JP3390109B2 - Low iron loss high magnetic flux density - Google Patents
Low iron loss high magnetic flux densityInfo
- Publication number
- JP3390109B2 JP3390109B2 JP20105195A JP20105195A JP3390109B2 JP 3390109 B2 JP3390109 B2 JP 3390109B2 JP 20105195 A JP20105195 A JP 20105195A JP 20105195 A JP20105195 A JP 20105195A JP 3390109 B2 JP3390109 B2 JP 3390109B2
- Authority
- JP
- Japan
- Prior art keywords
- annealing
- steel sheet
- temperature
- cold rolling
- rolling
- 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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Classifications
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Landscapes
- Manufacturing Of Steel Electrode Plates (AREA)
- Soft Magnetic Materials (AREA)
Description
【０００１】[0001]
【発明の属する技術分野】本発明は鉄損特性の優れた一
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 a method for producing a grain-oriented electrical steel sheet having excellent iron loss characteristics.
【０００２】[0002]
【従来の技術】一方向性電磁鋼板は主として変圧器、発
電機その他の電気機器の鉄心材として用いられ、それが
有する磁気特性として励磁特性と鉄損特性が良好である
ことの他、良好な被膜を有するものでなければならな
い。2. Description of the Related Art Unidirectional electrical steel sheets are mainly used as core materials for transformers, generators and other electric equipment, and have good magnetic properties such as excitation properties and iron loss properties. It must have a coating.
【０００３】一方向性電磁鋼板は、二次再結晶現象を利
用して圧延面に｛１１０｝面、圧延方向に＜００１＞軸
を持ついわゆるゴス方位を有する結晶粒を発達させるこ
とによって得られる。A unidirectional electrical steel sheet is obtained by utilizing secondary recrystallization phenomenon to develop crystal grains having a so-called Goss orientation having a {110} plane in the rolling surface and a <001> axis in the rolling direction. .
【０００４】前記二次再結晶現象は、よく知られている
ように、仕上げ焼鈍過程で生じるが、二次再結晶の発現
を十分なものとするためには、仕上げ焼鈍過程における
二次再結晶発現温度域まで一次再結晶粒の成長を抑制す
るＡｌＮ、ＭｎＳ、ＭｎＳｅ等の微細な析出物、いわゆ
るインヒビターを鋼中に存在させる必要がある。As is well known, the secondary recrystallization phenomenon occurs during the finish annealing process, but in order to sufficiently develop the secondary recrystallization, the secondary recrystallization phenomenon occurs in the finish annealing process. It is necessary to allow fine precipitates such as AlN, MnS, and MnSe, so-called inhibitors, which suppress the growth of primary recrystallized grains up to the development temperature range, to be present in the steel.
【０００５】従って、電磁鋼スラブはインヒビター形成
元素、例えばＡｌ、Ｍｎ、Ｓ、Ｓｅ、Ｎ等を完全に固溶
させるために、１３５０〜１４００℃といった高温に加
熱される。そして、電磁鋼スラブ中に完全に固溶せしめ
られたインヒビター形成元素は、熱延板あるいは最終冷
間圧延前の中間板厚の段階で、焼鈍によってＡｌＮ、Ｍ
ｎＳ、ＭｎＳｅとして微細に析出せしめられる。Therefore, the electromagnetic steel slab is heated to a high temperature such as 1350 to 1400 ° C. in order to completely dissolve the inhibitor forming elements such as Al, Mn, S, Se and N. Then, the inhibitor-forming element completely solid-solved in the electromagnetic steel slab is AlN, M by annealing at the stage of intermediate plate thickness before hot rolling or final cold rolling.
Finely precipitated as nS and MnSe.
【０００６】この他冶金的には二次再結晶粒を小さくす
ることにより、磁区細分化を図り鉄損の低減が可能であ
る。この方法には例えば特開昭５０−１６６１０号公報
に示される冷間圧延時に熱効果を与える方法、あるいは
特開昭５８−２３４１４号公報に示されるような鋼中に
Ｓｎを添加する方法等があり、又プロセス面からは特開
平１−２９０７１６号公報に示される如く、冷延鋼板を
急速加熱処理し脱炭焼鈍を施す方法が提案されている。
これらはいずれも高温スラブ加熱を前提とした製造プロ
セスによるものである。In addition to this, metallurgically, by making the secondary recrystallized grains small, it is possible to subdivide the magnetic domains and reduce the iron loss. Examples of this method include a method of imparting a heat effect during cold rolling as disclosed in Japanese Patent Laid-Open No. 50-16610, or a method of adding Sn to steel as disclosed in Japanese Patent Laid-Open No. 58-23414. In view of the process, as disclosed in Japanese Patent Laid-Open No. 1-290716, a method has been proposed in which a cold rolled steel sheet is subjected to rapid heat treatment and decarburization annealing.
All of these are based on a manufacturing process premised on high temperature slab heating.
【０００７】このような高温スラブ加熱法に対して特公
昭６１−６０８９６号公報、特開昭６２−４０３１５号
公報等に開示されている技術、即ち二次再結晶に必要な
インヒビターは、脱炭焼鈍完了以降から仕上げ焼鈍にお
ける二次再結晶発現以前まで造り込むものがある。その
手段としては、鋼中にＮを侵入させることによって、イ
ンヒビターとして機能する（Ａｌ、Ｓｉ）Ｎを形成させ
る。[0007] A special method for such high temperature slab heating method
The techniques disclosed in JP-A-61-60896 and JP-A-62-40315, that is, the inhibitors required for secondary recrystallization, are from the completion of decarburization annealing to the appearance of secondary recrystallization in finish annealing. There is something to build. As a means thereof, N is allowed to penetrate into steel to form (Al, Si) N which functions as an inhibitor.
【０００８】鋼中にＮを侵入させる手段としては、仕上
げ焼鈍昇温過程での雰囲気ガスからのＮの侵入を利用す
るか、脱炭焼鈍後段領域あるいは脱炭焼鈍完了後のスト
リップを連続ラインでＮＨ3 等の窒化源となる雰囲気ガ
スを用いて行う。As a means for injecting N into the steel, the invasion of N from the atmospheric gas in the finish annealing temperature rising process is used, or the strip after decarburization annealing or the strip after decarburization annealing is completed in a continuous line. It is performed by using an atmosphere gas such as NH 3 which serves as a nitriding source.
【０００９】[0009]
【発明が解決しようとする課題】本発明は、低温スラブ
加熱を前提とする特公昭６１−６０８９６号公報に基づ
くものであるが、このプロセスにおいて重要なことは、
脱炭焼鈍板の結晶組織（平均粒径、粒径分布）、集合組
織の調整と冷延以降のインヒビターの造り込みである。
特に脱炭焼鈍の結晶組織および集合組織は製品の磁気特
性に大きな影響を及ぼすことが知られている。The present invention is based on Japanese Patent Publication No. 61-60896, which is premised on low temperature slab heating. What is important in this process is:
This is the adjustment of the crystal structure (average grain size, grain size distribution) and texture of the decarburized annealed sheet and the incorporation of the inhibitor after cold rolling.
It is known that the crystal structure and texture of decarburization annealing have a great influence on the magnetic properties of the product.
【００１０】結晶組織に影響を与える工程として冷間圧
延と脱炭焼鈍がある。もちろん冷間圧延前の焼鈍条件が
影響することは言うまでもない。本発明は熱延板焼鈍の
冷却条件と冷間圧延時の鋼板温度に着目し、これらの条
件と鉄損特性の関係を明らかにして鉄損の低い高磁束密
度一方向性電磁鋼板の製造方法を提供するものである。Cold rolling and decarburization annealing are processes that affect the crystal structure. Needless to say, the annealing conditions before cold rolling have an influence. The present invention focuses on the cooling conditions of hot-rolled sheet annealing and the steel sheet temperature during cold rolling, and clarifies the relationship between these conditions and iron loss characteristics to produce a high magnetic flux density unidirectional electrical steel sheet with low iron loss. Is provided.
【００１１】[0011]
【課題を解決するための手段】本発明は重量比で、Ｃ
：０．０２５〜０．０７５％、 Ｓｉ：２．５〜４．
５％、Ｍｎ：０．０５０〜０．４５％、 Ｓ ≦０．
０１５％、酸可溶性Ａｌ：０．０１５〜０．０４０％、
Ｎ≦０．０１０％、必要に応じてＳｎ：０．０２〜
０．１５％、 Ｃｒ：０．０５〜０．３０％、Ｃ
ｕ：０．０３〜０．３０％を含有し、残部Ｆｅ及び不可
避的不純物からなる電磁鋼スラブを１２８０℃以下の温
度に加熱した後、熱延し、最終冷延前に焼鈍を実施し、
一回または中間焼鈍を介挿する二回以上の圧延でその最
終圧延率を８０％以上とし、ついで脱炭焼鈍、窒化処
理、仕上げ焼鈍をする一方向性電磁鋼板の製造におい
て、最終冷延前の鋼板の焼鈍を２段均熱とし、高温側の
温度、均熱時間を９５０〜１１５０℃、１８０秒以内、
低温側の温度、均熱時間を８００〜９５０℃、３０〜３
００秒とし、８００〜９５０℃の温度域から３００℃ま
での平均冷却速度をＲ℃/secで冷却し、最終冷延の複数
回のパスの少なくとも１回以上鋼板に１００〜３００℃
の温度範囲で下記条件を満たすＴ℃で１分以上の時間保
持する熱効果を与えることを特徴とする低鉄損高磁束密
度一方向性電磁鋼板の製造方法にある。
４００−１０Ｒ≦Ｔ≦６９０−１２ＲThe present invention provides a weight ratio of C
: 0.025 to 0.075%, Si: 2.5 to 4.
5%, Mn: 0.050 to 0.45%, S ≤ 0.
015%, acid soluble Al: 0.015 to 0.040%,
N ≦ 0.010%, Sn: 0.02 as required
0.15%, Cr: 0.05-0.30%, C
u: A magnetic steel slab containing 0.03 to 0.30% and the balance Fe and unavoidable impurities is heated to a temperature of 1280 ° C. or lower, hot rolled, and annealed before final cold rolling,
In the production of unidirectional electrical steel sheet in which final rolling rate is 80% or more in one rolling or two or more rollings with intermediate annealing, and then decarburization annealing, nitriding treatment and finish annealing are performed, before final cold rolling. Of the steel sheet of No. 2 is soaked in two steps, the temperature on the high temperature side, the soaking time is 950 to 1150 ° C., within 180 seconds,
Temperature on the low temperature side, soaking time is 800 to 950 ° C, 30 to 3
00 seconds, the average cooling rate from the temperature range of 800 to 950 ° C. to 300 ° C. is cooled at R ° C./sec, and 100 to 300 ° C. is applied to the steel sheet at least once in multiple passes of final cold rolling.
In the method for producing a low iron loss high magnetic flux density grain-oriented electrical steel sheet, which has a thermal effect of holding at T ° C. satisfying the following conditions in the temperature range of 1 minute or more. 400-10R ≦ T ≦ 690-12R
【００１２】以下本発明を詳細に説明する。本発明にお
いて、出発材料とするスラブの成分組成の限定理由は以
下の通りである。Ｃはその含有量が０．０２５％未満で
は、高磁束密度が安定して得られ難い。一方、０．０７
５％を超えて多くなりすぎると、脱炭焼鈍時間が長くな
り生産性を損なう。Ｓｉは含有量が２．５％未満になる
と低鉄損の製品が得られ難く、４．５％を超えると冷間
圧延時に、割れ、破断が多発し安定した冷間圧延作業を
不可能にする。The present invention will be described in detail below. In the present invention, the reasons for limiting the component composition of the slab used as the starting material are as follows. When the content of C is less than 0.025%, it is difficult to stably obtain a high magnetic flux density. On the other hand, 0.07
If it exceeds 5% and becomes too large, the decarburization annealing time becomes long and the productivity is impaired. If the Si content is less than 2.5%, it is difficult to obtain a product with low iron loss, and if it exceeds 4.5%, cracks and fractures frequently occur during cold rolling, making stable cold rolling work impossible. To do.
【００１３】本発明の成分系における特徴の１つは、Ｓ
を０．０１５％以下、好ましくは０．０１０％以下とす
る点にある。公知の技術、例えば特公昭４０−１５６４
４号公報あるいは特公昭４７−２５２５０号公報に開示
されている技術においては、Ｓは二次再結晶を発現させ
るのに必要な析出物の一つであるＭｎＳの形成元素とし
て必須であった。しかしながら、インヒビターとして
（Ａｌ、Ｓｉ）Ｎを用いる本発明においては、ＭｎＳは
特に必要としない。むしろ、ＭｎＳが増加することは一
次再結晶粒径調整を困難にし、高磁束密度鋼板を得難く
する。One of the features of the component system of the present invention is S
Is 0.015% or less, preferably 0.010% or less. Known technology, for example, Japanese Patent Publication No. 40-1564
In the technique disclosed in Japanese Patent Publication No. 4 or Japanese Patent Publication No. 47-25250, S was indispensable as an element for forming MnS, which is one of the precipitates necessary for causing secondary recrystallization. However, MnS is not particularly required in the present invention using (Al, Si) N as the inhibitor. Rather, an increase in MnS makes it difficult to adjust the primary recrystallization grain size and makes it difficult to obtain a high magnetic flux density steel sheet.
【００１４】ＡｌはＮと結合してＡｌＮを形成するが、
本発明においては後工程、即ち、一次再結晶完了鋼を窒
化することにより（Ａｌ、Ｓｉ）Ｎを形成せしめること
を必須としているから、フリーのＡｌが一定量以上必要
である。そのため酸可溶性Ａｌとして０．０１５〜０．
０４０％添加する。Al combines with N to form AlN,
In the present invention, it is necessary to form (Al, Si) N by a post-process, that is, by nitriding the primary recrystallized steel, so that a certain amount of free Al is required. Therefore, as acid-soluble Al, 0.015 to 0.
Add 040%.
【００１５】Ｎは０．０１０％以下にする必要がある。
これを超えるとブリスターと呼ばれる鋼板表面の膨れが
発生する。下限は、０．００２０％程度がよい。Ｍｎは
その含有量が少なすぎると二次再結晶の発達が悪くな
り、一方多すぎると磁束密度鋼板が得られ難くなる。適
正な含有量は０．０５０〜０．４５％である。N must be 0.010% or less.
If it exceeds this, swelling of the steel sheet surface called blister occurs. The lower limit is preferably about 0.0020%. If the content of Mn is too small, the development of secondary recrystallization deteriorates, while if it is too large, it becomes difficult to obtain a magnetic flux density steel sheet. The proper content is 0.050 to 0.45%.
【００１６】ＳｎとＣｒは複合添加で仕上げ焼鈍時の被
膜形成を安定化すると同時にＳｎは脱炭焼鈍後の一次再
結晶集合組織を改善し、ひいては二次再結晶粒を小粒化
し、被膜の安定化と相俟って鉄損改善に効果が大きい。
Ｓｎの適量は０．０２〜０．１５％であり、これより少
ないと効果が弱く、一方多いと窒化が困難になり二次再
結晶粒が発達しなくなる。Ｃｒの適量は０．０５〜０．
３０％が良い。Ｃｕは高磁束密度鋼板を得るうえで効果
がありその適量は０．０３〜０．３０％の範囲である。
なお、微量のＰ、Ｔｉを鋼中に含有せしめることは、本
発明の主旨を損なうものではない。[0016] Sn and Cr stabilize the film formation during finish annealing by the combined addition, and at the same time, Sn improves the primary recrystallization texture after decarburization annealing, which in turn reduces secondary recrystallized grains to stabilize the film. The effect of improving iron loss is large in combination with
An appropriate amount of Sn is 0.02 to 0.15%, and if it is less than this, the effect is weak, while if it is more than that, nitriding becomes difficult and secondary recrystallized grains do not develop. An appropriate amount of Cr is 0.05 to 0.
30% is good. Cu is effective in obtaining a high magnetic flux density steel sheet, and its appropriate amount is in the range of 0.03 to 0.30%.
It should be noted that the inclusion of a trace amount of P and Ti in the steel does not impair the gist of the present invention.
【００１７】次に本発明の製造プロセスを説明する。電
磁鋼スラブは、転炉あるいは電気炉などの溶解炉で鋼を
溶製し、必要に応じて真空脱ガス処理し、しかる後熱間
圧延に先立つスラブ加熱が成される。本発明のプロセス
においては、スラブの加熱温度は１２８０℃以下の低い
ものとして加熱エネルギーの消費量を少なくするととも
に、鋼中のＡｌＮを完全に固溶させずに不完全固溶状態
とする。このスラブを熱延して所定の厚みの熱延板を造
る。Next, the manufacturing process of the present invention will be described. The electromagnetic steel slab is produced by melting steel in a melting furnace such as a converter or an electric furnace, performing vacuum degassing treatment if necessary, and then performing slab heating prior to hot rolling. In the process of the present invention, the heating temperature of the slab is set to a low temperature of 1280 ° C. or lower to reduce the consumption of heating energy, and the AlN in the steel is not completely solid-solved to be an incomplete solid solution state. This slab is hot-rolled to make a hot-rolled plate having a predetermined thickness.
【００１８】次に、本発明の特徴である熱延板焼鈍条件
と冷延条件について説明する。Ｃ：０．０５４％、Ｓ
ｉ：３．２５％、Ｍｎ：０．１０％、Ｐ：０．０２％、
Ｓ：０．００８％、酸可溶性Ａｌ：０．０３０％、Ｓ
ｎ：０．０６％、Ｃｒ：０．１２％、Ｎ：０．００７８
％を含むインゴットを１１５０℃に加熱した後熱延し
２．３mmの熱延板を造った。次いでこの熱延板を表１の
条件で焼鈍し冷却した。Next, the hot-rolled sheet annealing conditions and cold-rolling conditions that characterize the present invention will be described. C: 0.054%, S
i: 3.25%, Mn: 0.10%, P: 0.02%,
S: 0.008%, acid-soluble Al: 0.030%, S
n: 0.06%, Cr: 0.12%, N: 0.0078
% Of the ingot was heated to 1150 ° C. and then hot rolled to produce a hot rolled sheet of 2.3 mm. Next, this hot rolled sheet was annealed and cooled under the conditions shown in Table 1.
【００１９】[0019]
【表１】 [Table 1]
【００２０】この後酸洗し板厚０．２３mmまで冷延し
た。この冷延の途中板厚で５０〜３５０℃の温度範囲で
５分保持するＡｇｉｎｇ処理をした。この条件を表２に
示す。After that, it was pickled and cold-rolled to a plate thickness of 0.23 mm. During this cold rolling, an aging treatment was performed in which the plate thickness was maintained for 5 minutes in the temperature range of 50 to 350 ° C. This condition is shown in Table 2.
【００２１】[0021]
【表２】 [Table 2]
【００２２】次いで脱炭焼鈍を８３５℃の温度でＮ2 ：
２５％、Ｈ2 ：７５％、露点６５℃の雰囲気中で行っ
た。次いで７５０℃×３０sec の窒化処理をＮ2 、
Ｈ2 、ＮＨ3 の混合ガス中で行い窒化後のＮ2 量をほぼ
２００ppm に調整した。この後ＭｇＯとＴｉＯ2 を主成
分とする焼鈍分離材を塗布し、１２００℃×２０時間の
仕上げ焼鈍を行った。この後無水クロム酸、リン酸アル
ミニウムを主成分とする張力コーティングを施した。熱
延板焼鈍後の冷却条件（Ｒ℃/sec）−冷延時のＡｇｉｎ
ｇ温度（Ｔ℃）−鉄損特性の関係を図１に示す。Then decarburization annealing was carried out at a temperature of 835 ° C. with N 2 :
It was carried out in an atmosphere of 25%, H 2 : 75%, and a dew point of 65 ° C. Next, nitriding treatment at 750 ° C. for 30 seconds is performed with N 2 ,
The amount of N 2 after nitriding was adjusted to approximately 200 ppm in a mixed gas of H 2 and NH 3 . After that, an annealing separator containing MgO and TiO 2 as main components was applied, and finish annealing was performed at 1200 ° C. for 20 hours. After that, tension coating containing chromic anhydride and aluminum phosphate as main components was applied. Cooling condition after hot-rolled sheet annealing (R ° C / sec) -Agin during cold rolling
FIG. 1 shows the relationship between g temperature (T ° C.) and iron loss characteristics.
【００２３】この図から４００−１０Ｒ≦Ｔ≦６９０−
１２Ｒの範囲で非常に優れた低鉄損材が得られることが
分かる。熱延板焼鈍の高温側の温度は９５０℃〜１１５
０℃の範囲とする。この温度より低くても高くても一次
再結晶粒の粒径成長が困難になり高Ｂ8 特性が得られ難
い。この焼鈍時間は１８０秒以内とする。この時間を超
しても特別の効果は認められない。From this figure, 400-10R≤T≤690-
It is understood that a very excellent low iron loss material can be obtained in the range of 12R. The temperature on the high temperature side of hot-rolled sheet annealing is 950 ° C to 115 ° C.
It shall be in the range of 0 ° C. If the temperature is lower or higher than this temperature, it is difficult to grow the grain size of the primary recrystallized grains, and it is difficult to obtain high B 8 characteristics. This annealing time is within 180 seconds. No special effect is observed even if this time is exceeded.
【００２４】低温側の温度は８００〜９５０℃の範囲と
する。この温度域がＡｌＮ析出を促進させ一次再結晶粒
の粒径調整を容易にさせる他、僅かなγ相を残存させ
て、この後の急冷によりｈａｒｄ相を形成させ適正な一
次再結晶集合組織を得る。焼鈍時間は３０〜３００秒が
よい。The temperature on the low temperature side is in the range of 800 to 950.degree. This temperature range promotes AlN precipitation and facilitates the grain size adjustment of primary recrystallized grains, and also leaves a slight γ phase, which is then rapidly cooled to form a hard phase to form an appropriate primary recrystallized texture. obtain. The annealing time is preferably 30 to 300 seconds.
【００２５】冷却規制温度下限を３００℃とした理由
は、急冷によって材質硬度に十分影響を与える温度であ
るからである。勿論この温度以下も急冷することが好ま
しい。冷延途中段階のＡｇｉｎｇ温度は１００〜３００
℃で鉄損改善の効果が大きい。The reason why the lower limit of cooling regulation temperature is set to 300 ° C. is that it is the temperature at which the material hardness is sufficiently affected by the rapid cooling. Of course, it is preferable to rapidly cool below this temperature. Aging temperature during the cold rolling is 100 to 300
Greatly improves iron loss at ℃.
【００２６】Ａｇｉｎｇ時間は１分以上であれば効果が
でるが、好ましくは５分程度が良い。これより長くなっ
ても効果は十分ある。なお工業的にはリバース圧延機に
よる高温圧延域あるいは加熱装置設置により対応でき
る。本発明においては優れた磁気特性を得る上で、脱炭
焼鈍後の一次再結晶粒径とその集合組織の調整が重要で
ある。適正な一次再結晶粒径は１５μｍ以上通常２０〜
２６μｍと高温スラブ加熱材の１０μｍ程度に比べて大
きい。The aging time is effective if it is 1 minute or more, but preferably about 5 minutes. Even if it is longer than this, the effect is sufficient. Incidentally, industrially, it can be dealt with by setting up a high temperature rolling zone by a reverse rolling mill or installing a heating device. In the present invention, it is important to adjust the primary recrystallized grain size and its texture after decarburization annealing in order to obtain excellent magnetic properties. An appropriate primary recrystallized grain size is 15 μm or more, usually 20 to
26 μm, which is larger than about 10 μm of the high temperature slab heating material.
【００２７】一般に集合組織の面からは粒径が大きくな
ることは好ましくない。このため、より厳密な集合組織
調整が必要となってくる。本発明の冷延前の鋼板の冷却
速度と冷延時のＡｇｉｎｇの組み合わせは将にこの冷延
集合組織を適正化し好ましい一次再結晶集合組織を得て
いるものと考えられる。冷間圧延率は高いＢ8 値を得る
ために８０％以上とする。Generally, it is not preferable that the grain size is large in terms of texture. For this reason, more rigorous organization adjustment is needed. It is considered that the combination of the cooling rate of the steel sheet before cold rolling and the aging at the time of cold rolling of the present invention generally optimizes this cold rolled texture to obtain a preferable primary recrystallization texture. The cold rolling rate is 80% or more in order to obtain a high B 8 value.
【００２８】脱炭焼鈍は脱炭を行う他に、一次再結晶組
織の調整及び被膜形成に必要な酸化層を形成させる役割
がある。これは通常８００〜９００℃の温度域で湿水
素、窒素ガス中で行う。次に窒化処理について述べる。
窒化処理は通常脱炭焼鈍後に６５０〜８５０℃の温度域
でストリップを走行せしめる状態下で行う。In addition to decarburization, the decarburization annealing has a role of adjusting the primary recrystallization structure and forming an oxide layer necessary for forming a film. This is usually performed in a temperature range of 800 to 900 ° C. in wet hydrogen and nitrogen gas. Next, the nitriding process will be described.
The nitriding treatment is usually performed after decarburization annealing in a state where the strip is run in a temperature range of 650 to 850 ° C.
【００２９】雰囲気ガスは特にこだわらないが、一般に
水素ガス、窒素ガス、アンモニアガスの混合ガスを用い
る。この後、ＭｇＯ、ＴｉＯ2 を主成分とするスラリー
を塗布し、１１００℃以上の温度で仕上げ焼鈍を公知の
方法で行う。The atmosphere gas is not particularly limited, but generally a mixed gas of hydrogen gas, nitrogen gas and ammonia gas is used. Then, a slurry containing MgO and TiO 2 as a main component is applied, and finish annealing is performed at a temperature of 1100 ° C. or higher by a known method.
【００３０】[0030]
［実施例１］Ｃ：０．０５８％、Ｓｉ：３．４５％、Ｍ
ｎ：０．１０％、Ｓ：０．００７％、酸可溶性Ａｌ：
０．０２７％、Ｓｎ：０．０５％、Ｃｒ：０．１２％、
Ｎ：０．００８０％を含むスラブを１１５０℃に加熱し
た後熱延し２．６mmの熱延板を造った。[Example 1] C: 0.058%, Si: 3.45%, M
n: 0.10%, S: 0.007%, acid-soluble Al:
0.027%, Sn: 0.05%, Cr: 0.12%,
A slab containing N: 0.0080% was heated to 1150 ° C. and then hot-rolled to produce a hot-rolled sheet of 2.6 mm.
【００３１】次いで熱延板焼鈍を１０８０℃×３０sec
＋８５０℃×２min の焼鈍をした後、８５０℃〜３００
℃までの冷却速度を１０℃/secと、４０℃/secとして室
温まで冷却した。この後酸洗し０．３０mmまで冷延し
た。この冷延の途中板厚段階において表３のようなＡｇ
ｉｎｇ処理を行った。Then, hot-rolled sheet annealing is performed at 1080 ° C. for 30 seconds.
After annealing at + 850 ° C x 2min, 850 ° C-300
The cooling rate to 10 ° C. was set to 10 ° C./sec and 40 ° C./sec to cool to room temperature. This was followed by pickling and cold rolling to 0.30 mm. Ag in the plate thickness stage during this cold rolling as shown in Table 3
The ing process was performed.
【００３２】[0032]
【表３】 [Table 3]
【００３３】次いで脱炭焼鈍を８３０℃の温度でＮ2 ：
２５％、Ｈ2 ：７５％、露点６５℃の雰囲気中で行っ
た。次いで７５０℃×３０秒の窒化処理をＮ2 、Ｈ2 、
ＮＨ3の混合ガス中で行い、窒化後のＮ2 量をほぼ２０
０ppm に調整した。この後ＭｇＯとＴｉＯ2 を主成分と
する焼鈍分離剤を塗布し、１２００℃×２０時間の仕上
げ焼鈍を行った。この後水洗し、無水クロム酸、リン酸
アルミニウムを主成分とする張力コーティングを施し
た。磁気特性を表４に示す。本発明の範囲で非常に優れ
た鉄損値を示している。Then decarburization annealing was carried out at a temperature of 830 ° C. with N 2 :
It was carried out in an atmosphere of 25%, H 2 : 75%, and a dew point of 65 ° C. Next, nitriding treatment at 750 ° C. for 30 seconds is performed with N 2 , H 2 ,
It is performed in a mixed gas of NH 3 and the amount of N 2 after nitriding is set to about 20.
Adjusted to 0 ppm. After that, an annealing separator containing MgO and TiO 2 as main components was applied, and finish annealing was performed at 1200 ° C. for 20 hours. After that, it was washed with water and subjected to tension coating containing chromic anhydride and aluminum phosphate as main components. The magnetic properties are shown in Table 4. It shows a very good iron loss value within the range of the present invention.
【００３４】[0034]
【表４】 [Table 4]
【００３５】[0035]
【発明の効果】本発明のの低温スラブ加熱法により、磁
気特性の優れた一方向性電磁鋼板を得ることができる。According to the low temperature slab heating method of the present invention, it is possible to obtain a grain-oriented electrical steel sheet having excellent magnetic properties.
【図１】Ａｇｉｎｇ温度と熱延板焼鈍の冷速と磁気特性
の関係を示す図表である。FIG. 1 is a chart showing a relationship between an aging temperature, a cold speed of hot-rolled sheet annealing, and magnetic properties.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 山崎 幸司 北九州市戸畑区飛幡町１番１号 新日本 製鐵株式会社 八幡製鐵所内 (72)発明者 黒木 克郎 北九州市戸畑区大字中原46−59 日鐵プ ラント設計株式会社内 (56)参考文献 特開 昭61−60896（ＪＰ，Ａ) (58)調査した分野(Int.Cl.7，ＤＢ名) C21D 8/12 C21D 9/46 501 C22C 38/00 303 C22C 38/06 H01F 1/16 ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Koji Yamazaki 1-1 Tobahata-cho, Tobata-ku, Kitakyushu City Shin Nippon Steel Co., Ltd. Yawata Works (72) Inventor Katsuro Kuroki 46-59 Nakahara, Tobata-ku, Kitakyushu Nittetsu Plant Design Co., Ltd. (56) Reference JP-A-61-60896 (JP, A) (58) Fields investigated (Int.Cl. 7 , DB name) C21D 8/12 C21D 9/46 501 C22C 38/00 303 C22C 38/06 H01F 1/16
Claims (3)
ラブを１２８０℃以下の温度に加熱した後、熱延し、最
終冷延前に焼鈍を実施し、一回または中間焼鈍を介挿す
る二回以上の圧延でその最終圧延率を８０％以上とし、
ついで脱炭焼鈍、窒化処理、仕上げ焼鈍をする一方向性
電磁鋼板の製造において、最終冷延前の鋼板の焼鈍を２
段均熱とし、高温側の温度、均熱時間を９５０〜１１５
０℃、１８０秒以内、低温側の温度、均熱時間を８００
〜９５０℃、３０〜３００秒とし、８００〜９５０℃の
温度域から３００℃までの平均冷却速度をＲ℃/secで冷
却し、最終冷延の複数回のパスの少なくとも１回以上鋼
板に１００〜３００℃の温度範囲で下記条件を満たすＴ
℃で１分以上の時間保持する熱効果を与えることを特徴
とする低鉄損高磁束密度一方向性電磁鋼板の製造方法。 ４００−１０Ｒ≦Ｔ≦６９０−１２Ｒ1. By weight ratio, C: 0.025 to 0.075%, Si: 2.5 to 4.5%, Mn: 0.050 to 0.45%, S ≤ 0.015%, acid soluble Al: 0.015 to .040%, after heating the electrical steel slab containing N ≦ 0.010% the balance being Fe and unavoidable impurities to a temperature of 1280 ° C. or less, hot rolled, the outermost
Annealing is performed before final cold rolling, and the final rolling rate is set to 80% or more by rolling once or twice or more with intermediate annealing.
Then, in the production of unidirectional electrical steel sheet that undergoes decarburization annealing, nitriding treatment, and finish annealing, annealing of the steel sheet before final cold rolling is
Stage soaking, high temperature side, soaking time 950-115
0 ℃, within 180 seconds, low temperature side, soaking time 800
To 950 ° C., 30 to 300 seconds, the average cooling rate from the temperature range of 800 to 950 ° C. to 300 ° C. is cooled at R ° C./sec, and the steel sheet is subjected to at least one or more times of multiple passes of final cold rolling 100 times or more. T satisfying the following conditions in the temperature range of ~ 300 ° C
A method for producing a low iron loss high magnetic flux density unidirectional electrical steel sheet, which is characterized by imparting a thermal effect of holding at ℃ for 1 minute or more. 400-10R ≦ T ≦ 690-12R
避的不純物からなる電磁鋼スラブを出発素材とする請求
項１記載の方法。2. By weight ratio, C: 0.025 to 0.075%, Si: 2.5 to 4.5%, Mn: 0.050 to 0.45%, S ≤ 0.015%, acid Soluble Al: 0.015 to 0.040%, N ≤ 0.010%, Sn: 0.02 to 0.15%, Cr: 0.05 to 0.30%, and the balance Fe and unavoidable impurities 2. The method according to claim 1, wherein said electromagnetic steel slab is used as a starting material.
避的不純物からなる電磁鋼スラブを出発素材とする請求
項１記載の方法。3. By weight ratio, C: 0.025 to 0.075%, Si: 2.5 to 4.5%, Mn: 0.050 to 0.45%, S ≤ 0.015%, acid Soluble Al: 0.015 to 0.040%, N ≤ 0.010%, Sn: 0.02 to 0.15%, Cr: 0.05 to 0.30%, Cu: 0.03 to 0.30. The method according to claim 1, wherein an electromagnetic steel slab containing 10% by weight and the balance Fe and unavoidable impurities is used as a starting material.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP20105195A JP3390109B2 (en) | 1995-08-07 | 1995-08-07 | Low iron loss high magnetic flux density |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP20105195A JP3390109B2 (en) | 1995-08-07 | 1995-08-07 | Low iron loss high magnetic flux density |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0949022A JPH0949022A (en) | 1997-02-18 |
| JP3390109B2 true JP3390109B2 (en) | 2003-03-24 |
Family
ID=16434591
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|---|---|---|---|
| JP20105195A Expired - Lifetime JP3390109B2 (en) | 1995-08-07 | 1995-08-07 | Low iron loss high magnetic flux density |
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| Country | Link |
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| KR100435478B1 (en) * | 1999-12-27 | 2004-06-10 | 주식회사 포스코 | A method for manufacturing grain oriented electrical steel sheet with high magnetic induction using low temperature slab reheating process |
| KR100406420B1 (en) * | 1999-12-27 | 2003-11-20 | 주식회사 포스코 | A method for manufacturing grain oriented electrical steel sheet with high permeability |
| US7887645B1 (en) | 2001-05-02 | 2011-02-15 | Ak Steel Properties, Inc. | High permeability grain oriented electrical steel |
| KR100721823B1 (en) * | 2005-12-22 | 2007-05-25 | 주식회사 포스코 | A hot rolling method for grain-oriented electrical steel sheet |
| KR100825305B1 (en) * | 2006-12-28 | 2008-04-28 | 주식회사 포스코 | Method for manufacturing the grain-oriented electrical steel sheets having improved magnetic property |
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1995
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| JPH0949022A (en) | 1997-02-18 |
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