JP2647323B2 - Manufacturing method of grain-oriented electrical steel sheet with low iron loss - Google Patents

Manufacturing method of grain-oriented electrical steel sheet with low iron loss

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Publication number
JP2647323B2
JP2647323B2 JP5003440A JP344093A JP2647323B2 JP 2647323 B2 JP2647323 B2 JP 2647323B2 JP 5003440 A JP5003440 A JP 5003440A JP 344093 A JP344093 A JP 344093A JP 2647323 B2 JP2647323 B2 JP 2647323B2
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JP
Japan
Prior art keywords
steel sheet
grain
annealing
electrical steel
oriented electrical
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JP5003440A
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Japanese (ja)
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JPH06212263A (en
Inventor
健司 小菅
美樹雄 伊藤
尚 吉村
晴雄 深沢
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新日本製鐵株式会社
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Description

【発明の詳細な説明】DETAILED DESCRIPTION OF THE INVENTION

【0001】[0001]

【産業上の利用分野】本発明は、2.5〜7.0%のS
iを含み、冷間圧延での生産性が優れ、かつ低い鉄損を
もつ一方向性電磁鋼板の製造方法を提供するものであ
る。
The present invention relates to a method for producing 2.5-7.0% S
It is an object of the present invention to provide a method for producing a grain-oriented electrical steel sheet having excellent cold-rolling productivity and low iron loss.

【0002】[0002]

【従来の技術】一般に、一方向性電磁鋼板の磁気特性は
鉄損特性と励磁特性の両方で評価される。励磁特性を高
めることは設計磁束密度を高める機器の小型化に有効で
ある。一方鉄損特性を少なくすることは、電気機器とし
て使用する際、熱エネルギーとして失われるものを少な
くし、消費電力を節約できる点で有効である。しかし、
一方向性電磁鋼板は2.5〜7.0%のSiを含有し、
一般の鋼材に比べて脆く破断し易いだけでなく、変形抵
抗も極めて高いため、冷間圧延時は一般にロール径が約
100mmφ前後と小さいゼンジミアミルのようなリバー
スミルを用い、圧延速度が500mpm 前後の非常に低速
で圧延する必要があった。そのため、一方向の高速で圧
延する複数スタンドのタンデムミルに比べて非常に生産
性が悪かった。
2. Description of the Related Art Generally, the magnetic properties of a grain-oriented electrical steel sheet are evaluated based on both iron loss properties and excitation properties. Increasing the excitation characteristics is effective in reducing the size of equipment that increases the design magnetic flux density. On the other hand, reducing the iron loss characteristics is effective in that when it is used as an electric device, heat loss is reduced and power consumption can be saved. But,
The grain-oriented electrical steel sheet contains 2.5 to 7.0% of Si,
Not only is it brittle and fragile than ordinary steel materials, it is also extremely high in deformation resistance. Therefore, during cold rolling, a roll mill is generally used, such as a Sendzimir mill having a small roll diameter of about 100 mmφ, and a rolling speed of about 500 mpm. It had to be rolled at a very low speed. Therefore, the productivity was extremely low as compared with a multi-stand tandem mill that performs high-speed rolling in one direction.

【0003】タンデムミルによる一方向性電磁鋼板の製
造方法としては、特開平2−173210号に開示され
ているように、最終スタンドでの圧下率配分を制限した
方法がある。しかし、この方法は、鋼板表面粗さの低減
を求めたものであり、充分な磁気特性が得られないこと
が判明した。
As a method for producing a grain-oriented electrical steel sheet using a tandem mill, there is a method in which the reduction ratio distribution at the final stand is restricted, as disclosed in Japanese Patent Application Laid-Open No. 2-173210. However, this method seeks to reduce the surface roughness of the steel sheet, and it has been found that sufficient magnetic properties cannot be obtained.

【0004】[0004]

【発明が解決しようとする課題】最近、生産性の向上、
品質・歩留りの向上および省力化の観点から、方向性電
磁鋼板のような難圧延材も、高効率のタンデムミルで生
産することを目指してきた。しかし、従来の一方向性電
磁鋼板を製造する方法だけでは、特に高級電磁鋼板にお
いて磁気特性が非常にばらつき不安定で、良好でないと
いう問題点があった。本発明は、それを解決する製造方
法を提供するものである。
SUMMARY OF THE INVENTION Recently, productivity improvement,
From the viewpoint of improving quality and yield and saving labor, it has been aimed to produce hard-to-roll materials such as grain-oriented electrical steel sheets with a high-efficiency tandem mill. However, the conventional method of manufacturing a grain-oriented electrical steel sheet alone has a problem that the magnetic properties of the high-grade electrical steel sheet are very unstable and unstable. The present invention provides a manufacturing method for solving the problem.

【0005】[0005]

【課題を解決するための手段】本発明は、重量でC:
0.10%以下、Si:2.5〜7.0%ならびに通常
のインヒビター成分を含み、残余はFeおよび不可避的
不純物よりなる一方向性電磁鋼熱延板に熱延板焼鈍を施
し、圧下率50%以上の冷間圧延を施し、脱炭焼鈍した
後、最終仕上焼鈍を施して一方向性電磁鋼板を製造する
方法において、上記冷間圧延を、複数スタンドのタンデ
ムミルによって行い、かつ最終製品厚まで圧延されたス
トリップを、脱炭焼鈍する前に80℃/秒以上の加熱速
度で700℃以上の温度へ加熱処理することにより、生
産性に優れ、低い鉄損をもつ一方向性電磁鋼板の製造方
法が得られることを見い出した。
SUMMARY OF THE INVENTION The present invention provides a C:
0.10% or less, Si: 2.5 to 7.0%, containing a usual inhibitor component, the balance being a unidirectional electromagnetic steel hot-rolled steel sheet consisting of Fe and unavoidable impurities, subjected to hot-rolled sheet annealing, In a method for producing a grain-oriented electrical steel sheet by performing cold rolling at a rate of 50% or more, decarburizing annealing, and then performing final finishing annealing, the cold rolling is performed by a tandem mill having a plurality of stands, and By heating the strip rolled to the product thickness to a temperature of 700 ° C or more at a heating rate of 80 ° C / sec or more before decarburizing annealing, a unidirectional electromagnetic coil with excellent productivity and low iron loss is obtained. It has been found that a method for manufacturing a steel sheet can be obtained.

【0006】以下に本発明を詳細に説明する。一方向性
電磁鋼板は、その製造工程の最終焼鈍中に二次再結晶を
充分に起こさせ、所謂ゴス集合組織を得ることにより製
造できる。このゴス集合組織を得るためには、一次再結
晶粒の成長粗大化を抑制し、(110)〈001〉方位
の再結晶粒のみを或る温度範囲で選択的に成長させる。
つまり、二次再結晶させるような素地を作ってやること
が必要である。そのためには、素材にMnS,AlN,
Cu2 S等の微細な介在物が一次再結晶粒の成長の抑制
材(インヒビター)として、均一に分散していなければ
ならない。さらに、一次再結晶の段階で、(110)面
方位再結晶粒をできるだけ増やしてやる必要がある。
Hereinafter, the present invention will be described in detail. The grain-oriented electrical steel sheet can be manufactured by sufficiently causing secondary recrystallization during the final annealing in the manufacturing process to obtain a so-called Goss texture. In order to obtain this Goss texture, coarsening of primary recrystallized grains is suppressed, and only recrystallized grains of the (110) <001> orientation are selectively grown in a certain temperature range.
In other words, it is necessary to make a base material for secondary recrystallization. To do so, the material must be MnS, AlN,
Fine inclusions such as Cu 2 S must be uniformly dispersed as an inhibitor of the growth of primary recrystallized grains. Furthermore, in the stage of primary recrystallization, it is necessary to increase the (110) plane recrystallized grains as much as possible.

【0007】しかし、タンデムミルによる一方向の圧延
では、通常圧延と比較して一次再結晶後の(110)面
方位再結晶粒が、従来のリバース圧延に比べて、あまり
多くないということが判った。そこで、タンデムミルを
前提とした一次再結晶組織の改善について、検討を重ね
た結果、最終製品厚まで圧延されたストリップを、脱炭
焼鈍する直前に80℃/秒以上の加熱速度で700℃以
上の温度へ加熱処理することにより、良好な磁気特性を
有する一方向性電磁鋼板を得ることが可能なことを突き
止めた。
However, in the unidirectional rolling by the tandem mill, it has been found that the (110) plane recrystallized grains after the primary recrystallization are not so many as compared with the conventional reverse rolling. Was. Therefore, as a result of repeated studies on the improvement of the primary recrystallization structure on the assumption of a tandem mill, the strip rolled to the final product thickness was heated at a heating rate of at least 80 ° C./sec to 700 ° C. or more immediately before decarburizing annealing. It was ascertained that a heat-treated steel sheet having a good magnetic property can be obtained by performing a heat treatment at a temperature of.

【0008】[0008]

【作用】次に本発明において、鋼組成および製造条件を
前記のように限定した理由を、詳細に説明する。この鋼
成分の限定理由は下記のとおりである。Cについての上
限0.10%は、これ以上多くなると脱炭所要時間が長
くなり、経済的に不利となるので限定した。Siは鉄損
を良くするために下限を2.5%とするが、多すぎると
冷間圧延の際に割れ易く加工が困難となるので上限を
7.0%とする。
Next, the reason why the steel composition and the manufacturing conditions are limited as described above in the present invention will be described in detail. The reasons for limiting the steel components are as follows. The upper limit of 0.10% for C is limited because if it is more than this, the time required for decarburization becomes longer and it is economically disadvantageous. The lower limit of Si is set to 2.5% in order to improve iron loss, but if it is too large, it is likely to break during cold rolling and processing becomes difficult, so the upper limit is set to 7.0%.

【0009】さらに、一方向性電磁鋼板を製造するため
に、通常のインヒビター成分として以下の成分元素を添
加することが好ましい。インヒビターとしてMnSを利
用する場合は、MnとSを添加する。MnはMnSの適
当な分散状態を得るため、0.02〜0.15%が望ま
しい。SはMnS,(Mn・Fe)Sを形成するために
必要な元素で、適当な分散状態を得るため、0.001
〜0.05%が望ましい。さらに、インヒビターとして
AlNを利用する場合は、酸可溶性AlとNを添加す
る。酸可溶性Al,AlNの適正な分散状態を得るため
0.01〜0.04%が望ましい。Nも、AlNの適正
な分散状態を得るため0.003〜0.02%が望まし
い。その他、Cu,Sn,Sb,Cr,Biはインヒビ
ターを強くする目的で1.0%以下において少なくとも
1種添加しても良い。
Further, in order to produce a grain-oriented electrical steel sheet, it is preferable to add the following component elements as ordinary inhibitor components. When MnS is used as an inhibitor, Mn and S are added. Mn is desirably 0.02 to 0.15% in order to obtain an appropriate dispersion state of MnS. S is an element necessary for forming MnS and (Mn · Fe) S.
~ 0.05% is desirable. Further, when AlN is used as an inhibitor, acid-soluble Al and N are added. In order to obtain an appropriate dispersion state of acid-soluble Al and AlN, 0.01 to 0.04% is desirable. N is also preferably 0.003 to 0.02% in order to obtain a proper dispersion state of AlN. In addition, at least one of Cu, Sn, Sb, Cr and Bi may be added at 1.0% or less for the purpose of strengthening the inhibitor.

【0010】次に、上記の溶鋼を通常の鋳塊鋳造法また
は連続鋳造法、熱間圧延により中間厚のストリップを得
る。この時ストリップ鋳造法も本発明に適用することも
可能である。さらに、インヒビターとして窒化物を必要
とする場合は、AlN等の析出のために950〜120
0℃で30秒〜30分の中間焼鈍を行うことが望まし
い。
Next, the above-mentioned molten steel is subjected to a usual ingot casting method or a continuous casting method, and hot-rolled to obtain a strip having an intermediate thickness. At this time, the strip casting method can also be applied to the present invention. Further, when a nitride is required as an inhibitor, 950 to 120 is required for precipitation of AlN or the like.
It is desirable to perform intermediate annealing at 0 ° C. for 30 seconds to 30 minutes.

【0011】次に、1回の圧延により最終製品厚のスト
リップを得る。この時の圧下率は高いゴス集積度をもつ
製品を得るため、圧下率50%以上が望ましい。下限5
0%はこれ以下では必要なゴス核が得られないからであ
る。この時の冷間圧延方法として、生産性を向上させる
ため、複数スタンドのタンデムミルを用いる。この時の
ロール径は、脆性材の圧延に安定性を与えるため、でき
れば600mmφ以下のものが良い。
Next, a strip having a final product thickness is obtained by one rolling. The rolling reduction at this time is desirably 50% or more in order to obtain a product having a high Goss integration degree. Lower limit 5
If the value is less than 0%, a necessary Goss nucleus cannot be obtained. As a cold rolling method at this time, a tandem mill having a plurality of stands is used to improve productivity. The roll diameter at this time is preferably 600 mmφ or less, if possible, in order to impart stability to the rolling of the brittle material.

【0012】以上、最終製品厚まで圧延されたストリッ
プに加熱処理を施す。まず、ストリップを80℃/秒以
上の加熱速度で700℃以上の温度へ急速加熱する。こ
の時の加熱速度の下限80℃/秒は、これ以下では二次
再結晶の核となる一次再結晶後での(110)〈00
1〉方位粒が減少し、微細な二次再結晶粒が得られない
ので限定した。また、下限700℃は、これ以下では再
結晶が開始されないので限定した。図1に各製造方法で
の一次再結晶後の(110)面強度を示す。
As described above, the strip rolled to the final product thickness is subjected to a heat treatment. First, the strip is rapidly heated to a temperature of 700 ° C. or more at a heating rate of 80 ° C./sec or more. The lower limit of the heating rate at this time, 80 ° C./sec, is below (110) <00 after primary recrystallization, which is the nucleus of secondary recrystallization.
1) The orientation grain size was reduced, and fine secondary recrystallized grains could not be obtained. The lower limit of 700 ° C. was limited because recrystallization does not start below this temperature. FIG. 1 shows the (110) plane strength after primary recrystallization in each manufacturing method.

【0013】これは、2.2mmの熱延板から0.27mm
厚のストリップを冷間圧延する際、従来のリバース圧延
(ゼンジミアミル)による方法、タンデム圧延による方
法を示す。生産性を向上させるためタンデム圧延を行う
と(110)面強度が低下してしまう。そこで最終板厚
まで圧延されたストリップは昇温速度90℃/秒で85
0℃まで急速加熱すると(110)面強度が増加する。
なお、この急速加熱処理は、皮膜形成等の問題から、で
きるだけ還元雰囲気、あるいは無酸化雰囲気中で実施す
ることが望ましい。
[0013] This is 0.27 mm from a 2.2 mm hot rolled sheet.
When a thick strip is cold rolled, a conventional reverse rolling (Senzimir mill) method and a tandem rolling method will be described. When tandem rolling is performed to improve productivity, the (110) plane strength is reduced. Therefore, the strip rolled to the final thickness is 85 ° C. at a heating rate of 90 ° C./sec.
Rapid heating to 0 ° C. increases the (110) plane strength.
Note that it is desirable to perform this rapid heating treatment in a reducing atmosphere or a non-oxidizing atmosphere as much as possible in view of problems such as film formation.

【0014】なお、上記の急速加熱処理は、次に施され
る脱炭焼鈍前に行われても、脱炭焼鈍の加熱段階として
脱炭焼鈍工程に組み込むことも可能である。この後は、
湿水素雰囲気中で脱炭焼鈍を行う、この時製品での磁気
特性を劣化させないため炭素は0.005%以下に低減
されなければならない。ここで、熱延でのスラブ加熱温
度が低く、AlNのみをインヒビターとして利用する場
合は、アンモニア雰囲気中で窒化処理を付加することも
ある。さらに、MgO等の焼鈍分離剤を塗布して、二次
再結晶と純化のため1100℃以上の仕上焼鈍を行うこ
とで、低い鉄損特性を有する一方向性電磁鋼板が製造さ
れる。以上得られた製品に、さらに鉄損を良好にするた
め、上記一方向性電磁鋼板に、磁区を細分化するための
処理を施すことも可能である。
The above-mentioned rapid heating treatment can be incorporated into the decarburizing annealing step as a heating step of the decarburizing annealing even if it is performed before the next decarburizing annealing. After this,
Decarburization annealing is performed in a wet hydrogen atmosphere. At this time, carbon must be reduced to 0.005% or less so as not to deteriorate magnetic properties of the product. Here, when the slab heating temperature in hot rolling is low and only AlN is used as an inhibitor, nitriding treatment may be added in an ammonia atmosphere. Further, an annealing separator such as MgO is applied and finish annealing at 1100 ° C. or higher is performed for secondary recrystallization and purification, whereby a grain-oriented electrical steel sheet having low iron loss characteristics is manufactured. In order to further improve the iron loss of the obtained product, it is possible to subject the above-mentioned grain-oriented electrical steel sheet to a treatment for subdividing magnetic domains.

【0015】[0015]

【実施例】【Example】

(実施例1)表1に示す化学成分を含み、2.3mm厚に
まで熱間圧延させた熱延板に1100℃で1分間焼鈍を
施した。この後、ゼンジミアミルによるリバース圧延
と、タンデムミルにより一方向圧延の2種の冷間圧延方
法により最終板厚0.27mmにまで圧延した。
(Example 1) A hot rolled sheet containing the chemical components shown in Table 1 and hot-rolled to a thickness of 2.3 mm was annealed at 1100 ° C for 1 minute. Thereafter, it was rolled to a final sheet thickness of 0.27 mm by two types of cold rolling methods: reverse rolling by a Sendzimir mill and unidirectional rolling by a tandem mill.

【0016】さらに、得られたストリップを脱炭焼鈍す
る際、加熱段階で10℃/秒,85℃/秒,150℃/
秒の3条件で加熱し、その後、湿潤水素中で脱炭焼鈍
し、MgO粉を塗布した後、1200℃に10時間、水
素ガス雰囲気中で高温焼鈍を行った。表2に、得られた
製品の生産性と磁気特性を示す。本発明により、生産性
が良好で磁気特性に優れた一方向性電磁鋼板が得られて
いる。
Further, when the obtained strip is decarburized and annealed, it is heated at 10 ° C./sec, 85 ° C./sec, 150 ° C./sec.
After heating under three conditions of 2 seconds, decarburizing annealing in wet hydrogen and applying MgO powder, high-temperature annealing was performed at 1200 ° C. for 10 hours in a hydrogen gas atmosphere. Table 2 shows the productivity and magnetic properties of the obtained product. According to the present invention, a grain-oriented electrical steel sheet having good productivity and excellent magnetic properties has been obtained.

【0017】[0017]

【表1】 [Table 1]

【0018】[0018]

【表2】 [Table 2]

【0019】(実施例2)表3に示す成分組成を含む溶
鋼を鋳造し、スラブ加熱後、熱間圧延を行い、2.3mm
の熱延鋼板を得た。これを、1100℃で5分間焼鈍を
行い、さらに酸洗した後、6スタンドのタンデム冷間圧
延により0.22mm厚にした。圧延された鋼板を二対の
直接通電加熱ロールにより290℃/秒の加熱速度で8
45℃まで加熱した。この後、同じ845℃の均一温
度、湿潤水素中で脱炭焼鈍した。次にMgO粉を塗布し
た後、1200℃に10時間、水素ガス雰囲気中で高温
焼鈍を行った。これにより得られた製品の磁気特性は、
8 =1.94T、W17/50 =0.83(W/kg)の極め
て低い鉄損をもつ一方向性電磁鋼板が得られた。
Example 2 A molten steel containing the composition shown in Table 3 was cast, heated to a slab, and then hot-rolled to 2.3 mm.
Was obtained. This was annealed at 1100 ° C. for 5 minutes, pickled, and then tandem cold rolled in 6 stands to a thickness of 0.22 mm. The rolled steel sheet is heated at a heating rate of 290 ° C./sec.
Heated to 45 ° C. Thereafter, decarburization annealing was performed in wet hydrogen at the same uniform temperature of 845 ° C. Next, after applying MgO powder, high-temperature annealing was performed at 1200 ° C. for 10 hours in a hydrogen gas atmosphere. The magnetic properties of the resulting product are:
A unidirectional electrical steel sheet having an extremely low iron loss of B 8 = 1.94 T and W 17/50 = 0.83 (W / kg) was obtained.

【0020】[0020]

【表3】 [Table 3]

【0021】[0021]

【発明の効果】本発明によれば、生産性に優れ、かつ良
好な鉄損特性を有する一方向性電磁鋼板を製造すること
ができるので、産業上の貢献するところが極めて大であ
る。
According to the present invention, it is possible to produce a grain-oriented electrical steel sheet having excellent productivity and good iron loss characteristics.

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

【図1】冷間圧延方法による集合組織の変化の図表であ
る。
FIG. 1 is a chart showing a change in texture by a cold rolling method.

Claims (2)

(57)【特許請求の範囲】(57) [Claims] 【請求項1】 重量でC:0.10%以下、Si:2.
5〜7.0%ならびに通常のインヒビター成分を含み、
残余はFeおよび不可避的不純物よりなる一方向性電磁
鋼熱延板に熱延板焼鈍を施し、圧下率50%以上の冷間
圧延を施し、脱炭焼鈍した後、最終仕上焼鈍を施して一
方向性電磁鋼板を製造する方法において、上記冷間圧延
を、複数スタンドのタンデムミルによって行い、かつ最
終製品厚まで圧延されたストリップを、脱炭焼鈍する前
に80℃/秒以上の加熱速度で700℃以上の温度へ加
熱処理することを特徴とする低い鉄損をもつ一方向性電
磁鋼板の製造方法。
1. C: 0.10% or less by weight, Si: 2.
5 to 7.0% as well as the usual inhibitor components,
The remainder is subjected to hot-rolled sheet annealing of a unidirectional electromagnetic steel hot-rolled sheet composed of Fe and unavoidable impurities, cold-rolled at a reduction ratio of 50% or more, decarburized annealing, and then subjected to final finish annealing. In the method for producing a grain-oriented electrical steel sheet, the cold rolling is performed by a tandem mill having a plurality of stands, and the strip rolled to a final product thickness is heated at a heating rate of 80 ° C./sec or more before decarburizing annealing. A method for producing a grain-oriented electrical steel sheet having a low iron loss, wherein the method is heat-treated to a temperature of 700 ° C. or more.
【請求項2】 急速加熱処理が脱炭焼鈍の加熱段階とし
て行われることを特徴とする請求項1記載の方法。
2. The method according to claim 1, wherein the rapid heating treatment is performed as a heating stage of the decarburizing annealing.
JP5003440A 1993-01-12 1993-01-12 Manufacturing method of grain-oriented electrical steel sheet with low iron loss Expired - Lifetime JP2647323B2 (en)

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JP2647323B2 true JP2647323B2 (en) 1997-08-27

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