JP3392695B2 - Manufacturing method of grain-oriented electrical steel sheet with extremely excellent iron loss characteristics - Google Patents
Manufacturing method of grain-oriented electrical steel sheet with extremely excellent iron loss characteristicsInfo
- Publication number
- JP3392695B2 JP3392695B2 JP08421797A JP8421797A JP3392695B2 JP 3392695 B2 JP3392695 B2 JP 3392695B2 JP 08421797 A JP08421797 A JP 08421797A JP 8421797 A JP8421797 A JP 8421797A JP 3392695 B2 JP3392695 B2 JP 3392695B2
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- Japan
- Prior art keywords
- steel sheet
- roll
- annealing
- iron loss
- temperature side
- 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.)
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- Manufacturing Of Steel Electrode Plates (AREA)
- Soft Magnetic Materials (AREA)
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、２．５〜７．０％
のＳｉを含み、良好な鋼板形状をもち、かつ、極めて優
れた鉄損特性を有する高磁束密度一方向性電磁鋼板の製
造方法に関するものである。TECHNICAL FIELD The present invention relates to 2.5 to 7.0%.
The present invention relates to a method for producing a high magnetic flux density unidirectional electrical steel sheet which contains Si, has a good steel sheet shape, and has extremely excellent iron loss characteristics.
【０００２】[0002]
【従来の技術】一方向性電磁鋼板の磁気特性は一般に、
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が可能と
なり、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。さら
に、製品の結晶粒の＜１００＞軸を圧延方向に揃えるこ
とは、磁化特性を高め、鉄損特性も低くすることができ
るため、近年特にこの面で多くの研究が重ねられ、様々
な製造技術が開発された。2. Description of the Related Art Generally, the magnetic properties of grain-oriented electrical steel sheets are
It is evaluated by both iron loss characteristics and excitation characteristics. Increasing the excitation characteristics makes it possible to downsize equipment that increases the design magnetic flux density, while reducing iron loss characteristics reduces the loss of heat energy when used as electrical equipment and reduces power consumption. It is effective in saving money. Furthermore, aligning the <100> axis of the crystal grains of the product in the rolling direction can enhance the magnetization characteristics and reduce the iron loss characteristics. Technology was developed.
【０００３】たとえば、特公昭４０−１５６４４号公報
には高い磁束密度を得るために、方向性電磁鋼板の製造
方法が開示されている。これは、ＡｌＮ＋ＭｎＳをイン
ヒビターとして機能させ、最終冷延工程における圧下率
が８０％を超える強圧下とする製造方法である。この方
法によれば二次再結晶粒の｛１１０｝＜００１＞方位の
集積度が高く、Ｂ8 が１．８７０Ｔ以上の高磁束密度を
有する方向性電磁鋼板が得られる。For example, Japanese Examined Patent Publication No. 40-15644 discloses a method for producing a grain-oriented electrical steel sheet in order to obtain a high magnetic flux density. This is a manufacturing method in which AlN + MnS is made to function as an inhibitor and the rolling reduction in the final cold rolling step is 80% or more. According to this method, it is possible to obtain a grain-oriented electrical steel sheet having a high degree of integration of the {110} <001> orientation of the secondary recrystallized grains and a high magnetic flux density of B8 of 1.870T or more.
【０００４】しかし、この製造方法はある程度の鉄損の
低減は図れるのであるが、二次再結晶マクロの粒径が１
０mmオーダと大きいため、鉄損に影響する因子である渦
電流損を減らすことができず、良好な鉄損値が得られて
いなかった。これを改善するために、特公昭５７−２２
５２号公報に開示されている鋼板にレーザ処理を施す方
法、さらに特公昭５８−２５６９号公報には鋼板に機械
的な歪みを加える方法など、磁区を細分化する様々な方
法が開示されている。However, although this manufacturing method can reduce iron loss to some extent, the grain size of the secondary recrystallization macro is 1
Since it was large on the order of 0 mm, the eddy current loss, which is a factor affecting iron loss, could not be reduced, and a good iron loss value was not obtained. To improve this, Japanese Patent Publication No. 57-22
Various methods for subdividing magnetic domains are disclosed, such as a method of subjecting a steel sheet to laser treatment disclosed in Japanese Patent Publication No. 52-52, and a method of applying mechanical strain to the steel sheet in Japanese Patent Publication No. 58-2569. .
【０００５】一方、二次再結晶粒をより小さくして磁気
特性を向上する方法として特公平６−５１１８７号公報
がある。すなわち、該公報には、常温で圧延された鋼板
（ストリップ）に１４０℃／秒以上の加熱速度で６５７
℃以上の温度へ超急速焼きなまし処理を施し、該鋼板を
脱炭素処理し、最終高温焼きなまし処理を施して二次成
長を行い、それによって前記鋼板が低減した寸法の二次
粒子および応力除去焼きなまし処理後も有意な変化なし
に持続する改善された鉄損を持つ製造法が開示されてい
る。On the other hand, Japanese Patent Publication No. 6-51187 discloses a method for making secondary recrystallized grains smaller to improve magnetic properties. That is, in this publication, a steel sheet (strip) rolled at room temperature is heated to 657 at a heating rate of 140 ° C./sec or more.
Ultra-rapid annealing treatment to a temperature of ℃ or more, decarburization treatment of the steel sheet, final high-temperature annealing treatment to carry out secondary growth, whereby secondary grain of the dimensions reduced by the steel sheet and stress relief annealing treatment Disclosed is a manufacturing process with improved iron loss that persists without significant change thereafter.
【０００６】しかし、この製造方法により単に二次粒子
を微細化するだけでは、従来の磁区細分化なみの鉄損を
得ることは困難である。特に鋼板が急速加熱で急激に高
温に曝されるにより、異なった組成の酸化被膜が形成さ
れ（ファイアライト（２ＭｇＯ・ＳｉＯ2 ）が優先的に
形成されるようになる）、最終焼鈍においてＭｇＯ塗布
によるフォルステライト（２ＭｇＯ・ＳｉＯ2 ）の形成
が必ずしも良好とならず、十分な被膜張力により優れた
磁気特性が得られないという問題がある。However, it is difficult to obtain iron loss similar to the conventional magnetic domain subdivision by simply refining the secondary particles by this manufacturing method. In particular, when a steel sheet is rapidly exposed to a high temperature by rapid heating, an oxide film having a different composition is formed (firelite (2MgO.SiO 2 ) is preferentially formed), and MgO is applied in the final annealing. The formation of forsterite (2MgO.SiO 2 ) is not always good, and there is a problem that excellent magnetic properties cannot be obtained due to sufficient film tension.
【０００７】本発明者らは、かかる問題を解決するため
に、最終板厚まで圧延されたストリップを脱炭焼鈍する
直前、若しくは脱炭焼鈍の加熱段階として、Ｐ H2 O ／
Ｐ H2 が０．２以下の非酸化性雰囲気中で１００℃／秒
以上の加熱速度で７００℃以上の温度へ加熱処理する方
法を提案し、特開平７−６２４３６号公報に開示してい
る。また、急速加熱の具体例として２対の直接通電加熱
ロールを用いることも提示している。In order to solve such a problem, the inventors of the present invention have made P H 2 O / as a heating step immediately before decarburizing annealing of a strip rolled to a final plate thickness or as a heating step of decarburizing annealing.
A method of heat treatment to a temperature of 700 ° C. or more at a heating rate of 100 ° C./sec or more in a non-oxidizing atmosphere having a PH 2 of 0.2 or less is proposed, and disclosed in JP-A-7-62436. . It also proposes to use two pairs of direct-current heating rolls as a specific example of rapid heating.
【０００８】この製造方法では、確かに良好な磁気特性
が得られるが、急速加熱中に鋼板表面に緻密な酸化層を
形成する場合があることが分かった。この酸化層が形成
されるとこれがバリヤーとなり脱炭作用に影響する。す
なわち、製品板での炭素含有量の低減が図れず、その結
果、磁気時効により製品磁気特性の劣化を生じてしま
う。また、十分な脱炭を行うために脱炭時間を長くすれ
ば、磁気時効の問題は解決されるが、脱炭時間を延長す
ることは製造コストアップになるので好ましくない。It has been found that although good magnetic properties are certainly obtained by this manufacturing method, a dense oxide layer may be formed on the surface of the steel sheet during rapid heating. When this oxide layer is formed, it acts as a barrier and affects the decarburizing action. That is, the carbon content in the product plate cannot be reduced, and as a result, the magnetic properties of the product deteriorate due to the magnetic aging. Further, if the decarburization time is lengthened in order to perform sufficient decarburization, the problem of magnetic aging can be solved, but extending the decarburization time is not preferable because it increases the manufacturing cost.
【０００９】鋼帯の連続熱処理において、上記した急速
加熱に２対の通電ロールを用いる方法にも種々の提案が
ある。例えば、特開平７−２９２４２３号公報には鋼帯
の形状を得るために必要な板張力（最大７kg／mm2 ）を
通電体ロール間に付与することが開示されている。該公
報記載の発明では磁気特性を対象にしていないが、板張
力を最大７kg／mm2 まで許容しており、この様な大きな
板張力を付与することは磁束密度の劣化を来たす。There are various proposals for a method of using two pairs of energizing rolls for rapid heating in the continuous heat treatment of steel strip. For example, Japanese Patent Application Laid-Open No. 7-292423 discloses that plate tension (maximum 7 kg / mm 2 ) required to obtain the shape of a steel strip is applied between the current-carrying rolls. Although the invention described in this publication does not deal with magnetic characteristics, the maximum plate tension is 7 kg / mm 2 , and application of such a large plate tension causes deterioration of magnetic flux density.
【００１０】また、特開平５−５４９５８号公報には通
電ロールの高温側ロールと被加熱体（鋼帯）との単位面
積辺りの圧下力を被加熱体の降伏点応力からユニット張
力を差し引いた値とすることが記載されている。該公報
記載の発明は通電ロールの磨耗防止と板形状劣化を防止
することを目的としており、磁気特性については対象と
していない。すなわち、圧下力の付与は磁気特性と無関
係に規制されている。さらに、特開平６−２９３９３４
号公報では、冷延鋼板を通電ロールを用いて連続焼鈍す
る際に、高温側通電ロールと接触する冷延鋼板の温度降
下量を板厚との関係で規制してる。これも前記公報記載
の発明と同様に、磁気特性を対象とするものでなく、磁
気特性と無関係に規制されている。従って、上記したこ
れらの通電ロールを用いた加熱処理は、一方向性電磁鋼
板の製造に適用できない。Further, in Japanese Unexamined Patent Publication No. 5-54958, a rolling force per unit area between a high temperature side roll of an energizing roll and a heated body (steel strip) is obtained by subtracting a unit tension from a yield point stress of the heated body. It is described that it is a value. The invention described in the publication is intended to prevent wear of the energizing roll and prevent deterioration of the plate shape, and does not deal with magnetic characteristics. That is, the application of the rolling force is regulated regardless of the magnetic characteristics. Furthermore, JP-A-6-293934
In the publication, when the cold-rolled steel sheet is continuously annealed by using the current-carrying roll, the temperature drop amount of the cold-rolled steel sheet which comes into contact with the high-temperature-side current-carrying roll is regulated in relation to the sheet thickness. Similar to the invention described in the above-mentioned publication, this is not intended for magnetic characteristics and is regulated regardless of magnetic characteristics. Therefore, the above-mentioned heat treatment using the energizing roll cannot be applied to the production of the grain-oriented electrical steel sheet.
【００１１】[0011]
【発明が解決しようとする課題】以上の従来の通電ロー
ルを用いる熱処理法は通常の冷延鋼板に関するものであ
り、これより磁気特性を向上させる手法を導き出すこと
は困難である。また一方向性電磁鋼板の製造法の脱炭焼
鈍前の急速加熱に適用される通電加熱では、脱炭性が課
題であった。本発明はこのような技術の現状にかんがみ
てなされたものであり、従来の問題点を解決して、十分
に低い鉄損をもつ高磁束密度一方向性電磁鋼板を安定し
て得る製造方法を提供するものである。The above-mentioned conventional heat treatment method using a current-carrying roll relates to an ordinary cold-rolled steel sheet, and it is difficult to derive a method for improving magnetic properties from this. Further, decarburization is a problem in the electric heating applied to the rapid heating before decarburization annealing in the production method of unidirectional electrical steel sheet. The present invention has been made in view of the current state of the art, and solves the conventional problems and provides a manufacturing method for stably obtaining a high magnetic flux density unidirectional electrical steel sheet having a sufficiently low iron loss. It is provided.
【００１２】本発明は、上記課題を解決すべく成された
ものであり、以下の構成を要旨とする。すなわち、
（１）重量で、Ｃ：０．１０％以下、Ｓｉ：２．５〜
７．０％ならびにＭｎ：０．０１５〜０．１５％、Ｓま
たはＳｅ：０．００１〜０．０５％、酸可溶性Ａｌ：
０．０１〜０．０４％、Ｎ：０．００３〜０．０２％を
含み、残余はＦｅおよび不可避的不純物よりなる鋼を通
常の方法で処理し、ほぼ最終製品厚まで圧延されたスト
リップを脱炭焼鈍し、最終仕上焼鈍を施す工程を含む一
方向性電磁鋼熱延板の製造方法において、ストリップを
脱炭焼鈍する際に、その直前で、急速加熱を通電ロール
を用いて行い、該通電ロールにおける低温側ロールと高
温側ロール間の板張力を１．０〜４．０kg／mm2 、高温
側ロールでの圧下力を線圧で１．０〜４．０kg／mm、高
温側ロールの温度を２００℃以上にすることを特徴とす
る極めて優れた鉄損特性を有する高磁束密度一方向性電
磁鋼板の製造方法。および
（２）急速加熱が脱炭焼鈍の昇温過程として行われるこ
とを特徴とする、請求項１記載の極めて優れた鉄損特性
を有する高磁束密度一方向性電磁鋼板の製造方法であ
る。 The present invention has been made to solve the above problems, and has the following structures. That is,
(1) By weight, C: 0.10% or less, Si: 2.5 to
7.0% and Mn: 0.015 to 0.15%, S or
Or Se: 0.001-0.05%, acid-soluble Al:
A steel containing 0.01 to 0.04%, N: 0.003 to 0.02% and the balance Fe and unavoidable impurities was processed in a conventional manner to obtain a strip rolled to almost the final product thickness. Decarburization annealing, in the method for producing a unidirectional electrical steel hot-rolled sheet including the step of performing a final finish annealing, when decarburizing and annealing the strip, immediately before that, using a current-carrying rapid heating, The plate tension between the low temperature side roll and the high temperature side roll of the energizing roll is 1.0 to 4.0 kg / mm 2 , the rolling force of the high temperature side roll is 1.0 to 4.0 kg / mm in linear pressure, and the high temperature side roll. The method for producing a high magnetic flux density unidirectional electrical steel sheet having extremely excellent iron loss characteristics, which is characterized in that the temperature is set to 200 ° C. or higher. And ( 2 ) rapid heating is performed as a heating process of decarburization annealing.
And very excellent iron loss characteristics according to claim 1.
With a high magnetic flux density grain-oriented electrical steel sheet
It
【００１３】上記のように本発明は、前記急速加熱を通
電体ロールを用いて行う場合に、低温側ロールと高温側
ロール間の板張力、および高温側ロールでの圧下力（線
圧）、並びに高温側ロールの温度を上記した範囲に規制
することにより、ストリップの板形状を良好にすると共
に、ストリップに適正な歪みを付与して、二次再結晶の
核となる一次再結晶後での｛１１０｝＜００１＞方位粒
の生成を促進し、微細な二次再結晶粒を形成して、Ｂ8
が１．９１（Ｔ）以上の高磁束密度と共にＷ17/50 で
０．８２Ｗ／kg以下の極めて優れた鉄損特性を有する一
方向性電磁鋼板を得ることができる。このように本発明
は良好な板形状と優れた磁気特性とを両立させた一方向
性電磁鋼板の製造方法を提供するものである。As described above, in the present invention, when the rapid heating is performed by using the current-carrying roll, the plate tension between the low temperature side roll and the high temperature side roll, and the rolling force (linear pressure) at the high temperature side roll, Also, by controlling the temperature of the high-temperature side roll within the above range, the strip plate shape is improved, and appropriate distortion is imparted to the strip, which is the core of secondary recrystallization. The formation of {110} <001> oriented grains is promoted to form fine secondary recrystallized grains, and B8
It is possible to obtain a grain-oriented electrical steel sheet having a high magnetic flux density of 1.91 (T) or more and an extremely excellent iron loss characteristic of 0.82 W / kg or less at W17 / 50. As described above, the present invention provides a method for producing a grain-oriented electrical steel sheet which has both a good plate shape and excellent magnetic properties.
【００１４】[0014]
【発明の実施の形態】以下に本発明をさらに詳細に説明
する。図１は本発明に用いられる通電加熱装置の１例を
模式的に示したもので、ストリップ１は、各押えロール
５，６と対になり、導電性部材２で接続された低温側通
電体ロール３と高温側通電体ロール４とにより通電さ
れ、加熱される。７は圧下力調整装置でありストリップ
の延伸を調整する。８は外部電源と接続される環状トラ
ンスである。この通電加熱装置は脱炭焼鈍の前、或い脱
炭焼鈍の加熱段階に組込んで設置することができる。BEST MODE FOR CARRYING OUT THE INVENTION The present invention will be described in more detail below. FIG. 1 schematically shows an example of an electric heating device used in the present invention, in which a strip 1 is paired with each of the pressing rolls 5 and 6 and is connected to a low temperature side electric conductor by a conductive member 2. The roll 3 and the high temperature side current-carrying roll 4 energize and heat. Reference numeral 7 is a rolling force adjusting device for adjusting the stretching of the strip. Reference numeral 8 is a ring transformer connected to an external power source. This electric heating device can be installed before decarburization annealing or by incorporating it in the heating stage of decarburization annealing.
【００１５】前記したように、ストリップを通電ロール
で加熱することは知られているが、本発明は磁気特性を
向上させるために、脱炭焼鈍に際して、急速加熱時に用
いる通電ロールの実施条件を適性に選択する。すなわち
本発明は、通電加熱するに際し、低温側ロールと高温側
ロールの間でストリップに板張を付与して適宜延伸さ
せ、板形状を良好にする。すなわち全幅方向に亘って平
坦化するのであるが、そのためには１．０kg／mm2 以上
の張力が必要である。一方、ロール間張力が高くなり過
ぎると、一時再結晶後の集合組織（１００）＜０２５＞
が増加する傾向にあり、これが二次再結晶方位の圧延方
向への先鋭性に影響し、磁束密度を低下させる。従っ
て、最終製品の磁束密度Ｂ8が１．９１（Ｔ）以上にな
るようにするためには張力が４kg／mm2 を超えないよう
にする必要がある。好ましくは１．５〜３．０kg／mm2
とするのがよい。As described above, it is known that the strip is heated by the current-carrying roll, but in the present invention, in order to improve the magnetic properties, the conditions for carrying out the current-carrying roll used during the rapid heating during decarburization annealing are suitable. To select. That is, according to the present invention, when electrically heating, the strip is stretched between the low temperature side roll and the high temperature side roll and appropriately stretched to improve the plate shape. That is, flattening is performed over the entire width direction, but for that purpose, a tension of 1.0 kg / mm 2 or more is required. On the other hand, when the tension between the rolls becomes too high, the texture (100) <025> after the temporary recrystallization is obtained.
Of the secondary recrystallization orientation influences the sharpness of the secondary recrystallization orientation in the rolling direction and reduces the magnetic flux density. Therefore, in order to make the magnetic flux density B8 of the final product to be 1.91 (T) or more, it is necessary to make the tension not exceed 4 kg / mm 2 . Preferably 1.5 to 3.0 kg / mm 2
It is good to say
【００１６】また本発明では高温側ロールに負荷する圧
下力を規制する。すなわち、線圧で１．０〜４．０kg／
mmとする。通電ロールの表面には異物が付着したり磨耗
によって凹凸が形成されることがあり、線圧が小さいと
接触が不均一になりストリップとの接点でスパークを起
こすことがある。これを防ぐために線圧１．０kg／mm以
上の圧下力とすることがよく、また板形状も良好とな
る。しかし、余り大きな線圧を負荷することは、高温加
熱されたストリップは変形抵抗が小さく変形しやすいた
め、形状性に好ましくなく、さらに一時再結晶後に１０
０面が増加したり、二次再結晶の安定性に影響し、磁束
密度や鉄損を劣化させる原因になる。そのために線圧は
４．０kg／mmが限界であり、これを上限とする。好まし
くは１．５〜３．０kg／mmとするのがよい。Further, in the present invention, the rolling down force applied to the high temperature side roll is regulated. That is, 1.0 to 4.0 kg / in linear pressure
mm. Foreign matter may adhere to the surface of the current-carrying roll or unevenness may be formed due to abrasion. If the linear pressure is small, the contact may become non-uniform and spark may occur at the contact point with the strip. In order to prevent this, it is preferable that the linear pressure is 1.0 kg / mm or more, and the plate shape is good. However, it is not preferable to apply an excessively large linear pressure because the strip heated at high temperature has a small deformation resistance and is easily deformed.
The number of zero planes increases, and the stability of secondary recrystallization is affected, which causes deterioration of magnetic flux density and iron loss. Therefore, the linear pressure is limited to 4.0 kg / mm, and this is the upper limit. It is preferably 1.5 to 3.0 kg / mm.
【００１７】図２は板厚０．２２mmの一方向性電磁鋼板
を製造する過程において、脱炭焼鈍の昇熱段階で行う急
速加熱を通電ロールで実施し、得られた製品の、ロール
間張力毎に高温側ロールと磁気特性（Ｂ8 ）との関係を
示したものである。すなわち、図２の製品は、Ｃ：０．
０７７（wt）％、Ｓｉ：３．２５％、Ｍｎ：０．０８
％、Ｐ：０．０１％、Ｓ：０．０３％、Ａｌ：０．０３
％、Ｎ：０．０１％、Ｃｕ：０．０８％、Ｓｎ：０．０
％、残部が実質的にＦｅよりなる連続鋳造スラブを熱間
圧延して２．４mm厚さの熱延板とし、１１２０℃×１分
の焼鈍を施した後、途中段階で２２０℃×１分間保持の
冷延により０．２６mmの板厚に仕上げた。この冷延板を
脱炭焼鈍するに際し、その昇温段階を図１に示す通電ロ
ールを用いて行い、脱炭焼鈍を８４０℃×１８０秒で行
った。その後焼鈍分離材を塗布し、仕上げ焼鈍を１２０
０℃×２４時間実施して得たものである。FIG. 2 shows that in the process of manufacturing a grain-oriented electrical steel sheet having a thickness of 0.22 mm, rapid heating performed in the heat-up stage of decarburization annealing was carried out by an energizing roll, and the tension between the rolls of the obtained product was measured. The relationship between the high temperature side roll and the magnetic characteristic (B8) is shown for each. That is, the product of FIG.
077 (wt)%, Si: 3.25%, Mn: 0.08
%, P: 0.01%, S: 0.03%, Al: 0.03
%, N: 0.01%, Cu: 0.08%, Sn: 0.0
%, The rest of which is substantially Fe, is hot-rolled into a hot-rolled sheet having a thickness of 2.4 mm, which is annealed at 1120 ° C. for 1 minute, and then 220 ° C. for 1 minute at an intermediate stage. The plate was finished to have a thickness of 0.26 mm by holding cold rolling. When decarburizing and annealing this cold-rolled sheet, the heating step was performed using the current-flowing roll shown in FIG. 1, and decarburizing and annealing was performed at 840 ° C. for 180 seconds. After that, an annealing separation material is applied and the final annealing is performed 120 times.
It was obtained by carrying out at 0 ° C. for 24 hours.
【００１８】図２から明らかのように、１．９１（Ｔ）
以上の高磁束密度（Ｂ8 ）を得るためには、ロール間張
力を４kg／mm2 以下、高温側の線圧を４kg／mm以下にす
ればよいことが分かる。As is apparent from FIG. 2, 1.91 (T)
In order to obtain the above high magnetic flux density (B8), it is understood that the tension between rolls should be 4 kg / mm 2 or less and the linear pressure on the high temperature side should be 4 kg / mm or less.
【００１９】さらに本発明においては、高温側ロールの
温度を２００℃以上にすることによって、通電体加熱さ
れた高温ストリップからの抜熱を抑制し、磁気特性の劣
化を防止する。すなわち、高温側ロールの温度が２００
℃に達しない低温では、これと接触する高温ストリップ
が抜熱によって形状変化を起こすと共に、導入される歪
みにより集合組織が変化し、二次再結晶方位の板面に対
する適正な潜り角度が得られず、磁束密度、鉄損共に劣
化するからである。好ましくは３００℃以上とするのが
よい。高温側ロールの昇温は適宜の加熱手段、例えば誘
導加熱手段等により行うことができる。Further, in the present invention, the temperature of the high temperature side roll is set to 200 ° C. or higher to suppress heat removal from the high temperature strip heated by the electric conductor and prevent deterioration of magnetic properties. That is, the temperature of the high temperature side roll is 200
At low temperatures below ℃, the hot strip that comes into contact with it undergoes shape change due to heat removal, and the texture changes due to the strain introduced, and a proper diving angle of the secondary recrystallization orientation with respect to the plate surface is obtained. However, both the magnetic flux density and the iron loss are deteriorated. The temperature is preferably 300 ° C. or higher. The temperature of the high temperature side roll can be raised by an appropriate heating means such as an induction heating means.
【００２０】以下に本発明の製造工程をさらに詳細に説
明する。先ず鋼成分の限定理由は下記の通りである。Ｃ
の含有は０．１０％以下とする。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からであ
る。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７．０％を上限とする。The manufacturing process of the present invention will be described in more detail below. First, the reasons for limiting the steel composition are as follows. C
Is 0.10% or less. This is because if the amount exceeds this, the time required for decarburization becomes long, which is economically disadvantageous. Si has a lower limit of 2.5% in order to improve iron loss, but if it is too much, it easily cracks during cold rolling, making it difficult to process it, so 7.0% is made the upper limit.
【００２１】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。インヒビターとしてＭｎとＳを添加する。Ｍｎ
は、ＭｎＳの適当な分散状態を得るため、０．０１５〜
０．１５％とする。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％とする。Ｓの代わりにＳｅ
を添加しても良く、また両方添加しても構わない。Furthermore, in order to produce a grain-oriented electrical steel sheet, add the following component elements as ordinary inhibitor components. The addition of M n and S as an inhibitor. Mn
Is 0.015 to obtain an appropriate dispersed state of MnS.
0.15% . S is MnS, an element necessary for forming the (Mn · Fe) S, to obtain a proper dispersion state, and 0.001 to 0.05%. Se instead of S
May be added, or both may be added.
【００２２】さらに、インヒビターとして酸可溶性Ａｌ
とＮを添加する。酸可溶性ＡｌはＡｌＮの適正な分散状
態を得るため０．０１〜０．０４％とする。Ｎも、Ａｌ
Ｎを得るため０．００３〜０．０２％とする。その他、
Ｃｕ，Ｓｎ，Ｓｂ，Ｃｒ，Ｂｉ，Ｍｏ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
加してもよい。[0022] In addition, acid as the inhibitor soluble Al
And N are added. Acid-soluble Al is a 0.01 to 0.04% to obtain a proper dispersion state of AlN. N is also Al
To obtain N, the content is set to 0.003 to 0.02%. Other,
At least one of Cu, Sn, Sb, Cr, Bi and Mo may be added in an amount of 1.0% or less for the purpose of strengthening the inhibitor.
【００２３】次に、上記したような成分を含有する溶鋼
を通常の鋳塊鋳造法または連続鋳造法で鋳片とし、これ
を熱間圧延して中間厚のストリップを得る。また、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。Next, molten steel containing the above components is cast into a slab by a conventional ingot casting method or a continuous casting method, which is hot-rolled to obtain an intermediate-thickness strip. The strip casting method can also be applied to the present invention.
【００２４】次に、熱延板焼鈍を施した後、１回乃至中
間焼鈍を含む２回以上の冷間圧延により最終製品厚のス
トリップを得る。または、熱延板焼鈍を施すことなく、
中間焼鈍を含む２回以上の冷間圧延により最終製品厚の
ストリップを得るこもできる。中間焼鈍を含む２回以上
の冷間圧延をする際の、一回目の圧延は圧下率５〜５０
％、熱延板焼鈍および中間焼鈍は９５０〜１２００℃で
３０秒〜３０分の焼鈍を行うことが望ましい。次の最終
冷延圧下率は圧下率８５％以上が望ましい。下限８５％
は、これ以下では｛１１０｝＜００１＞方位が圧延方向
に高い集積度をもつゴス核が得られないからである。Next, after hot-rolled sheet annealing, a strip having a final product thickness is obtained by cold rolling one or more times including intermediate annealing. Or, without applying hot-rolled sheet annealing,
It is also possible to obtain a strip with the final product thickness by cold rolling two or more times including intermediate annealing. When performing cold rolling twice or more including intermediate annealing, the first rolling is a reduction ratio of 5 to 50.
%, Hot-rolled sheet annealing and intermediate annealing are preferably performed at 950 to 1200 ° C. for 30 seconds to 30 minutes. The final final cold rolling reduction is preferably 85% or more. Lower limit 85%
This is because, below this, a Goss nucleus having a {110} <001> orientation with a high degree of integration in the rolling direction cannot be obtained.
【００２５】なお、冷間圧延工程では、冷間圧延中に複
数回のパスにより各板厚段階を経て最終板厚となるが、
磁気特性を向上させるため、そのパスの少なくとも一回
以上の途中板厚段階において、鋼板に１００℃以上の温
度範囲で１分以上の時間保持する熱効果を与えても構わ
ない。In the cold rolling process, the final thickness is obtained by passing through each thickness stage by a plurality of passes during cold rolling.
In order to improve the magnetic properties, the steel plate may be subjected to a thermal effect of holding the steel plate in a temperature range of 100 ° C. or more for a time of 1 minute or more in at least one or more intermediate thickness steps of the pass.
【００２６】以上の最終製品厚まで圧延されたストリッ
プには加熱処理を施す。この加熱処理は、前記した通電
体ロールを用いて行われ、先ずストリップを１００℃／
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を１００℃／秒としたの
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｝＜００１＞方位粒が減少し、微細な二次再
結晶粒が得られないからである。また、加熱処理の下限
温度を７００℃としたのは、これ以下では再結晶が開始
されないからである。The strip rolled to the above final product thickness is subjected to heat treatment. This heat treatment is performed by using the above-mentioned current-carrying roll, and the strip is first heated at 100 ° C /
Rapid heating to a temperature of 700 ° C. or higher at a heating rate of 2 seconds or more. The lower limit of the heating rate at this time is set to 100 ° C./sec. Below this value, the {110} <001> oriented grains after the primary recrystallization, which is the nucleus of the secondary recrystallization, are reduced, and the fine secondary This is because recrystallized grains cannot be obtained. The reason why the lower limit temperature of the heat treatment is 700 ° C. is that recrystallization does not start below this temperature.
【００２７】なお、この急速加熱処理は脱炭性の問題か
ら、鋼板の雰囲気をＰ H2 O ／Ｐ H2 ≦４．２の湿水素
雰囲気中とすることが好ましい。このような雰囲気以外
では、鋼板表面に緻密な酸化層が形成され、続いて行わ
れる脱炭焼鈍での脱炭性を低下させてしまう。すなわ
ち、一方向性電磁鋼板の製造工程での脱炭焼鈍工程で
は、磁気時効を起こさないために炭素含有量を２０ppm
以下にまで脱炭しなければならない。そのためには、鋼
板表面に形成される緻密な酸化層の形成を抑制し、炭素
と酸素との反応を抑制しないようにしなければならな
い。From the problem of decarburization in this rapid heat treatment, it is preferable to set the atmosphere of the steel sheet in a wet hydrogen atmosphere of PH 2 O / PH 2 ≤4.2. Except for such an atmosphere, a dense oxide layer is formed on the surface of the steel sheet, and the decarburizing property in the subsequent decarburizing annealing is deteriorated. That is, in the decarburizing annealing process in the production process of the grain-oriented electrical steel sheet, the carbon content is 20 ppm in order to prevent magnetic aging.
Must be decarburized to: For that purpose, it is necessary to suppress the formation of a dense oxide layer formed on the surface of the steel sheet and not to suppress the reaction between carbon and oxygen.
【００２８】従来、脱炭焼鈍均熱時の雰囲気Ｐ H2 O ／
Ｐ H2 を０．１５〜０．７５にすることが知られている
が、加熱段階での雰囲気に関する知見は、特開平７−６
２４３６号公報に開示された発明のみで、１００℃／ｓ
以上の加熱速度の時にＰ H2O ／Ｐ H2 ≦０．２にする
ことが開示されている。Conventionally, the atmosphere P H 2 O /
It is known that the P H 2 in 0.15 to 0.75, knowledge of the atmosphere in the heating step, JP-A-7-6
With the invention disclosed in Japanese Patent No. 2436 only, 100 ° C / s
It is disclosed that P H 2 O / P H 2 ≤0.2 at the above heating rates.
【００２９】しかし、急速加熱処理を施す場合、この雰
囲気では、鋼板表面に形成される緻密な酸化層の形成を
十分に抑制することができない。このような問題を解決
するため、急速加熱処理をＰ H2 O ／Ｐ H2 ≦４．２の
湿水素雰囲気とすることにより、鋼板表面に形成される
緻密な酸化層の形成を抑制し、脱炭性が非常に良好なも
のとなる。なお、上記目的を達成するためにＰ H2 O ／
Ｐ H2 の下限は０．４とすることが好ましい。However, when performing the rapid heat treatment, the formation of a dense oxide layer formed on the surface of the steel sheet cannot be sufficiently suppressed in this atmosphere. In order to solve such a problem, the formation of a dense oxide layer formed on the surface of the steel sheet is suppressed by setting the rapid heat treatment to a wet hydrogen atmosphere with P H 2 O / P H 2 ≤4.2, Very good decarburization. In order to achieve the above purpose, P H 2 O /
The lower limit of P H 2 is preferably 0.4.
【００３０】また、この通電加熱では、電気機器を用い
るために雰囲気を常温に保つ必要がある。この場合に
は、水素による爆発の危険性を伴うために雰囲気に水素
は１〜３％程度しかいれることができない。このように
水素量が１〜３％と少ない場合には、露点を高くするこ
とが望ましいが、露点を３０℃以上にすることは、電気
機器に結露等の悪影響を与えるために制限することが望
ましいことからも上記雰囲気とするのがよい。Further, in this energization heating, it is necessary to keep the atmosphere at room temperature in order to use electric equipment. In this case, hydrogen can only be contained in the atmosphere in an amount of 1 to 3% because of the danger of explosion due to hydrogen. When the amount of hydrogen is as small as 1 to 3%, it is desirable to increase the dew point. However, setting the dew point to 30 ° C. or higher may be restricted in order to adversely affect electrical equipment such as dew condensation. The above atmosphere is preferable because it is desirable.
【００３１】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が、後者の方が工程
数が少ないので好ましい。なお、熱延でのスラブ加熱温
度を低温とし、ＡｌＮのみをインヒビターとして利用す
るプロセスの場合は、アンモニア雰囲気中で窒化処理を
付加することもある。The above rapid heat treatment can be carried out before the subsequent decarburization annealing, or can be incorporated in the decarburization annealing step as a heating step of the decarburization annealing, but the latter case is a step. It is preferable because the number is small. 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.
【００３２】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℃以上の仕上げ焼
鈍を行うことで、フォルステライトなどの良好な皮膜を
鋼板表面に形成した微細な二次再結晶粒を得る。フォル
ステライトなどの皮膜の上に、さらに絶縁皮膜を塗布す
ることにより極めて低い鉄損特性を有する一方向性電磁
鋼板が製造される。Further, by applying an annealing separator such as MgO and performing final annealing at 1100 ° C. or higher for secondary recrystallization and purification, a fine film such as forsterite is formed on the surface of the steel sheet. Obtain secondary recrystallized grains. By coating an insulating film on a film such as forsterite, a grain-oriented electrical steel sheet having extremely low iron loss characteristics is manufactured.
【００３３】以上によって得られる磁気特性は、後の歪
み取り焼鈍を施しても、変化しない低鉄損を保持してい
る。なお、得られた製品で、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 magnetic characteristics obtained as described above maintain a low iron loss that does not change even after the subsequent strain relief annealing. In addition, in order to further improve the iron loss in the obtained product, the unidirectional electrical steel sheet may be subjected to a treatment for subdividing the magnetic domains.
【００３４】[0034]
【実施例】次に本発明の実施例を説明する。Ｃ：０．０
７８％、Ｓｉ：３．２５％、Ｍｎ：０．０８％、Ｐ：
０．０１％、Ｓ：０．０３％、Ａｌ：０．０３％、Ｎ：
０．０１％、Ｃｕ：０．０８％、Ｓｎ：０．１％、残部
が実質的にＦｅよりなる連続鋳造法で製造したスラブを
熱間圧延して２．３mmの熱延板とし、該熱延板を１１０
０℃×分の焼鈍を施した後、途中段階で２２０℃×５分
間保持の冷間圧延で板厚０．２２mmの冷延板を製造し
た。EXAMPLES Examples of the present invention will be described below. C: 0.0
78%, Si: 3.25%, Mn: 0.08%, P:
0.01%, S: 0.03%, Al: 0.03%, N:
0.01%, Cu: 0.08%, Sn: 0.1%, and the balance being substantially Fe, which is manufactured by a continuous casting method, is hot-rolled into a hot-rolled sheet of 2.3 mm, 110 hot rolled sheet
After annealing at 0 ° C. × min, a cold rolled plate having a plate thickness of 0.22 mm was manufactured by cold rolling at 220 ° C. × 5 minutes holding in the middle.
【００３５】この冷延板を８４０℃×１８０秒の脱炭焼
鈍を行い、焼鈍分離剤塗布後仕上げ焼鈍を１２００℃×
２４時間施した。This cold-rolled sheet was decarburized and annealed at 840 ° C. for 180 seconds, and after the annealing separator was applied, finish annealing was performed at 1200 ° C.
It was applied for 24 hours.
【００３６】脱炭焼鈍の加熱段階での急速加熱は、各種
の条件で図１に示すような２対の通電ロールで行った。
雰囲気は水素＋窒素とし、Ｐ H2 O ／Ｐ H2 ：０．５４
の湿潤雰囲気とした。表１に通電体ロールの通版条件
と、得られた製品の形状性および磁気特性（磁束密度Ｂ
8 （Ｔ）、鉄損Ｗ17/15 （Ｗ／kg））を示した。Rapid heating in the heating stage of decarburization annealing was performed under various conditions with two pairs of energizing rolls as shown in FIG.
Atmosphere and hydrogen + nitrogen, P H 2 O / P H 2: 0.54
It was a wet atmosphere. Table 1 shows the plate-making conditions of the current-carrying roll, and the shape and magnetic properties of the obtained product (magnetic flux density B
8 (T), iron loss W17 / 15 (W / kg)).
【００３７】[0037]
【表１】 [Table 1]
【００３８】表１において条件２〜４および６は本発明
例であり、１，５，７〜１１は比較例である。条件１は
ロール間張力が０．９と低いため形状性が悪く、条件６
は出側（高温側）ロール温度が低いため磁束密度が低
い。条件７はロール間張力が７．０と高いため磁束密度
が低く、鉄損も悪くなっている。条件８はロール間張力
が８．０と高すぎるため鉄損値が高く、磁束密度も低く
なり、形状性も良くない。条件９は出側ロール圧下力が
高く、形状性は良いが、磁束密度および鉄損とも低下し
ている。条件１０は出側ロール圧下力が低いため形状が
劣化している。条件１１は出側ロール温度が低いため形
状が劣化し、鉄損も悪い。これに対して本発明例はいず
れも、形状、磁束密度、鉄損共に優れている。In Table 1, Conditions 2 to 4 and 6 are examples of the present invention, and 1, 5, 7 to 11 are comparative examples. Condition 1 is poor in shape because the tension between rolls is as low as 0.9.
Has a low magnetic flux density because the roll temperature on the output side (high temperature side) is low. In Condition 7, the tension between rolls is as high as 7.0, so the magnetic flux density is low and the iron loss is also poor. In condition 8, the tension between the rolls is too high at 8.0, so the iron loss value is high, the magnetic flux density is low, and the shape is not good. Condition 9 has a high roll-down force on the exit side and good formability, but both magnetic flux density and iron loss are low. In Condition 10, the shape is deteriorated because the rolling force at the exit side roll is low. Condition 11 has a low exit roll temperature, resulting in poor shape and poor iron loss. On the other hand, all the examples of the present invention are excellent in shape, magnetic flux density, and iron loss.
【００３９】[0039]
【発明の効果】以上のように、本発明によれば、通電ロ
ールによる急速加熱でのロール間張力、高温ロールの圧
下力および温度を調整することにより、二次再結晶方位
の圧延方向の尖鋭化、二次再結晶の板面潜り角度を適正
化し、かつ安定化することが可能となり、これにより極
めて優れた鉄損特性を有する高磁束密度一方向性電磁鋼
板を製造することができる。As described above, according to the present invention, the sharpness of the secondary recrystallization orientation in the rolling direction is adjusted by adjusting the inter-roll tension in the rapid heating by the energizing roll, the rolling force of the high temperature roll and the temperature. It is possible to optimize and stabilize the plate surface submerged angle of secondary recrystallization, and thus it is possible to manufacture a high magnetic flux density unidirectional electrical steel sheet having extremely excellent iron loss characteristics.
【図１】本発明の通電体加熱装置を模式的に示す図。FIG. 1 is a diagram schematically showing an electric heating device of the present invention.
【図２】通電体加熱におけるロール間張力毎の高温ロー
ル線圧と磁束密度との関係を示す図。FIG. 2 is a diagram showing a relationship between a high-temperature roll linear pressure and a magnetic flux density for each tension between rolls in heating an electric conductor.
───────────────────────────────────────────────────── フロントページの続き (56)参考文献 特開 平８−295937（ＪＰ，Ａ) 特開 平６−212274（ＪＰ，Ａ) 特開 平７−41860（ＪＰ，Ａ) (58)調査した分野(Int.Cl.7，ＤＢ名) C21D 8/12 C21D 9/46 501 H01F 1/16 ─────────────────────────────────────────────────── ─── Continuation of front page (56) References JP-A-8-295937 (JP, A) JP-A-6-212274 (JP, A) JP-A-7-41860 (JP, A) (58) Field (Int.Cl. 7 , DB name) C21D 8/12 C21D 9/46 501 H01F 1/16
Claims (2)
２．５〜７．０％ならびにＭｎ：０．０１５〜０．１５
％、ＳまたはＳｅ：０．００１〜０．０５％、酸可溶性
Ａｌ：０．０１〜０．０４％、Ｎ：０．００３〜０．０
２％を含み、残余はＦｅおよび不可避的不純物よりなる
鋼を通常の方法で処理し、ほぼ最終製品厚まで圧延され
たストリップを脱炭焼鈍し、最終仕上焼鈍を施す工程を
含む一方向性電磁鋼熱延板の製造方法において、ストリ
ップを脱炭焼鈍する際に、その直前で、急速加熱を通電
ロールを用いて行い、該通電ロールにおける低温側ロー
ルと高温側ロール間の板張力を１．０〜４．０kg／m
m2 、高温側ロールでの圧下力を線圧で１．０〜４．０k
g／mm、高温側ロールの温度を２００℃以上にすること
を特徴とする極めて優れた鉄損特性を有する高磁束密度
一方向性電磁鋼板の製造方法。1. C: 0.10% or less by weight, Si:
2.5-7.0% and Mn: 0.015-0.15
%, S or Se: 0.001-0.05%, acid soluble
Al: 0.01 to 0.04%, N: 0.003 to 0.0
A unidirectional electromagnetic process including the steps of treating steel containing 2% and the balance of Fe and unavoidable impurities by a conventional method, decarburizing and annealing a strip rolled to almost the final product thickness, and subjecting it to final finishing annealing. In the method for producing a hot-rolled steel sheet, immediately before decarburization annealing of a strip, rapid heating is performed using an energizing roll, and the plate tension between the low temperature side roll and the high temperature side roll of the energizing roll is 1. 0-4.0kg / m
m 2 , the rolling force on the high temperature side roll is 1.0 to 4.0k in linear pressure.
A method for producing a high magnetic flux density unidirectional electrical steel sheet having extremely excellent iron loss characteristics, characterized in that the temperature of the roll on the high temperature side is 200 ° C. or higher in g / mm.
われることを特徴とする、請求項１記載の極めて優れたThe excellent feature of claim 1 characterized in that
鉄損特性を有する高磁束密度一方向性電磁鋼板の製造方Manufacturing method of high magnetic flux density unidirectional electrical steel sheet with iron loss characteristics
法。Law.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP08421797A JP3392695B2 (en) | 1997-04-02 | 1997-04-02 | Manufacturing method of grain-oriented electrical steel sheet with extremely excellent iron loss characteristics |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP08421797A JP3392695B2 (en) | 1997-04-02 | 1997-04-02 | Manufacturing method of grain-oriented electrical steel sheet with extremely excellent iron loss characteristics |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH10280041A JPH10280041A (en) | 1998-10-20 |
| JP3392695B2 true JP3392695B2 (en) | 2003-03-31 |
Family
ID=13824323
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP08421797A Expired - Fee Related JP3392695B2 (en) | 1997-04-02 | 1997-04-02 | Manufacturing method of grain-oriented electrical steel sheet with extremely excellent iron loss characteristics |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3392695B2 (en) |
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|---|---|---|---|---|
| JP7006772B2 (en) | 2018-03-20 | 2022-01-24 | 日本製鉄株式会社 | Manufacturing method of grain-oriented electrical steel sheet and grain-oriented electrical steel sheet |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2679928B2 (en) * | 1993-01-12 | 1997-11-19 | 新日本製鐵株式会社 | Manufacturing method of grain-oriented electrical steel sheet with extremely low iron loss |
| JP3359385B2 (en) * | 1993-07-28 | 2002-12-24 | 新日本製鐵株式会社 | Manufacturing method of unidirectional electrical steel sheet |
| JP3392579B2 (en) * | 1995-04-26 | 2003-03-31 | 新日本製鐵株式会社 | Manufacturing method of grain-oriented electrical steel sheet with extremely low iron loss |
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- 1997-04-02 JP JP08421797A patent/JP3392695B2/en not_active Expired - Fee Related
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| Publication number | Publication date |
|---|---|
| JPH10280041A (en) | 1998-10-20 |
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