図（ＩＩ）や第２図に示したように、
圧延の／Ｊ向にλ・１じＧＯ・〜９０°の角度とした場
合がとくに有効であつＩζ。さらにフＡルステライ１〜
異厚領域の厚みｉｒについ（゛は、第３図に示しｌζよ
うに過厚にした揚合し、減厚にした場合もほば同様の結
果が得られ、いずれにしても厚み弁が０．３μｍ以上あ
れば有効であることがわかった。次に連続または非連続
の線状凹凸領域の幅につい【は、第４図に示したにうに
０．０５〜２．０ｍｍとくに０．８〜１．５ｎ＋ｎ＋の
範囲で優れた効果が得られた。Next] Regarding the direction of the thickness region of the film, as shown in Figure (II) and Figure 2,
It is particularly effective to make an angle of λ·1GO·˜90° in the /J direction of rolling. Furthermore, A Fullsterai 1~
Regarding the thickness ir of the different thickness region (゛ is shown in Fig. 3, when the thickness is increased as shown in lζ, almost the same results are obtained when the thickness is decreased, and in any case, the thickness valve is 0. It was found that it is effective if the width of the continuous or discontinuous linear uneven area is 0.05 to 2.0 mm, especially 0.8 to 2.0 mm, as shown in Figure 4. Excellent effects were obtained in the range of 1.5n+n+.

なお）Ａルステライト被膜の層厚領域は、圧延方向を横
切る向きに繰返し形成覆ることが、鋼板全体の鉄損を下
げるために有効で、たとえば第１図（ハ）に示したよう
な領域間の間隔は、第５図に示したようにｌｎｖ〜３０
ｍｍの範囲と−４ることが望ましい。またフォルステラ
イト被膜にお１ノる層厚領域の形成は、鋼板の両面であ
っても、片面にのみひあってｂ、その効果にはどんと変
わりはない。Note) It is effective to repeatedly form and cover the layer thickness region of the A lusterite coating in a direction transverse to the rolling direction. For example, it is effective to reduce the iron loss of the entire steel plate. The interval is lnv~30 as shown in Figure 5.
A range of -4 mm is desirable. Furthermore, even if the forsterite coating is formed in a layer thickness region of 1 mm, it is applied only to one side of the steel plate, and the effect remains the same.

さらに、この発明の鋼板においては、形状変化部分は被
膜８１Ｓに限られているので、変化分は少なく、従って
占積率を低下さびることはほとんどない。Furthermore, in the steel plate of the present invention, since the shape-changing portion is limited to the coating 81S, the amount of change is small, and therefore the space factor is hardly reduced and rust is unlikely to occur.

次にこの発明に係る方向性けい素鋼板の製造方法につい
て説明する。Next, a method for manufacturing a grain-oriented silicon steel sheet according to the present invention will be explained.

この発明の素４１は、公知の製鋼方法、例えば転炉、電
気炉などに五つ−（°製鋼し、さらに迄塊−分塊法また
は連続ｖｉ造法などによってスラブ（鋼片）としたのら
、熱間１１−延によって得られる熱延二１イルを用いる
。The element 41 of the present invention is produced by manufacturing steel using a known steel manufacturing method such as a converter or an electric furnace, and further forming a slab (steel billet) by a block-blooming method or a continuous VI manufacturing method. A hot-rolled 21-yl obtained by hot 11-rolling is used.

この熱延板は、５ｉを２．０〜４．０％程度含有Ｊ。This hot rolled sheet contains about 2.0 to 4.0% of 5i.

る組成である必要がある。というのは、Ｓｌが２．０％
未Ｗｈで（３（鉄損の劣化が大きく、また４、０％を超
えると、冷間加］−性が劣化するからである。The composition must be suitable for This means that Sl is 2.0%
This is because the deterioration of the iron loss is large at less than Wh, and if it exceeds 4.0%, the cold workability deteriorates.

その他の成分についてはｈ向性けい素鋼板の素材成分で
あれば、いり゛れも適用可能である。Any other ingredients can be applied as long as they are the material ingredients of the h-oriented silicon steel sheet.

次に冷間ｌロー延にＪ、す、最終目標板厚とされるが、
冷間圧延は、′１回ｂり、、＜は中間焼鈍を挾む２回の
冷間圧延ににり行なわれる。このとき必要に応じて熱延
板の均一化焼鈍や、ｌ？目１１１圧延に替わる温間圧延
を隔りこともでさる。。Next, the final target thickness is determined by cold rolling.
The cold rolling is carried out in two cold rolling steps, one with an intermediate annealing in between. At this time, if necessary, uniform annealing of the hot rolled sheet or l? It is also possible to use warm rolling to replace the 111th rolling. .

最終板厚どされた冷延板（よ、１ＩｉＪ炭可能な程度の
酸化性雰ｆｕｌｌ気ししくはりｌスクール形成可能な程
度の弱酸化性雰囲気中（゛１次再結晶焼鈍が施される。The final thickened cold-rolled plate is subjected to primary recrystallization annealing in a full oxidizing atmosphere capable of forming 1IJ carbon or a weak oxidizing atmosphere sufficient to form a school.

ついで、鋼板表面にＭ（１０を主成分とづ゛る焼鈍分離
剤を塗布Ｊ゛るのであるが、この塗装ｌ工程において、
鋼板表面に局所的に該分離剤の未塗布領域を形成させる
ことにより、この発明で所期した［１的が有利に達成さ
れるのである。Next, an annealing separator containing M (10) as the main component is applied to the surface of the steel plate.
The first objective of the present invention can be advantageously achieved by locally forming areas on the surface of the steel sheet where the separation agent is not applied.

すなわち、２次再結晶とそれに続く高温純化焼鈍く最終
仕上焼鈍）を行なうことにより、焼鈍分離剤が塗布され
ている面には通常のフォルステライト被膜が形成される
のに対し、焼鈍分離剤が塗装１ｊされていない面には薄
いフォルスアライト被膜しか生成せず、従って減厚領域
が形成されるわけである。In other words, by performing secondary recrystallization followed by high-temperature purification annealing and final finishing annealing), a normal forsterite film is formed on the surface coated with the annealing separator, whereas the annealing separator Only a thin false alite film is formed on the unpainted surface, thus forming a region of reduced thickness.

なお焼鈍分離剤を鋼板へ（＝Ｊ着さＵる手段どしては、
ロールやへケによる塗布、吹ｆ４け、静電塗装が公知で
あるが、いずれを採用してしＪ、い。The method for applying the annealing separator to the steel plate is as follows:
Coating with a roll or spatula, blowing F4, and electrostatic coating are well known, but any of these may be used.

またかかる層厚領域を形成する他の手法としては上記の
方法の他部下にのべる４つの方法がある。Further, as other methods for forming such a thick layer region, there are four methods that are subordinate to the above-mentioned method.

ｉ）１次再結晶焼鈍後の鋼板表面への焼鈍分離剤の塗布
工程において、該塗布に先立も、鋼板表面に焼鈍分離剤
との反応を阻害する物資を１ｇ／Ｂ２以下の範囲で局所
的に付着さける方法。i) In the process of applying an annealing separator to the steel plate surface after primary recrystallization annealing, a substance that inhibits the reaction with the annealing separator is locally applied to the steel plate surface in an amount of 1 g/B2 or less prior to the application. How to avoid adhesion.

この方法においで反応用害物質としてはＳｉ　０２　、
ＡＪ２２０３　、Ｚｒ　０２などの酸化物や、／１）、
ΔＡ、８１１　、Ｎｉ　、　Ｆｅなどの金属が挙げられ
る。かかる反応阻害物質は、１ｇ／ｍ２を超えｃ’（Ｐ
Ｉさると、反応阻害効果が過剰となり、）Ａルステライ
ト被膜が形成されなくなる。従一つＣあくＪ、でも、１
ｇ／ｍ２以下の範囲でノＡルステシイト被膜の減厚■を
制御Ｊる必要がある。’ｃ衣Ｊ３、これらの反応阻害物
質のｖ！Ａ仮への（ｔＪ看手［９としては、塗布、吹付
け、メッキ、印刷ｄ３よび静電塗装などがいずれも利用
できる。In this method, the harmful substances for reaction include Si 02 ,
Oxides such as AJ2203, Zr 02, /1),
Examples include metals such as ΔA, 811, Ni, and Fe. Such a reaction inhibitor exceeds 1 g/m2 c'(P
In the case of I, the reaction inhibiting effect becomes excessive and no lusterite film is formed. Juichitsu C Aku J, but 1
It is necessary to control the thickness reduction of the NOA Rusteshite coating within a range of g/m2 or less. 'c clothing J3, v of these reaction inhibitors! Coating, spraying, plating, printing d3, electrostatic painting, etc. can all be used for A provisional (tJ inspection) [9].

１ｉ）１次再結晶焼鈍後の鋼板表面への焼鈍分離剤の塗
布工程においで、該塗布に先立ら鋼板表面に焼鈍分前剤
スラリー（水と焼鈍分離剤との懸濁液）に対するＩＷ水
水物物質０．Ｉｇ　／ｍ　２以下の範囲で局所的に（”
Ｉ　Ｑ’＃さける方法。1i) In the process of applying an annealing separator to the surface of the steel sheet after primary recrystallization annealing, IW is applied to the surface of the steel sheet prior to the application of an annealing pre-agent slurry (a suspension of water and an annealing separator). Water substance 0. Locally within the range of Ig/m2 or less (”
I Q'# How to avoid.

かかる撥水性物質としては、油性ペイントやワニスなど
がイＩ刊に適合し、鋼板表面と焼鈍分頼剖とのＩＢ　Ｗ
ｐｈをＩｊｌげて、）Ａルステライ１〜生成、反応を遅
ｔｆｔ！させて減厚領域を形成させるわけである。ただ
し０，１（１／ｒａ　２を超えて１１着させた場合は、
反応遅滞効果が過剰となって７オルスｊライト被膜が全
く形成されなくなるので、あくまでも０．１！＋　／ｍ
　２以トの範囲で７オルステライ１〜被膜の減厚量を制
御する必要がある。なＪ３これらの撥水性物質の鋼板へ
のイ］着手段としては、前掲した反応阻害物質と同様、
塗布、吹イ」番ノ、印刷ａ３よび静電塗装などが利用で
きる。As such water-repellent substances, oil-based paints and varnishes are suitable for IBW of steel sheet surfaces and annealing separations.
Raise the pH to produce A Lusterai 1~, slow down the reaction! Thus, a reduced thickness region is formed. However, if 11th place exceeds 0,1 (1/ra 2),
Since the reaction retardation effect becomes excessive and no 7 ors j-lite film is formed, it is only 0.1! + /m
It is necessary to control the amount of thickness reduction of the 7-orsterite film in the range of 2 or more. J3 As a means of attaching these water-repellent substances to the steel plate, similar to the reaction inhibitors listed above,
Coating, blowing, printing A3, electrostatic painting, etc. can be used.

１ｉｉ）１次再結晶焼鈍後の鋼板表°面への焼鈍分離剤
の塗布工程にＪ３いて、その塗布に先立ら、鋼板表面に
鋼中の３ｉの酸化剤となるような物質を２（＋／１１１
２以下の範囲で局所的に１１着さＵる方法。1ii) In the step of applying an annealing separator to the surface of the steel sheet after primary recrystallization annealing, a substance that acts as an oxidizing agent for 3i in the steel is applied to the surface of the steel sheet prior to the application. +/111
A method of locally applying 11 U in a range of 2 or less.

これらの物質はその後の最終仕上焼鈍にＪ３いて高温で
鋼中のＳ　ｌ／！：酸化させ、鋼板表層リブスケール中
のＳ：　０２粒子の聞を増加ざｌることによって、最終
仕上焼鈍後のフォルステライト被膜の厚みを増加さμる
ので、鋼板表面に局所的に過厚被膜を形成させることが
できるわ４−Ｊである。かかる酸化剤としては、Ｆｅ　
Ｏ。These substances are then subjected to a final final annealing at J3 to reduce S l/! in the steel at high temperatures. : By oxidizing and increasing the number of S:02 particles in the surface rib scale of the steel plate, the thickness of the forsterite coating after final annealing is increased, resulting in a locally overthick coating on the steel plate surface. 4-J can be formed. As such an oxidizing agent, Fe
O.

Ｆ６２　Ｑ３．−１’ｉ　０２などの酸化物、Ｆｅ２５
ｉＯｎなどの還元され易い珪酸塩、Ｍ（ＩＩ（ＯＨ）ｚ
などの水酸化物などが有利に適合づるが、これらの酸化
剤の（＝ｌ　Ｗ　但が２１１／ｌ１１２を超えると、被
膜の厚みが大きくなり過ぎて、鋼板への１＆名力を失い
、被膜がはく落してしまって所期した目的を達成づるこ
とかできない。F62 Q3. -1'i 02 and other oxides, Fe25
Easily reduced silicates such as iOn, M(II(OH)z
Hydroxides such as oxidizers such as If you fail, you will not be able to achieve your intended purpose.

１ｖ）２次再結晶後の鋼板表面に被成したフォルレステ
ライト被１１，３／ａ、地鉄鋼板表層に塑性歪を加えな
いようにしＣ除去りることより減厚領域を形成　づ　る
　７ノ　ン大　。1v) Forresterite coating 11,3/a formed on the surface of the steel sheet after secondary recrystallization, forming a reduced thickness region by removing C without applying plastic strain to the surface layer of the base steel sheet. Non-large.

かヨウ／、Ｃ１ｊｖ、ト１ノ’ＣＬｉＬ、化学ｒｊｌ　
Ｊｉｆｆ　ヤｍ解ｒｔｙ＋ｉの他、回転りる円？Ｉ：）
状の凪６による除去、軽圧力による鉄釘での除去さらに
は出力を適切に調整したレーＩＪ”−ビームなどの光学
的除去などの方法がある。とくに光学的除去法としてレ
ーザービームを利用する場合は、１つの光源から複数本
のビームを取出したり、また適当なマスキングの存在の
下に全面照射を行うことにＪ、って、１回の操”作で効
率よく複数本の層厚領域を形成させることかできる利点
がある。Kayo/, C1jv, To1no'CLiL, Chemistry rjl
Jiff In addition to Yam solving rty + i, is there a rotating circle? I:)
There are methods such as removal with a 3-dimensional calm 6, removal with an iron nail using light pressure, and optical removal such as a laser IJ''-beam whose output is appropriately adjusted. In particular, a laser beam is used as an optical removal method. In some cases, it is possible to extract multiple beams from a single light source or to irradiate the entire surface in the presence of appropriate masking. It has the advantage of being able to form

ところで上述した除去方式による層厚領域の形成方法に
おいて、どくに注意すべきことはかかる除去処理の際に
、地鉄表面に塑竹歪域を形成させないようにするとであ
る。というのは塑性歪が導入された場合は、後述づるよ
うに歪取り焼鈍後の鋼板の特性が著しく劣化Ｊるからで
ある。By the way, in the method of forming a thick layer region using the above-mentioned removal method, care must be taken not to form a plastic bamboo strain region on the surface of the base metal during such removal processing. This is because when plastic strain is introduced, the properties of the steel sheet after strain relief annealing are significantly deteriorated, as will be described later.

かような層厚領域の形状としては、連続的な線状凹凸を
なすものがとりわ【ノ有効であるが、その他罪連続す＜
ｒわち点の列で置き替えることもできる。しかし４ｒが
らかかる非連続の線状凹凸の場合は、点と点との間隔が
０．５１１ＩＩ１１以上離れていると効果が小さくなる
。またかような線状凹凸領域幅としては、０．０５〜２
．０Ｉｌ１ｍ程度がとくに効果が大きい。As for the shape of such a layer thickness region, a continuous linear unevenness is particularly effective, but other forms are effective.
It is also possible to replace it with a sequence of points. However, in the case of discontinuous linear unevenness such as 4r, the effect becomes small if the distance between the points is 0.511II11 or more. In addition, the width of such a linear uneven region is 0.05 to 2
．． A value of about 0Il1m is particularly effective.

線状凹凸領域の向きについ（は、ＩＥ延方向に対して６
０〜９０°の角度範囲がとくに好ましい。圧延方向に平
行な方向して場合は効果がなく、圧延方向と直角方向で
最大の効果が得られる。こうした鋼板圧延方向にｉｔす
る角度はとくに垂要で、層厚領域の幅が広′りぎる場合
や、孤立した点の場合に鉄損低減効果が弱まるのは、そ
の方向性が不明瞭になるためと思われる。Regarding the direction of the linear uneven area (is 6 with respect to the IE extension direction)
An angular range of 0 to 90° is particularly preferred. There is no effect in the direction parallel to the rolling direction, and the maximum effect is obtained in the direction perpendicular to the rolling direction. This angle in the rolling direction of the steel plate is particularly important, and the reason why the iron loss reduction effect weakens when the thickness region is too wide or at isolated points is that the directionality becomes unclear. It seems to be for a reason.

こうした連続または非連続の線状凹凸領域は圧延方向に
対しで異なる形状、幅、角度のものも含めて繰返し存（
ｔ　ｔｌることが好ましく、この時の領域と領域との間
隔は１．０〜３０ＩｌｌｌＲの範囲がとりわ番〕有効で
ある。These continuous or discontinuous linear uneven regions, including those with different shapes, widths, and angles, exist repeatedly in the rolling direction (
It is preferable that the spacing between the regions be in the range of 1.0 to 30IllR.

またフィルスプライ１−被膜の層厚の領域は鋼板の両面
に存（しシて６片面のみに存在していてもその効果にＧ
；Ｌどんど変りは４【い。Also, the thickness of the film sply 1 coating exists on both sides of the steel plate (6) Even if it exists only on one side, the effect will be
;L Dondo change is 4 [i.

以し述べたようにして）Ａルステライ１−と被膜に層厚
領域を局所的に形成さμｋｌｊ向１ｇ、　４ノい素鋼板
は、通常の１１１１１日」い素鋼板と同様にそのまま製
品どして使用される場１合、またさらに上塗り絶縁コー
ティングを稈して製品として使用される場合のいずれに
お−（（，１、実際の機器に使用された場Ａ　自　ｈｉ
　／）　Ｉ４紹　讐ｔ、１ここにこの発明に従いフィル
スプライト被膜に層厚領域を区画形成することによって
鉄損特性が改善される理由は、該被膜に異厚領域を段Ｇ
Ｊたことにより鋼板表面には異張力領域が生じるが、こ
の異張ノ」によって鋼板表面に弾性歪が導入され、その
結果磁区が有効に細分化されるためであろうと考えられ
る。A raw steel sheet with a μklj direction of 1g and 4 in which a layer thickness region is locally formed in the coating with A Lusterite 1- as described above is used as a product as it is in the same way as a normal 11111'' raw steel sheet. When used as a product, or when used as a product with a top insulating coating ((,1, When used in actual equipment)
/) I4 Introduction, 1 Herein, the reason why the core loss characteristics are improved by forming thick regions in the fill sprite film according to the present invention is that the film has different thickness regions.
This is thought to be due to the fact that different tension regions are created on the surface of the steel sheet due to the difference in tension, and elastic strain is introduced to the surface of the steel sheet due to this different tension, and as a result, the magnetic domains are effectively subdivided.

このような巽張力弾性歪を附加した方向性けい素鋼板に
おいて【、Ｉ、鋼板の地鉄表層部に塑性歪領域やレーザ
ー照射痕のような高転位密度領域を存在させる従来法の
場合と異なり、人為的な塑性歪領域がみられないので、
通常８００℃前後で１分間から数時間にわたって施され
る歪取り焼鈍を施しでら鉄損の劣化がはとｌυどないと
いう特筆Ｊべき利点がある。前者の場合番よ、地鉄表層
部の塑性歪が高温にＪ：って消滅さくいくので鉄損の劣
化が生じるという致命的な欠点を有づるが、この発明の
場合は歪取り焼鈍の有無にかかわらｆ良好な鉄損を示す
。In a grain-oriented silicon steel sheet to which Tatsumi tensile elastic strain has been added [,I, unlike the conventional method in which high dislocation density regions such as plastic strain regions and laser irradiation marks are present in the surface layer of the steel sheet, , since no artificial plastic strain region is observed,
It has the notable advantage that the deterioration of iron loss does not stop even after strain relief annealing, which is usually performed at around 800°C for a period of one minute to several hours, is carried out. In the former case, the plastic strain in the surface layer of the steel base disappears at high temperatures, leading to deterioration of iron loss, which is a fatal drawback. Despite this, f shows good iron loss.

実施例 １１１上 ３ｉ　：　３．２％を含有りるけい素鋼素材を、常法に
従って厚み０．３Ｏｎ＋ｍの冷間鋼板としたのち脱炭・
１次？Ｑ結晶焼鈍を施し、ついでこの焼鈍板の表面に焼
鈍分離剤を塗布Ｊるに先立って焼鈍分離剤と鋼板４ノブ
スクール中Ｓ：０２どの反応阻害物質であるへλ２０３
粉末を付＠　ｍ　：　０，５（１／　ｍ　２゜ｒａ−ｍ
Ａ向どなり角爪：９０°、何着幅：２Ｉそして圧延方向
の繰返し間隔４　Ｉｌｌ　ＩＩＩの条件下に、鋼板表面
に線状にイ」着さＩ、しかるのち焼鈍分離剤をその上に
塗布してから２次ＩＩ■結晶焼鈍ついで１２００℃。Example 111, Part 3i: A 3.2% silicon steel material was made into a cold steel plate with a thickness of 0.3 On+m according to a conventional method, and then decarburized and
1st order? Q Crystal annealing is performed, and then an annealing separator is applied to the surface of this annealed plate.
Add powder @ m: 0,5 (1/ m 2゜ra-m
Under the conditions of A-direction angle nail: 90°, number of width: 2I, and rolling direction repeating interval of 4 Ill III, I' is applied in a linear manner to the steel sheet surface, and then an annealing separator is applied thereon. Then, secondary II ■ crystal annealing was performed at 1200°C.

５時間の純化焼鈍を施した。Purification annealing was performed for 5 hours.

なお比較のためΔμ２０３粉末の何着処理のない常法に
従う７Ｊ　＞）ｓにＪ、す／Ｊ向性けい素鋼板を作成し
、比較例とした。For comparison, a 7J>)s J, S/J oriented silicon steel plate was prepared according to a conventional method without any treatment with Δμ203 powder and used as a comparative example.

被膜性状について調べＩこところ比較例では灰色で均等
厚の被膜が形成されていたが、実施例においてはへβ２
０３粉末を（ｔイロした領域については、０．８μｍだ
り厚みの少ない）Ａルステライト被躾が形成されていた
。両者の鉄損値は下記のとおりであった。When examining the film properties, it was found that in the comparative example, a gray film of uniform thickness was formed, but in the example, β2
03 powder (the area where it was colored had a small thickness of 0.8 μm) was formed with A lusterite. The iron loss values for both were as follows.

比較例　Ｗ　１７／　５０　＝　１．０６　Ｗ　／　ｋ
ｇ実施例　Ｗ１７１５０＝　１．０２　Ｗ／ｋｇこの後
りんＩｌｉ塩系の通常上塗り」−ティングを施した場合
の鉄損値について調べたところ、それぞれ下記のとおり
であった。Comparative example W 17/50 = 1.06 W/k
gExample W17150=1.02 W/kg After this, the iron loss values when a phosphorus Ili salt-based regular overcoat was applied were investigated and the results were as follows.

比較例　Ｗ１７１５０＝　１．０６　Ｗ／ｋｇ実施例　
Ｗ１７１５０＝　１．０１　Ｗ／ｋｇざらに、これらの
試料に８００℃で２時間の歪取り焼鈍を施した場合の、
鉄Ｊｔ’ｌ値について調べｌ〔ところ下記の値が得られ
た。Comparative example W17150 = 1.06 W/kg example
W17150 = 1.01 W/kg When these samples were subjected to strain relief annealing at 800°C for 2 hours,
The iron Jt'l value was investigated and the following value was obtained.

比較例　Ｗ１７１５０　＝　１．０６　Ｗ／驕実施例　
Ｗ１７１５０＝　１．０１　Ｗ／ｋｇ実施例２ ３ｉ　：　３．２％を含有り−るけい素鋼素材を、常法
に従って厚み０．３０ｍｍの冷延鋼板としたのち、脱炭
・１次再結晶焼鈍を施し、ついでこの焼鈍板表面に焼鈍
分離剤を塗布するに先立ち、焼鈍分離剤スラリーに対し
撥水ｆｊｌを右−４るラッカーを付着量：０．０５（１
／Ｉｌ＋　２．圧延／ｊ向どなず角麿ニア５°、付着幅
：　０．５ｍｓ＋そして圧！Ｉｉｈ向の繰返し間隔３Ｉ
Ｉ１ｍの条件下に鋼板表面に線状に吹（−Ｉ　ＧＥＬ　
（Ｎ１着させたのち、その上に焼鈍分薗剤スラリーを塗
布してから加熱乾燥し、しかるのち２次Ｉ１１結晶焼鈍
ついで１２００℃。Comparative example W17150 = 1.06 W/Example
W17150 = 1.01 W/kg Example 2 A silicon steel material containing 3i: 3.2% was made into a cold-rolled steel plate with a thickness of 0.30 mm according to a conventional method, and then decarburized and primary recrystallized. Before annealing and then applying an annealing separator to the surface of the annealed plate, apply a lacquer with a water repellent fjl of -4 to the annealing separator slurry in an amount of 0.05 (1).
/Il+ 2. Rolling/J direction: 5° near corner, adhesion width: 0.5ms + and pressure! Repeat interval 3I in Iih direction
Linear blowing on the surface of the steel plate under the condition of I1m (-I GEL
(After depositing N1, an annealing bulking agent slurry was applied thereon and then heated and dried, followed by secondary I11 crystal annealing at 1200°C.

５時間の純化焼鈍を施した１゜ なお比較の！、：め、焼鈍分離剤の塗布に先立つ撥水性
物質の付猶処理のない通常の工程にＪ：って方向性１ノ
い素鋼４ｋを作成し、比較例とした。1° after 5 hours of purification annealing for comparison! As a comparative example, a raw steel 4k having a directionality of 1 was prepared using a normal process without additional treatment of a water-repellent substance prior to application of an annealing separator.

被膜す４状についＣ調べたどころ比較例では、均等厚で
灰色のフＡルスデライト被・躾が形成されていたが、実
施例に（１３い゛（は、ラッカー吹付けた領域について
【よ、０．５μｍだり厚みの少ないフォルステライ１−
被膜が形成されていた。両者の鉄損値は下記のとＪ′３
りであっ／ｌ−１１ 比較例　Ｗ　１？／　！＋０−１．０６　Ｗ　／　ｋｇ
実施例　Ｗ１７／！ｉ０−　１．０１　Ｗ／ｋｇこの後
クロム酸」偏光の通常の上塗りコーディングを施した場
合のＤ　ＩＱ　ｌ１ｆｌ［について調べたところ、それ
ぞれ下記のとおりであった。When the coating was inspected, it was found that a uniformly thick gray fulsdellite coating was formed in the comparative example, but in the example (13), the lacquer-sprayed area was Forsterei 1- with a small thickness of 0.5μm
A film was formed. The iron loss values for both are as follows and J'3
Ride/l-11 Comparative example W 1? /! +0-1.06 W/kg
Example W17/! The DIQ l1fl[ when a normal overcoating of i0-1.01 W/kg chromic acid'' polarized light was applied was investigated and the results were as follows.

比較例　Ｗ　１７／　５０＝　１．０６　Ｗ／　ｋｇ実
施例　Ｗ　１７／　５０＝　１．００　Ｗ　／　ｋｇさ
らにこれらの試料に８００℃で２時間の歪取り焼鈍を施
した場合の鉄損値について調べたところ下記のとおりで
あった。Comparative example W 17/50= 1.06 W/kgExample W 17/50= 1.00 W/kgFurthermore, the iron loss value was investigated when these samples were subjected to strain relief annealing at 800°C for 2 hours. The results were as follows.

比較例　Ｗ１７１５０　＝　１．０６　Ｗ／ｋｇ実施例
　Ｗ１７１５０＝　１．００　Ｗ／ｋｇ実施例３ ３ｉ　：　３，０％を含有するけい素鋼素材を、常法に
従って厚み０．２８ｍ１の冷延鋼板としたのち、脱炭・
１次再結晶焼鈍を施し、ついでこの焼鈍板表面にＭｏＯ
を主成分とする焼鈍分離剤を一旦塗布したのち先の細い
プラスチックの棒で、焼鈍分離剤を、圧延方向となす角
度９０°１幅１．５１．圧延方向における繰返し間隔２
＃ｌｌｌの条イシ１下に線状に除去し、ついで２次再結
晶を兼ねる１２００℃、５時間の最終仕上げ焼鈍を施し
た。なａ３焼鈍分離剤を除去づることのない通常の工程
で最終仕上げ焼鈍まで施したものを比較祠とした。Comparative example W17150 = 1.06 W/kg Example W17150 = 1.00 W/kg Example 3 A silicon steel material containing 3i: 3.0% was made into a cold rolled steel plate with a thickness of 0.28 m1 according to a conventional method. After that, decarburization
Primary recrystallization annealing is performed, and then MoO is applied to the surface of this annealed plate.
After applying the annealing separator as a main component, use a thin plastic rod to apply the annealing separator at an angle of 90 degrees with the rolling direction and a width of 1.51 mm. Repeat interval in rolling direction 2
#1ll was removed in a line under the strip 1, and then final annealing was performed at 1200° C. for 5 hours, which also served as secondary recrystallization. The comparison shrine was one that was subjected to final annealing in a normal process without removing the A3 annealing separator.

両者の被膜ｆｌ状についで調べたところ、比較例におい
ては、均等厚な灰色のフォルステライ１〜被膜が形成さ
れたが、実施例にＪ３いては焼鈍分離剤を除去した領域
につい（は厚みの小さいフォルステライト被膜が形成さ
れた。これらの鉄損値は下記のとＪ５すＣあった。When the shapes of both coatings were examined, it was found that in the comparative example, a uniformly thick gray Forsterei 1 coating was formed, but in the example J3, the area where the annealing separator was removed (was A small forsterite film was formed.These iron loss values were as follows:

比較例　Ｗ１７／　！ｉ０＝　１．（１７Ｗ／驕実施例
　Ｗ１７１５０　＝　１．０１　Ｗ／ｋｇさらにこれら
の試オ′＋１に８００°Ｃで５時間の歪取り焼鈍を施し
た場合の鉄損値について調べたところ下記の値が得られ
た１゜ 比較例　ＷＩ７〜！ｉｏ＝　１．０７　Ｗ／　ｋｇ実施
例　Ｗ１７／’！１（１−１，０１Ｗ／に８実施例４ ３ｉ　：　３．（１％を含有りる【ノい素鋼索材を、常
法に従って厚み１１．３０１１１　Ｉｌ＋の冷延鋼板と
したのち、脱炭・１次再結晶焼鈍を施し、ついで凹凸を
右づるゴムロールによっ−Ｃ鋼扱表面に焼鈍分離剤を塗
布しに０このとさ、焼鈍分離剤の塗布は、圧延方向に対
して交互に塗布領域と未塗布領域とを区画形成し、朱塗
イ５領域の幅は１．！ｉｍｍで圧延方向の繰返し間隔は
５ＩＩＩＩｎの条件Ｆに行なった。その後２次再結晶焼
鈍と１２００℃、５時間の純化焼鈍を施した。Comparative example W17/! i0=1. (17 W/Example W17150 = 1.01 W/kg Furthermore, when these test O'+1 were subjected to strain relief annealing at 800°C for 5 hours, the iron loss value was investigated, and the following values were obtained. Comparative example WI7~!io = 1.07 W/ kg Example W17/'!1 (1-1,01 W/8 Example 4 3i: 3. (containing 1% The steel cable material was made into a cold-rolled steel plate with a thickness of 11.30111 Il+ according to a conventional method, and then subjected to decarburization and primary recrystallization annealing, and then an annealing separator was applied to the -C steel surface using a rubber roll that smoothed the irregularities. In this case, the annealing separator was applied by forming coated areas and uncoated areas alternately in the rolling direction, and the width of the red coating area was 1.!imm, and the annealing separation agent was applied repeatedly in the rolling direction. The interval was 5IIIn under condition F. Thereafter, secondary recrystallization annealing and purification annealing at 1200° C. for 5 hours were performed.

なお比較のため、フォルスプライト被膜を鋼板全面に一
様に塗布する通常の製造工程によつＣ方向性（プい素鋼
板を作成し、比較例とした。For comparison, a C-direction steel sheet was prepared by a normal manufacturing process in which a false sprite coating was uniformly applied to the entire surface of the steel sheet, and this was used as a comparative example.

両者の被膜性状についで調べたところ比較例では均等厚
な灰色のフォルスプライト被膜が形成され、実施例にお
いでは焼鈍分子ｉｌｌ剤を未塗布した領域については、
厚みの薄いフォルステライト被膜が形成されていた。こ
れらの鉄損Ｉｆｆは下記のとおりであった。When the properties of both films were investigated, a uniformly thick gray false sprite film was formed in the comparative example, and in the example, the area where the annealing molecular ill agent was not applied was as follows.
A thin forsterite film was formed. These iron losses Iff were as follows.

比較例　Ｗ１７１５０　＝　１．０５　Ｗ／ｋｇ実施例
　Ｗ１７１５０＝　１．０３　Ｗ／ｋｇさらにこれらの
試料に８００°Ｃで１１１４間の歪取り焼鈍を１進じた
場合の鉄損値についＣ調べたところ下記の値が得られた
。Comparative example W17150 = 1.05 W/kg Example W17150 = 1.03 W/kg Furthermore, C was investigated for the iron loss value when these samples were subjected to strain relief annealing at 800°C between 1114 and 1. The following values were obtained.

比較例　Ｗ　１７／　５０＝　１．０８　Ｗ　／　ｋｇ
実施例　Ｗ　１７／　５０＝　１．０３　Ｗ　／　ｋｇ
実施例５ Ｓｉ　：　３．２％を含イ１゛りる（ノい素鋼索材を、
常法に従って厚み０．３０ｍｍの冷延の鋼板とし、つい
で脱炭・１次再結晶焼鈍を施し、ついで焼鈍分離剤を塗
布覆るに先立ち、鋼板表面に鋼中３ｉに対して酸化剤で
あるＦｅＯを、０．５ｇ　７ｍ　’の範囲で圧延方向と
なり角爪９０°１幅：２１１１ｍ、圧延方向における繰
返し間ｌ１ｒｉｉ：　１（１１１１１１の条（’ｌ下に
線状に塗布したのち、焼鈍分離剤を−ｔ　Ｉ／）　、Ｊ
二に塗装ＩＩシ、しかるのち２次丙結晶焼鈍−）いＣ１
２００℃、５１１；’ｉ間の純化焼鈍を°施した１、な
（１３比較例のため、焼鈍分離剤の塗布に先立ち酸化剤
の塗（１ｉを行わない通常の工程によって方向性（°Ｊ
い素鋼板を作成し、比較例とした。Comparative example W 17/50= 1.08 W/kg
Example W 17/50= 1.03 W/kg
Example 5 Si: 1 ml containing 3.2% (no raw steel cable material,
A cold-rolled steel plate with a thickness of 0.30 mm is prepared according to a conventional method, and then subjected to decarburization and primary recrystallization annealing. Then, before coating with an annealing separator, FeO, which is an oxidizing agent for 3i in steel, is applied to the surface of the steel plate. in the rolling direction in the range of 0.5 g 7 m', square claw 90° 1 width: 2111 m, repetition interval in the rolling direction l1rii: 1 (111111 strips ('1) After applying the annealing separator in a linear manner under -t I/), J
Second, paint II, then secondary C crystal annealing -) C1
1 and 13 were subjected to purification annealing at 200°C between 511 and 'i.
A steel plate was prepared and used as a comparative example.

鉄損値は土間のど、１３すＣ（ら・）ｌＪ０比較例　Ｗ
　１７／　！１０＝−１，０４Ｗ　／　ｋｇ実施例　Ｗ
　１７１．’　！ｉｏ＝　０．９９　Ｗ　ｌ　ｋｇさら
に、８００℃、２＋１ｉ′Ｉ間の１１≧取り焼鈍を施し
た後の鉄損（ｌｆｉについて調べｋどころ下記の値が得
られた。Iron loss value is earth floor, 13sC(ra・)lJ0 comparison example W
17/! 10=-1,04W/kgExample W
171. '! io = 0.99 W l kg Further, the iron loss (lfi) after annealing at 800°C between 2+1i'I was investigated and the following value was obtained.

比較例　Ｗ　１７／　！＋０　＝　１．０４　、Ｗ　、
／　ｋｇ実施例　Ｗ１７１５０＝　０．９呵ＩＷ／ｋｇ
実施例６ ３ｉ　：　３．２％を含有するけい素鋼索材を、常法に
従って厚み０．２０ｍｍの冷延鋼板としたのら脱炭・１
次再結晶焼鈍を施し、ついぐ焼鈍分離剤を塗布するに先
立ち、焼鈍分離剤スラリーに対して撥水性を有する油性
ペイントを、印刷法によって下記の要領で鋼板表面に０
．０’＋ｇ／ｍ　２の量印刷した。Comparative example W 17/! +0 = 1.04, W,
/ kg Example W17150 = 0.9 IW/kg
Example 6 3i: Silicon steel cable material containing 3.2% was made into a cold-rolled steel plate with a thickness of 0.20 mm according to a conventional method, and decarburization/1
Before performing the next recrystallization annealing and then applying an annealing separator, an oil-based paint that is water repellent to the annealing separator slurry is applied to the surface of the steel plate using the printing method as described below.
．． A quantity of 0'+g/m2 was printed.

印刷した領域が圧延り向とｈ寸角瓜９０°１幅０．３１
１１ｎｌ非連続線状列の点と点との間隔：　０．３ｍｎ
＋、そして印刷領域の圧延方向に対す゛る間隔：３ｎ＋
ｎ＋。The printed area corresponds to the rolling direction and h dimension 90° 1 width 0.31
Distance between points in 11nl discontinuous linear array: 0.3mn
+, and the distance between the printing area in the rolling direction: 3n+
n+.

その後、焼鈍分離剤を塗布してから加熱乾燥し、しかる
のち２次再結晶焼鈍を兼ねる１２００℃、１０時間の純
化焼鈍を施した。なａ３比較のため上記したような撥水
性物質印刷処理を施さない通常の工程により方向性けい
素鋼板を作成し、比較例とした。Thereafter, an annealing separator was applied and then heated and dried, followed by purification annealing at 1200° C. for 10 hours, which also served as secondary recrystallization annealing. A3 For comparison, a grain-oriented silicon steel plate was prepared by a normal process without the water-repellent material printing treatment as described above, and was used as a comparative example.

両者の鉄損値は下記のとおりであった。The iron loss values for both were as follows.

比較例　Ｗ　１７／　５０＝　０．９２　Ｗ　／　ｋｇ
実施例Ｗ　１７／　５０＝　０．８７　Ｗ　／　ｋｇさ
らに８００℃、２時間の歪取り焼鈍を施した後の鉄損値
に′）い（は下記の値が１ｑられた。Comparative example W 17/50=0.92 W/kg
Example W 17/50=0.87 W/kgThe following value was added to the iron loss value after further strain relief annealing at 800°C for 2 hours.

比較例　Ｗ　１７／　！ｉｏ　＝　０．９２　Ｗ／　ｋ
ｇ実施例　Ｗ　１７．／　！ｉ０　＝　０．８７　Ｗ　
／　ｋｇ実施例７ ３ｉ　：　３．２％を含イｊ′ＩＪる（〕い素素鋼材を
、７１法に従って厚み０．３０ｍｎ＋の冷延鋼板とした
のち、脱炭・１次■ｉ」結晶力２鈍を施し、ついで鋼板
表面にＭｇＯを主成分とする焼鈍分離剤を塗布し／ｊの
ち、２次再結晶焼鈍ついぐ１２００℃、５時間の高温純
化焼鈍を施しＣ表面に灰色で均一なフォルステライト被
膜をそなえるＩＪ向ｔＩＩ　ＩＪい素鋼板を作成しｌこ
。Comparative example W 17/! io = 0.92W/k
g Example W 17. /! i0 = 0.87W
/ kg Example 7 3i: A raw steel material containing 3.2% was made into a cold-rolled steel sheet with a thickness of 0.30 mm+ according to the 71 method, and then decarburized and primary ■i'' crystals were formed. After applying an annealing separator mainly composed of MgO to the surface of the steel sheet, secondary recrystallization annealing was performed, followed by high-temperature purification annealing at 1200°C for 5 hours, and the surface of the steel sheet was uniformly gray. A raw steel plate for IJ with a strong forsterite coating was created.

この鋼板の鉄１ｔ、１値はＷ１７１５０で１．０６Ｗ、
／ｋｇであった。1 ton of iron of this steel plate, 1 value is W17150 and 1.06W,
/kg.

次に先の細い鉄↑１にｌｊＹ、　＜圧力をか【ノＣ線引
きりることによる、フＡルスｉライｌ〜被躾の除去方法
により、深さ：０，５μ川で幅０．５ｎ＋ｍの圧延方向
と９０°の角度をなづ線状フォルステライト被膜の減厚
領域を形成し１．：。なお圧延方向におけるこの領域の
間隔は（ｉｍｍとした。Next, apply pressure to the thin iron ↑ 1. By drawing a line with a thin tip, draw a full A line to a depth of 0.5 μ and a width of 0.5 n + m. Forming a thinned region of linear forsterite coating at an angle of 90° with the rolling direction of 1. :. Note that the interval between these regions in the rolling direction was set as (imm).

この結果、鋼板の鉄損はＷ１７１５０てせ１．０２　Ｗ
／　ｋｇとなった。なおこの鋼板にさらに８５０℃、２
時間の歪取り焼鈍を施した後の鉄損値はＷ１７１５０で
１．Ｏ１Ｗ／ｋｇであった。As a result, the iron loss of the steel plate is W17150 1.02 W
/ kg. Furthermore, this steel plate was further heated at 850℃ for 2
The iron loss value after time strain relief annealing is 1. It was O1W/kg.

発明の効果 かくしてこの発明によれば、歪取り焼鈍を施した場合で
あってｂ特性が劣化しない鉄損特性に優れた方向性【）
い素鋼板を得ることができ、右利である。Effects of the Invention Thus, according to the present invention, the directionality is excellent in iron loss characteristics without deterioration of b characteristics even when subjected to strain relief annealing.
It is advantageous to be able to obtain raw steel sheets.

【図面の簡単な説明】[Brief explanation of drawings]

第１図（イ）、（ロ）、および（ハ）はそれぞれ、フォ
ルステライト被膜に区画形成した該被膜の層厚領域の形
状、圧延方向に対する傾き具合および間隔の測定要領を
示した図表、 第２図は、線状層厚領域が圧延方向となり角度が、鉄損
特性に及は一４影響を示したグラフ、第３図は、異尽領
域の厚み差と鉄損値との関係を示したグラフ、 第４図は、層厚領域の幅と鉄損値との関係を示したグラ
フ、 第５図は、層厚領域の間隔と鉄損値との関係について示
したグラフＣある。 特狛出願人　川崎製鉄株式会社Figures 1 (a), (b), and (c) are diagrams showing the shape, inclination with respect to the rolling direction, and interval measurement procedures of the thickness regions of the forsterite film, respectively. Figure 2 is a graph showing how the linear layer thickness region is in the rolling direction and the angle has an effect on the iron loss characteristics. Figure 3 is a graph showing the relationship between the thickness difference in the uneven thickness region and the iron loss value. FIG. 4 is a graph showing the relationship between the width of the layer thickness region and the iron loss value, and FIG. 5 is a graph C showing the relationship between the interval of the layer thickness region and the iron loss value. Special Koma Applicant: Kawasaki Steel Corporation

Claims (1)

【特許請求の範囲】 １、地鉄表層部に塑ＩＩｌ歪域がみられないフＡルスー
フフーｒ１・被膜イー１きの方向性けい素鋼板であって
、該ノＡルスフライト被膜が異厚領域を有りることを特
徴とりる、歪取り焼鈍によって特１イＩが劣化しくＫい
低鉄損の方向性けい素鋼板。 ２．７Ａルスデライｉ〜被膜の異厚領域が、連続または
非連続の線状凹凸領域である特許請求の範囲第１１３″
ｌ記載のｈ向性ｔＪい素鋼板。 ３、連続または非連続の線状凹凸領域が、鋼板のロー延
り向にλＪＬＧＯ°〜９０°Ｑ角亀をなずものである特
許請求の範囲第１または２項記載の方向性ｔＪいＳｎ４
板。 ４、フＡルステライト被膜異厚領域の厚み差が、０．３
μｍ　１；／、　ｌである特許請求の範囲第１．２また
は３項記載の方向性番プい素鋼板。 ５、含けい素鋼スラブを熱間１１延して得られた熱延板
に、１回または中間焼鈍を挾む２回の冷間圧延を施して
最終板厚としたのち、脱炭・１次再結晶焼鈍を施し、つ
いで鋼板表面にＭ（１０を主成分とする焼鈍弁＊１剤を
塗布してから２次再結晶焼鈍および純化焼鈍をｆｉ　ｔ
一連の工程よりなる方向性りい素鋼板の製造方法におい
て、 脱炭・１次再結晶後の鋼板表向への焼鈍分離剤の塗布処
理につき、該分離剤を局所的に未塗布または一様塗布後
局所的に除去することにより、純化焼鈍後、鋼板表面に
被成づるフォルステライト被膜に異厚領域を形成させる
ことを特徴とづる、歪取り焼鈍によって特性が劣化しな
い低鉄損の方向性りい素鋼板の製造方法。 ６、含けい素鋼スラブを熱間圧延して得られた・熱延板
に、１回または中間焼鈍を挾む２回の冷間圧延を施して
最終板厚としたのち、脱炭・１次再結晶焼鈍を施し、つ
いで鋼板表面にＭｇＯを主成分とりる焼鈍分離剤を塗布
してから２次再結晶焼鈍および純化焼鈍を施°り一連の
工程よりなる方向性けい素鋼板のＩｌｌｌｌ法において
、 焼鈍分離剤の塗イｌｉに先立って脱炭・１次再結晶焼鈍
後の鋼板表面に、該分離剤と鋼板表面ザブスケニル小（
１）　Ｓ　ｉ　０２との反応を阻害す５る物質を１（１
／ｎ’以下の範囲で局所的に（＝Ｊ盾さＵることにより
、純化焼鈍後、鋼板表面に被成りる〕Ａルステライト被
膜に異厚領域を形成さＵることを特徴どする、歪取り焼
鈍によって特性が劣化しない低鉄損の方向性りい素鋼板
の製〕Δ／Ｊ法、。 ７、含【ノい素鋼スラブを熱間圧延して得られた熱延板
に、１゛回ま是は中間焼鈍を挾む２回の冷間圧延を施し
゛Ｃ最終板厚としたのち、脱炭・１次再結晶焼鈍を施し
、ついで鋼板表面にＭＯＯを主成分とする焼鈍分離剤を
塗布してから２次１９結晶焼鈍Ｊ３よび純化焼鈍を掩ず
一連の■稈よりなる方向性【ノい素鋼板の製造方法にお
いて、 焼鈍分離剤の塗布に先立って脱炭・１次再結晶焼鈍後の
鋼板表面に、焼鈍分離剤スラリーの撥水性物質を、０．
Ｉｇ　７ｍ　２以下の範囲で局所的にイ」着さけること
により、純化焼鈍後、鋼板表面に被成づるフォルステ°
ライト被膜に異厚領域を形成させることを特徴とする、
歪取り焼鈍によって特性が劣化しない低鉄損の方向性け
い素鋼板の製造方法。 ８、含けい素鋼スラブを熱間圧延して得られた熱延板に
、１回または中間焼鈍を挾む２回の冷間圧延を施して最
終板厚どしたのち、脱炭・１次再結晶焼鈍を施し、つい
で鋼板表面にＭ（ＪＯを主成分どする焼鈍分離剤を塗布
してから２次再結晶焼鈍および純化焼鈍を施す一連の工
程よりなる方向性けい素鋼板の製造方法において、 焼鈍分離剤の塗布に先立つ−Ｃ脱炭・１次再結晶焼鈍後
の鋼板表面に、鋼中Ｓｉに対する酸化剤を２！Ｊ　／ｓ
＋　２以下の範囲で局所的に１４着さ２せることにより
、純化焼鈍後、）Ａルステライト被膜に異厚領域を形成
させることを特徴どＭる、歪取り焼鈍によって特性が劣
化しない低鉄１１の方向＋ｇＧＩＪい素鋼板の製造方法
。 ９、含けい素鋼スラブを熱間圧延して得られた熱延板に
、１回または中間焼鈍を挾む２回の冷間圧延を施しＣ最
終板厚としたのち、脱炭・１次７Ｑ帖品焼鈍を施し、つ
いで鋼板表面にｆｖｌｏＯを主成分とり−る焼鈍分離剤
を塗布してから２次１３結晶焼鈍（１３よび純化焼鈍を
施り一連の工程よりなる方向性（〕い索鋼板の製造方法
にａりい（、 ）Ａルスアライト被膜形成後、鋼板の地鉄内部に塑性歪
を尋人ηることなしに、局所的に該被膜の一部を除゛六
りることにより、フォルステライ１へ被膜にｋｌ／厚領
域を形成さＵることを特徴どりる、歪取り焼鈍によって
特性が劣化しない（ＩＸ鉄損の方向性けい素鋼板の製造
方法。[Scope of Claims] 1. A grain-oriented silicon steel sheet with a full Arusuffu r1/coating E1 in which no plastic II strain region is observed in the surface layer of the base steel, wherein the non-Arusfrite coating has a different thickness region. A grain-oriented silicon steel sheet with low iron loss that does not deteriorate due to strain relief annealing. 2.7A Lusdelai i ~ Claim 113'' in which the region of different thickness of the coating is a continuous or discontinuous linear uneven region
The h-tropic tJ raw steel sheet described in l. 3. Directionality tJSn4 according to claim 1 or 2, wherein the continuous or discontinuous linear uneven region has a λJLGO° to 90°Q angle turtle in the rolling direction of the steel plate.
Board. 4. The thickness difference in the A-fulsterite coating different thickness region is 0.3
The grain-oriented steel sheet according to claim 1.2 or 3, wherein μm is 1;/, l. 5. A hot-rolled sheet obtained by hot-rolling a silicon-containing steel slab is subjected to cold rolling once or twice with intermediate annealing to obtain the final thickness, and then decarburized and Perform secondary recrystallization annealing, then apply an annealing valve*1 agent containing M(10 as the main component) to the surface of the steel sheet, and then perform secondary recrystallization annealing and purification annealing.
In a method for producing a grain-oriented silicon steel sheet that includes a series of steps, in the process of applying an annealing separator to the surface of the steel sheet after decarburization and primary recrystallization, the separator is not applied locally or uniformly. By locally removing it after application, a region of different thickness is formed in the forsterite film that forms on the surface of the steel sheet after purification annealing.It is characterized by a low core loss directionality that does not deteriorate its characteristics due to strain relief annealing. Manufacturing method of silicon steel sheet. 6. The hot-rolled plate obtained by hot rolling a silicon-containing steel slab is subjected to cold rolling once or twice with intermediate annealing to achieve the final thickness, and then decarburized and 1 Illll method for grain-oriented silicon steel sheets, which consists of a series of steps: performing secondary recrystallization annealing, then applying an annealing separator containing MgO as a main component to the surface of the steel sheet, and then performing secondary recrystallization annealing and purification annealing. In the process, prior to applying the annealing separator, the separator and the steel sheet surface Zabskenyl (
1) Add 5 substances that inhibit the reaction with S i 02 to 1 (1
/n' (= formed on the surface of the steel sheet after purification annealing by shielding) A strain characterized by the formation of regions of different thickness in the lusterite film. [Production of grain-oriented silicon steel sheet with low iron loss whose properties do not deteriorate by annealing] Δ/J method. 7. A hot rolled sheet obtained by hot rolling a raw steel slab containing゛The steel sheet is cold-rolled twice with an intermediate annealing in between to achieve the final plate thickness, then subjected to decarburization and primary recrystallization annealing, and then subjected to annealing separation with MOO as the main component on the surface of the steel sheet. After applying the annealing agent, the secondary 19-crystal annealing J3 and purification annealing are performed. A water-repellent substance of annealing separator slurry is applied to the surface of the steel sheet after crystal annealing.
By locally depositing Ig in a range of 7 m2 or less, the forste° that forms on the steel plate surface after purification annealing is reduced.
characterized by forming a region of different thickness in the light film,
A method for manufacturing a grain-oriented silicon steel sheet with low iron loss whose properties do not deteriorate due to strain relief annealing. 8. Hot-rolled sheets obtained by hot-rolling silicon-containing steel slabs are cold-rolled once or twice with intermediate annealing to achieve the final thickness, and then decarburized and subjected to primary In a method for producing a grain-oriented silicon steel sheet, which comprises a series of steps of performing recrystallization annealing, then applying an annealing separator containing M (JO as the main component) to the surface of the steel sheet, and then performing secondary recrystallization annealing and purification annealing. , An oxidizing agent for Si in steel was applied to the surface of the steel sheet after -C decarburization and primary recrystallization annealing prior to application of an annealing separator at a rate of 2!J/s.
A low iron 11 whose characteristics do not deteriorate by strain relief annealing, characterized by forming a region of different thickness in the lusterite film after purification annealing by locally depositing 14 in a range of + 2 or less. direction + gGIJ method for producing raw steel sheet. 9. A hot-rolled plate obtained by hot rolling a silicon-containing steel slab is subjected to cold rolling once or twice with intermediate annealing to obtain a final plate thickness of C, and then subjected to decarburization and primary rolling. 7Q standard annealing is applied, and then an annealing separator containing fvloO as the main component is applied to the surface of the steel sheet, followed by secondary 13 crystal annealing (13 and purification annealing), which is a series of process steps. A method for manufacturing a steel plate is that after forming a rusualite film, a part of the film is locally removed without creating plastic strain inside the base steel of the steel plate. , a method for producing grain-oriented silicon steel sheet with IX core loss, characterized by forming a kl/thick region in the coating on Forsterei 1, and whose properties are not deteriorated by strain relief annealing.