JP4383181B2 - Non-oriented electrical steel sheet with excellent uniformity of magnetic properties in coil and high production yield, and method for producing the same - Google Patents
Non-oriented electrical steel sheet with excellent uniformity of magnetic properties in coil and high production yield, and method for producing the same Download PDFInfo
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- JP4383181B2 JP4383181B2 JP2004009220A JP2004009220A JP4383181B2 JP 4383181 B2 JP4383181 B2 JP 4383181B2 JP 2004009220 A JP2004009220 A JP 2004009220A JP 2004009220 A JP2004009220 A JP 2004009220A JP 4383181 B2 JP4383181 B2 JP 4383181B2
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- 229910052742 iron Inorganic materials 0.000 claims description 18
- 238000005097 cold rolling Methods 0.000 claims description 7
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Description
本発明は、モーターやトランス用の鉄芯材料として用いられる、鉄損および磁束密度ともに極めて優れた無方向性電磁鋼板およびその製造方法に関するものである。 The present invention relates to a non-oriented electrical steel sheet, which is used as an iron core material for motors and transformers, and has excellent iron loss and magnetic flux density, and a method for producing the same.
無方向性電磁鋼板は、重電機器、家電用など各種モーター、変圧器、安定器等の鉄芯材料として広く用いられている。商業的には鉄損でグレード分けされ、モーターやトランスの設計特性に合せて使い分けがなされている。近年、エネルギー節減の観点から一層の低鉄損化が、また、電気機器の小型化の観点から一層の高磁束密度化が要求されており、鉄損、磁束密度ともにさらに優れた鋼板の開発が強く要望されている。 Non-oriented electrical steel sheets are widely used as iron core materials for various motors, transformers, ballasts and the like for heavy electrical equipment and home appliances. Commercially, the grades are classified by iron loss, and they are used according to the design characteristics of the motor and transformer. In recent years, there has been a demand for further reduction of iron loss from the viewpoint of energy saving and further increase in magnetic flux density from the viewpoint of miniaturization of electrical equipment. There is a strong demand.
このような背景で、これまでに鉄損や磁束密度の改善を目的とした多くの技術が開示され、成分の最適化、特殊元素の添加、熱延板焼鈍の付与、仕上焼鈍の高温化などが実用化されている。これらの技術が制御しようとしている因子の一つは析出物の形態であり、材質特性に強く影響を及ぼすため重要な因子と考えられている。 Against this background, many technologies aimed at improving iron loss and magnetic flux density have been disclosed so far, including optimization of components, addition of special elements, provision of hot-rolled sheet annealing, higher temperature of finish annealing, etc. Has been put to practical use. One of the factors that these technologies are trying to control is the form of precipitates and is considered to be an important factor because it strongly affects the material properties.
一般に鋼板中に微細な析出物が存在すると、焼鈍時の粒成長を阻害するとともに磁壁移動の障害となり鉄損上昇および特に低磁場での磁束密度低下の原因となる。特に、微細な硫化物はこの悪影響が大きいことが知られており、磁気特性を向上させるには、硫化物量を低減するか粗大化するかし無害化する必要がある。この目的で例えば特許文献１にはＣａ、Ｍｇ等の強力な硫化物形成元素を添加し硫化物を粗大化する技術が開示されている。しかし、これらは一方で特殊な酸化物を形成するため、鋳造時のノズル閉塞等を引起す原因となるとともに、硫化物粗大化効果も安定しない面がある。 In general, when fine precipitates are present in a steel sheet, it inhibits grain growth during annealing and hinders domain wall movement, leading to an increase in iron loss and a decrease in magnetic flux density, particularly in a low magnetic field. In particular, fine sulfides are known to have a large adverse effect, and in order to improve magnetic properties, it is necessary to reduce or coarsen the amount of sulfides or make them harmless. For this purpose, for example, Patent Document 1 discloses a technique for adding a strong sulfide-forming element such as Ca or Mg to coarsen the sulfide. However, since they form a special oxide on the other hand, they cause nozzle clogging at the time of casting, and the effect of the coarsening of sulfides is not stable.
このような特殊元素を添加しない技術としては特許文献２，３に開示されているようなＣｕ硫化物に注目した技術が開示されている。この技術は微細なＣｕ硫化物の制御に注目した点では技術的な進歩性は著しいが、その制御方法が適正ではなく効果の安定性に問題があった。 As a technique not adding such a special element, a technique focusing on Cu sulfide as disclosed in Patent Documents 2 and 3 is disclosed. Although this technology is remarkable in terms of technical progress in terms of controlling fine Cu sulfide, the control method is not appropriate and there is a problem in stability of the effect.
本発明者らは、微細なＣｕ硫化物が熱延時に形成されるものであり、効果を安定的に得るには従来考えられているより微細な硫化物の制御が必要で、このためには熱延条件の制御を欠くことができないことを知見し特許文献４の技術を開示した。この技術によって硫化物に起因する悪影響をほぼ取り除くことが可能になったが、特定の成分を有する材料にこの技術を適用した場合、実際の製造、使用においては以下のような問題が生ずることが明らかとなった。すなわち、従来よりＣｕ、Ｓ、Ａｌ含有量が低く純度が高く、磁気特性としては純度が低い材料より磁気特性のレベルが良好な材料においては、通常コイル状に製造される鋼板のコイル内の部位による材質の変動が期待する範囲内に収まらない場合があり、コイル端部を切り捨てる必要が生じ製造歩留まりが劣化したり、製造したモーターの特性にばらつきが生ずることがある。 The inventors of the present invention form fine Cu sulfide during hot rolling, and in order to obtain the effect stably, it is necessary to control fine sulfide more conventionally considered. Knowing that control of hot rolling conditions is indispensable, the technique of Patent Document 4 was disclosed. Although this technology has made it possible to almost eliminate the adverse effects caused by sulfides, when this technology is applied to materials having specific components, the following problems may occur in actual production and use. It became clear. That is, in a material having a lower Cu, S, Al content and higher purity, and a magnetic property level better than that of a material having lower purity than the conventional material, a portion in a coil of a steel sheet usually manufactured in a coil shape In some cases, the variation of the material due to the above may not be within the expected range, and it is necessary to cut off the end of the coil, which may deteriorate the manufacturing yield or cause variations in the characteristics of the manufactured motor.
本発明はこのような状況に鑑みなされたもので、実際の操業においてコイル内の材質変動が生じる原因を明確にし、その抑制に必要な成分と製造条件を明確にすることにより磁気特性が良好なだけでなく、コイル内の磁気特性の均一性に優れ良好な特性を安定して得ることができ、製造歩留まりが高い無方向性電磁鋼板を製造する方法を提供するものである。 The present invention has been made in view of such a situation. By clarifying the cause of material fluctuation in the coil in actual operation, and by clarifying the components and manufacturing conditions necessary for the suppression, the magnetic characteristics are good. In addition, the present invention provides a method for producing a non-oriented electrical steel sheet that is excellent in uniformity of magnetic properties in a coil and can stably obtain good properties and has a high production yield.
本発明者らは、微細なＣｕ硫化物を制御するポイントが熱延条件にあったことを明確にした経験から、磁気特性のコイル内変動が生ずる原因も熱延条件にあると想定し熱延条件について詳細な検討を行い、Ｃｕ硫化物形態の最適な制御には溶解析出挙動に関して速度論的な考慮を行うことが不可欠であるとの結論に達し、本発明を完成したものである。 From the experience of clarifying that the point of controlling fine Cu sulfide was in the hot rolling conditions, the present inventors assumed that the cause of the fluctuation of the magnetic properties in the coil is also in the hot rolling conditions. The present invention has been completed by conducting a detailed study of the conditions and reaching the conclusion that it is essential to consider kinetics regarding dissolution and precipitation behavior for optimal control of Cu sulfide morphology.
（１）質量％でＣ：０．０４０％以下、Ｓｉ：０．０５〜３．５％、Ｍｎ：１．０％以下かつＳｉ／２以下、Ａｌ：０．００５％以下、Ｓ：０．００２％以下、Ｐ：０．１５％以下、Ｎ：０．０２０％以下、Ｃｕ：０．１０％以下を含み、残部Ｆｅおよび不可避的不純物からなり、（Ｃｕ硫化物であるＳ）／（鋼中Ｓ）≦０．２であり、かつ熱延コイルを基準としたコイル長手位置において先端より２ｍ位置の磁気特性ＸT、後端より２ｍ位置の磁気特性ＸB、中央部の磁気特性ＸMについて式１を満足し、前記各位置において鋼板中の直径０．０２μｍ以上０．１０μｍ以下のＣｕを含有する硫化物の数密度が０．５個／μｍ3以下であることを特徴とする無方向性電磁鋼板。
（Ｘmax−Ｘmin）／Ｘmin＊１００ ≦２５ ・・・式１
ただし、ＸT、ＸM、ＸBの内の最大値をＸmax
ＸT、ＸM、ＸBの内の最小値をＸmin
磁気特性はＢ10、Ｂ25、Ｂ50（単位Ｔ）、Ｗ15/50、Ｗ10/400（単位Ｗ／ｋｇ）の
いずれか１以上。
（２）質量％でＣ：０．０４０％以下、Ｓｉ：０．０５〜３．５％、Ｍｎ：１．０％以下かつＳｉ／２以下、Ａｌ：０．００５％以下、Ｓ：０．００２％以下、Ｐ：０．１５％以下、Ｎ：０．０２０％以下、Ｃｕ：０．１０％以下を含み、残部Ｆｅおよび不可避的不純物からなり、（Ｃｕ硫化物であるＳ）／（Ｍｎ硫化物であるＳ）≦０．２であり、かつ熱延コイルを基準としたコイル長手位置において先端より２ｍ位置の磁気特性ＸT、後端より２ｍ位置の磁気特性ＸB、中央部の磁気特性ＸMについて式１を満足し、各位置において鋼板中の直径０．０２μｍ以上０．１０μｍ以下のＣｕを含有する硫化物の数密度が０．５個／μｍ3以下であることを特徴とする無方向性電磁鋼板。
（３）熱延コイルを基準としたコイル長手位置において先端より２ｍ位置、後端より２ｍ位置、中央部の各位置において鋼板中の直径０．０２μｍ以上１．０μｍ以下のＣｕを含有する硫化物について、（平均直径が０．０５μｍ以上）または（直径が０．０５μｍ以下であるものの個数の割合が５０％以下）であることを特徴とする（１）もしくは（２）に記載の無方向性電磁鋼板。
(1) In mass%, C: 0.040% or less, Si: 0.05 to 3.5%, Mn: 1.0% or less and Si / 2 or less, Al: 0.005% or less, S: 0.00. 00 2 % or less, P: 0.15% or less, N: 0.020% or less, Cu: 0.10% or less, and the balance consisting of Fe and unavoidable impurities (S which is Cu sulfide) / ( In the steel, S) ≦ 0.2, and in the coil longitudinal position with respect to the hot rolled coil, the magnetic characteristic X T at the position 2 m from the front end, the magnetic characteristic X B at the position 2 m from the rear end, the magnetic characteristic X at the center portion The non-direction characterized in that the number density of sulfides containing Cu having a diameter of 0.02 μm or more and 0.10 μm or less in the steel sheet at each position is 0.5 / μm 3 or less, satisfying Equation 1 for M Electrical steel sheet.
(Xmax−Xmin) / Xmin * 100 ≦ 25 (1)
However, the maximum value of X T , X M , and X B is set to Xmax
The minimum value of X T , X M , and X B is Xmin
Magnetic properties B 10, B 25, B 50 ( unit T), W 15/50, W 10/400 any one or more (in W / kg).
(2) In mass%, C: 0.040% or less, Si: 0.05 to 3.5%, Mn: 1.0% or less and Si / 2 or less, Al: 0.005% or less, S: 0.00. 00 2 % or less, P: 0.15% or less, N: 0.020% or less, Cu: 0.10% or less, and the balance consisting of Fe and unavoidable impurities (S which is Cu sulfide) / ( Mn sulfide S) ≦ 0.2, and the magnetic characteristic X T at the position 2 m from the tip at the coil longitudinal position with respect to the hot rolled coil, the magnetic characteristic X B at the position 2 m from the rear end, The magnetic property X M satisfies Formula 1 and the number density of sulfides containing Cu having a diameter of 0.02 μm or more and 0.10 μm or less in the steel sheet at each position is 0.5 piece / μm 3 or less. Non-oriented electrical steel sheet.
(3) Sulfide containing Cu having a diameter of 0.02 μm or more and 1.0 μm or less in the steel sheet at each position of 2 m from the front end, 2 m from the rear end, and the central portion at the coil longitudinal position based on the hot rolled coil (The average diameter is 0.05 μm or more) or (the ratio of the number of those having a diameter of 0.05 μm or less is 50% or less), the non-directionality according to (1) or (2) Electrical steel sheet.
また、そのための製造方法として、In addition, as a manufacturing method therefor,
（４）（１）〜（３）のいずれか１項に記載の鋼板の製造方法として、連続鋳造後のスラブを９５０℃〜５００℃の温度域での滞在時間が１０分以上となるように冷却または保熱した後、これ以下の温度に保持することなく加熱炉に挿入し、スラブ加熱中に加熱炉内においてスラブの全ての部位について、スラブ温度が１２００℃を超えないように加熱し、１１００℃以下の温度で加熱炉から取り出して熱間圧延を開始し、熱間圧延後酸洗し、冷間圧延をした後、再結晶焼鈍することを特徴とする無方向性電磁鋼板の製造方法。(4) As a manufacturing method of the steel sheet according to any one of (1) to (3), the stay time in the temperature range of 950 ° C. to 500 ° C. of the slab after continuous casting is 10 minutes or more. After cooling or heat retention, it is inserted into a heating furnace without maintaining a temperature below this, and during the slab heating, all the parts of the slab are heated so that the slab temperature does not exceed 1200 ° C., A method for producing a non-oriented electrical steel sheet, wherein hot rolling is started at a temperature of 1100 ° C. or less, hot rolling is started, pickling is performed after hot rolling, cold rolling is performed, and then recrystallization annealing is performed. .
（５）スラブ加熱炉中の平均加熱速度が４．０℃／分以下であることを特徴とする（４）に記載の無方向性電磁鋼板の製造方法。(5) The method for producing a non-oriented electrical steel sheet according to (4), wherein an average heating rate in the slab heating furnace is 4.0 ° C./min or less.
（６）スラブ加熱炉内の滞在時間が３００分以上であることを特徴とする（４）〜（５）のいずれかに記載の無方向性電磁鋼板の製造方法。(6) The method for producing a non-oriented electrical steel sheet according to any one of (4) to (5), wherein a residence time in the slab heating furnace is 300 minutes or more.
本発明によれば、特性が良好な無方向性電磁鋼板についてコイル内の全体にわたって良好にすることで鋼板製造歩留まりを大幅に向上することができるとともに、鋼板を使用して製造される製品の品質を安定させることが可能となる。 According to the present invention, the non-oriented electrical steel sheet having good characteristics can be improved over the entire coil to significantly improve the steel sheet manufacturing yield, and the quality of products manufactured using the steel sheet. Can be stabilized.
以下、本発明の詳細を説明する。まず本発明を達成するに至った基本的な実験結果を示す。 Details of the present invention will be described below. First, basic experimental results that led to the achievement of the present invention will be described.
図１は、０．００２％Ｃ−０．７％Ｓｉ−０．５％Ｍｎ−０．００２％Ｓ−０．０６％Ｐ−０％Ａｌ−０．００６％Ｃｕ−０．００２％Ｎ鋼を溶製し、これを連続鋳造で鋼片となし、熱延スラブ加熱条件を表１のＡ〜Ｆのように変えて熱間圧延し、板厚２．２ｍｍの熱延板とし、さらに、熱延板を酸洗した後、０．５０ｍｍに冷延し、次いで７５０℃３０秒の連続焼鈍を実施し製品とした鋼板の、熱延コイルＭ部相当部より測定用サンプルを切り出し、歪取り焼鈍として７５０℃２時間の熱処理を行い得られたサンプルの磁気特性である。 FIG. 1 shows 0.002% C-0.7% Si-0.5% Mn-0.002% S-0.06% P-0% Al-0.006% Cu-0.002% N steel. This is made into a steel slab by continuous casting, hot-rolled slab heating conditions are changed as shown in A to F of Table 1, and hot-rolled to a thickness of 2.2 mm, After pickling the hot-rolled sheet, it is cold-rolled to 0.50 mm, then subjected to continuous annealing at 750 ° C. for 30 seconds, and a sample for measurement is cut out from the portion corresponding to the hot-rolled coil M part of the steel sheet to remove distortion. It is a magnetic characteristic of the sample obtained by performing the heat processing for 2 hours at 750 degreeC as annealing.
後段の加熱時間ｔ１を長くするほど鉄損は改善されるが、加熱の前段で一旦１１５０℃以上の高温にさらされた鋼Ａ〜Ｃは、後段で長時間の低温保持を行っても高温にさらされなかった材料と同等まで特性が回復しないことがわかる。 Although the iron loss is improved as the heating time t1 in the subsequent stage is lengthened, the steels A to C that have been once exposed to a high temperature of 1150 ° C. or higher in the previous stage of heating have a high temperature even if they are kept at a low temperature for a long time in the subsequent stage. It can be seen that the properties do not recover to the same extent as the unexposed material.
一方、図２は同じ連続鋳造鋼片を、熱延条件を表１のＧ〜Ｉのように変えて、上記と同様の処理を行ったサンプルの特性である。低温で加熱されていた材料でも、短時間といえども一旦高温にさらされてしまうと特性が急激に劣化することがわかる。 On the other hand, FIG. 2 shows the characteristics of a sample in which the same continuous cast steel slab was subjected to the same treatment as described above while changing the hot rolling conditions as shown in Tables 1 to 6. It can be seen that even if the material has been heated at a low temperature, the characteristics deteriorate rapidly once it is exposed to a high temperature even for a short time.
これらの材料のうち代表的なものについて硫化物を観察した結果が図３、４である。析出物はほぼ全てがＣｕ硫化物であるが、図３は１１００℃以上の温度に到達させることなく１０５０℃で６０分加熱した材料、図４は加熱時１２００℃まで過加熱した後１０５０℃で６０分加熱した材料である。高温への加熱を抑制した材料では微細なＣｕ硫化物が減少していることがわかる。 The results of observing sulfides for typical materials among these materials are shown in FIGS. Almost all of the precipitates are Cu sulfides, but FIG. 3 is a material heated at 1050 ° C. for 60 minutes without reaching a temperature of 1100 ° C. or higher, and FIG. 4 is at 1050 ° C. after overheating to 1200 ° C. during heating. It is a material heated for 60 minutes. It can be seen that fine Cu sulfide is reduced in the material that suppresses heating to high temperature.
また、図５は、上記と同様の工程で製造した０．００２％Ｃ−１．２％Ｓｉ−０．５％Ｍｎ−０．００２％Ｓ−０．０２％Ｐ−０％Ａｌ−０．００２％Ｎ鋼のＣｕ量を変化させた場合のコイル内のＷ15/50の変動率である。変動率は式１に従うものである。熱延条件等に加えＣｕ量の適当な制御によって材質ばらつきをさらに低減できることが明確である。 5 shows 0.002% C-1.2% Si-0.5% Mn-0.002% S-0.02% P-0% Al-0. It is the fluctuation rate of W 15/50 in the coil when the amount of Cu of 002% N steel is changed. The rate of change is according to Equation 1. It is clear that material variation can be further reduced by appropriate control of the amount of Cu in addition to hot rolling conditions.
次に本発明鋼の成分範囲をその限定理由とともに説明する。（含有量は全て質量％である。）
Ｃは、固溶Ｃとして磁気特性を向上させるため積極的に添加できるが過剰な添加は磁気特性を劣化させるので上限を０．０４０％とする。磁気時効性抑止の観点から冷延後に脱炭することも可能であるが、製造コストの観点からは０．００２０％が好ましい。
Next, the component range of the steel of the present invention will be described together with the reasons for limitation. (All contents are mass%.)
C can be positively added to improve the magnetic properties as solute C, but excessive addition degrades the magnetic properties, so the upper limit is made 0.040%. Although it is possible to decarburize after cold rolling from the viewpoint of suppressing magnetic aging, 0.0020% is preferable from the viewpoint of manufacturing cost.
Ｓｉは、磁気特性と通板性の兼ね合いから０．０５〜３．５％とする。これ以下では良好な磁気特性が得られず、これ以上では脆化のため製造工程での通板性が顕著に劣化する。 Si is set to 0.05 to 3.5% in view of the balance between magnetic properties and plate passing properties. Below this, good magnetic properties cannot be obtained, and above this, embrittlement causes a significant deterioration in the plate-passability in the manufacturing process.
Ｍｎは、一般的に硫化物を粗大化するため添加されるが、Ａｌ量が非常に低く鋼中に酸化物が多い本発明鋼では多量に添加するとＭｎ酸化物を形成し磁気特性が劣化する。この限界はＳｉ酸化物形成との兼ね合いでＳｉ含有量とも関係しており、１．０％以下かつＳｉ／２以下とする。このましくはＳｉ／３以下である。 Mn is generally added to coarsen sulfides. However, in the steel of the present invention having a very low Al content and a large amount of oxide in the steel, if added in a large amount, Mn oxide is formed and magnetic properties deteriorate. . This limit is also related to the Si content in consideration of Si oxide formation, and is 1.0% or less and Si / 2 or less. This is preferably Si / 3 or less.
Ｓは、硫化物量に直接関係し、含有Ｓ量が多いと磁気特性が劣化し、コイル内全ての部
位で特性が不良な値に揃ってくるため本発明が問題とするようなコイル内の特性変動が生
じ難くなる。上限は０．００３％とする。なお、０．００２％以下では従来技術において
はコイル内特性変動がより大きくなり本発明の効果がより顕著に現れる。本発明では、この０．００２％を上限として規定した。
S is directly related to the amount of sulfide, and if the content of S is large, the magnetic characteristics deteriorate, and the characteristics are inferior at all sites in the coil. Fluctuation is less likely to occur. The upper limit is 0.003%. If it is 0.002% or less, the characteristic variation in the coil becomes larger in the prior art, and the effect of the present invention appears more remarkably. In the present invention, this upper limit is defined as 0.002%.
Ｐは、過剰に含有すると磁束密度が劣化するので上限を０．１５％とする。一方、鋼板の硬度を高め打ち抜き性を向上させる作用があるので所望の打ち抜き硬度に応じ添加するだけでなく、本発明が対象としているＣｕ硫化物の形態にも好ましく作用する。好ましくは０．０２％以上、さらに好ましくは０．０３％以上、さらに好ましくは０．０４％以上、さらに好ましくは０．０６％以上、さらに好ましくは０．０７％以上とする。 If P is contained excessively, the magnetic flux density deteriorates, so the upper limit is made 0.15%. On the other hand, since it has the effect | action which raises the hardness of a steel plate and improves punching property, it not only adds according to desired punching hardness, but it acts favorably also on the form of Cu sulfide which this invention makes object. It is preferably 0.02% or more, more preferably 0.03% or more, further preferably 0.04% or more, more preferably 0.06% or more, and further preferably 0.07% or more.
Ａｌは、製鋼工程において脱酸のために添加されたものでも、鋼中に少なからず残存した場合、後工程でＡｌＮを形成しコイル内全ての部位で特性が不良な値に揃ってくるため、本発明が問題とするようなコイル内の特性変動が生じ難くなる。本発明では上限を０．００５％とする。好ましくは０．００４％以下、さらに好ましくは０．００３％以下、さらに好ましくは０．００２％以下、さらに好ましくは０．００１％以下、さらに好ましくは０も含む分析限界以下である。 Even if Al is added for deoxidation in the steelmaking process, if it remains in the steel, it will form AlN in the subsequent process, and the characteristics will be inferior at all parts in the coil. The characteristic fluctuation in the coil is less likely to be caused by the present invention. In the present invention, the upper limit is made 0.005%. Preferably it is 0.004% or less, More preferably, it is 0.003% or less, More preferably, it is 0.002% or less, More preferably, it is 0.001% or less, More preferably, it is below the analysis limit also including 0.
Ｎは、Ｃと同様に固溶Ｎとして磁気特性を向上させるため積極的に添加できるが過剰な添加は磁気特性を劣化させるので上限を０．０２０％とする。磁気時効性抑止の観点から冷延後に脱炭することも可能であるが、製造コストの観点からは０．００４０％が好しい。 N can be positively added to improve the magnetic characteristics as a solid solution N as in C, but excessive addition degrades the magnetic characteristics, so the upper limit is made 0.020%. Although it is possible to decarburize after cold rolling from the viewpoint of suppressing magnetic aging, 0.0040% is preferable from the viewpoint of manufacturing cost.
Ｃｕは本発明では特に重要な元素である。Ｃｕ硫化物の形態を制御するには多量に添加しＣｕ硫化物を粗大化させることで無害化し本発明が目的とするようなコイル内の材質均一性を得ることも可能である。しかし、添加コストや添加による磁束密度の劣化を避けるため上限を０．１０％とする。本発明では多量のＣｕ添加によらないコイル内材質の均一化を達成できるためあえて添加はしないことが好ましい。通常、鋼板中には原料や製造工程で混入するスクラップ等から不可避的に含有しているため０とすることは困難であるが、過度に少ないと本発明によってもＣｕ硫化物が不安定になりコイル内材質の変動が大きくなる。好ましくは０．００２〜０．０８％、さらに好ましくは０．００４〜０．０７％、さらに好ましくは０．００６〜０．０６％、さらに好ましくは０．００８〜０．０５％、さらに好ましくは０．０１０〜０．０４％とする。 Cu is a particularly important element in the present invention. In order to control the form of Cu sulfide, it is possible to make it harmless by adding a large amount and coarsening the Cu sulfide, and it is possible to obtain the material uniformity in the coil as intended by the present invention. However, the upper limit is made 0.10% in order to avoid the deterioration of the magnetic flux density due to the addition cost and addition. In the present invention, it is preferable not to add a material because a uniform material in the coil can be achieved without using a large amount of Cu. Usually, it is difficult to make it 0 because it is inevitably contained in the steel sheet from scraps mixed in the raw materials and manufacturing process, but if it is too small, Cu sulfide becomes unstable even by the present invention. Fluctuations in the coil material increase. Preferably it is 0.002-0.08%, More preferably, it is 0.004-0.07%, More preferably, it is 0.006-0.06%, More preferably, it is 0.008-0.05%, More preferably It shall be 0.010 to 0.04%.
本発明では窒化物が存在しない状況で、熱延条件によりＣｕ硫化物の形態を制御することでコイル内の材質を非常に小さく制御することが可能となる。このため本発明効果が発現するための窒化物形成元素、硫化物形成元素の量に上限がある。これらはトランプエレメントとして鉄鉱石、スクラップ他、製造工程で不可避的に混入し、また酸化物として鋼中に存在している場合は本発明効果への影響は小さくなるため限界を明確にすることは困難な面もあるが、本発明ではＴｉ：０．００２０％以下、Ｃａ：０．００２０％以下、Ｍｇ：０．００２０％以下、ＲＥＭ：０．００２０％以下、Ｃｒ：０．０５０％以下、Ｂ：０．００１０％以下とする。好ましくはＴｉ：０．００１２％以下、Ｃａ：０．００１２％以下、Ｍｇ：０．００１２％以下、ＲＥＭ：０．００１２％以下、Ｃｒ：０．０３０％以下、Ｂ：０．０００５％以下である。 In the present invention, it is possible to control the material in the coil very small by controlling the form of Cu sulfide according to hot rolling conditions in the absence of nitride. For this reason, there is an upper limit to the amount of nitride-forming element and sulfide-forming element for achieving the effects of the present invention. These are inevitably mixed in the manufacturing process as iron ore, scrap, etc. as a playing element, and if they are present in steel as oxides, the effect on the effect of the present invention is reduced, so the limit is not clarified. Although there are difficult aspects, in the present invention, Ti: 0.0020% or less, Ca: 0.0020% or less, Mg: 0.0020% or less, REM: 0.0020% or less, Cr: 0.050% or less, B: Set to 0.0010% or less. Preferably, Ti: 0.0012% or less, Ca: 0.0012% or less, Mg: 0.0012% or less, REM: 0.0012% or less, Cr: 0.030% or less, B: 0.0005% or less is there.
さらに磁気特性の更なる向上、強度、耐食性や疲労特性等の部材としての付加機能、また鋳造成や焼鈍通板性、スクラップ使用など製造工程上の生産等を向上させる目的でＳｎ，Ｗ、Ｍｏ、Ｓｂ、Ｎｉ、Ｃｏ等の微量元素を添加または不可避的に混入することは本発明の効果を何ら損なうものではない。 Furthermore, Sn, W, Mo for the purpose of further improving the magnetic properties, additional functions as members such as strength, corrosion resistance and fatigue properties, and the production in the manufacturing process such as casting, annealing, and scrap use. Addition or inevitable mixing of trace elements such as Sb, Ni and Co does not impair the effects of the present invention.
次に、本発明で用いるコイル内部位に関する定義について説明する。本発明の目的からして、各種の評価値は巨視的に見てコイル内の全ての部位において満足する必要があるが、コイル内の多くの部位についてこれを測定することは現実的でないため、本発明では以下の少なくとも３部位について満足するものとする。 Next, the definition regarding the site | part in a coil used by this invention is demonstrated. For the purpose of the present invention, it is necessary to satisfy various evaluation values macroscopically in all parts in the coil, but it is not realistic to measure this for many parts in the coil. In the present invention, the following at least three sites are satisfied.
本発明で対象としているコイル内の材質変動は後述のように熱延条件の変動によって生じていると考えられる。その変動は熱延コイルの端部と中央部で特に顕著であり代表的な変動を示す。端部とは熱延コイル長手位置における圧延先端部、終端部または幅位置におけるエッジ部を意味する。これらの部位は後述のように熱延時の熱履歴において加熱、冷却されやすいため、温度変化が比較的安定しているコイル中央部との材質差を生じやすい。長手位置の端部と幅位置の端部は類似した熱履歴を有するため特性も同様の挙動を示すが、特に長手位置の変動が大きく鋼板使用上に問題となりやすいので、本発明では長手位置における端部を対象とする。このとき最端よりどれくらいの距離の位置を対象とするかについては、ドーナツ型円柱状の熱延コイルの最内周側および最外周側を考え、コイル長手最端より２ｍの位置に相当する部位での特性を対象とする。 It is considered that the material fluctuation in the coil which is the subject of the present invention is caused by the fluctuation of hot rolling conditions as will be described later. The fluctuation is particularly remarkable at the end and center of the hot-rolled coil and shows a typical fluctuation. The end means the rolling tip at the longitudinal position of the hot rolled coil, the end at the end, or the edge at the width position. Since these portions are easily heated and cooled in the heat history during hot rolling as described later, a material difference from the coil central portion where the temperature change is relatively stable is likely to occur. Since the end of the longitudinal position and the end of the width position have similar thermal histories, the characteristics also show the same behavior, but since the variation of the longitudinal position is particularly large and is likely to be a problem when using the steel plate, in the present invention, Target the end. At this time, regarding the distance from the outermost end, the innermost side and the outermost side of the doughnut-shaped cylindrical hot-rolled coil are considered, and the portion corresponding to the position 2 m from the longest end of the coil Target the characteristics in
コイル長手中央部については、熱延コイル先端もしくは終端の１０ｍ程度以上中央に相当する部位であれば材質も安定するためこの範囲を対象とする。実際の特性や分析、析出物観察、さらには熱間圧延前のスラブにおける熱履歴等は全て熱延コイルでの各部位に相当する位置に換算して評価するものとする。なお、この時の幅位置は中央部での評価値を対象とする。以降、上述のコイル長手位置に関する名称として、熱延時の鋼材の進行方向を基準として前方の端部をＴ部、後方の端部をＢ部、中央部をＭ部と記述する。 About the coil longitudinal center part, since a material will also be stable if it is a site | part equivalent to the center of about 10 m or more of a hot-rolled coil front-end | tip or terminal, this range is made into object. Actual characteristics, analysis, observation of precipitates, and thermal history in the slab before hot rolling are all evaluated in terms of positions corresponding to the respective portions in the hot rolled coil. The width position at this time is for the evaluation value at the center. Hereinafter, as a name related to the above-described coil longitudinal position, a front end is described as a T portion, a rear end as a B portion, and a central portion as an M portion on the basis of the traveling direction of the steel material during hot rolling.
本発明の評価で重要なものは特性のばらつきである。 What is important in the evaluation of the present invention is variation in characteristics.
本発明鋼は熱延コイルを基準としたコイル長手位置において先端より２ｍ位置の磁気特性ＸT、後端より２ｍ位置の磁気特性ＸB、中央部の磁気特性ＸMについて式１を満足する必要がある。 In the steel of the present invention, the magnetic property X T at a position 2 m from the front end, the magnetic property X B at a position 2 m from the rear end, and the magnetic property X M at the center in the longitudinal position of the coil based on the hot-rolled coil must satisfy Formula 1. There is.
（Ｘmax−Ｘmin）／Ｘmin＊１００ ≦２５ ・・・式１
ただし、ＸT、ＸM、ＸBの内の最大値をＸmax
ＸT、ＸM、ＸBの内の最小値をＸmin
この値は、コイル内の特性変動の大きさのベース特性に対しての比率を％で表した数値となる。この値が２５を超える場合はコイル内に特性が不良な部位が存在し、その鋼板を使用して製造されたモーター等の品質にばらつきを生ずる原因となるため、鋼板製造歩留まりを下げてでも事前にその部位を切り捨てる必要が生じる。
(X max −X min ) / X min * 100 ≦ 25 (1)
However, the maximum value of X T , X M , and X B is set to X max
The minimum value of X T , X M , and X B is set to X min
This value is a numerical value representing the ratio of the magnitude of the characteristic variation in the coil to the base characteristic in%. If this value exceeds 25, there is a part with poor characteristics in the coil, which may cause variations in the quality of motors manufactured using the steel sheet. It is necessary to cut off the part.
式中で使用される磁気特性とは通常の電磁鋼板で評価される磁束密度または鉄損を指す。励磁電流や交流周波数などによりこれらの値は異なり、条件によっては測定誤差も含めて大きな変動を示す場合も考えられるため、本発明では磁束密度としてＢ10、Ｂ25、Ｂ50（単位Ｔ）、鉄損としてＷ15/50、Ｗ10/400（単位Ｗ／ｋｇ）、のいずれかを対象とするものとする。好ましくは式１の値が２０以下、さらに好ましくは１５以下、さらに好ましくは１０以下、さらに好ましくは５以下であり、本発明による最適な製造条件においては２以下も達成することが可能である。 The magnetic property used in the formula refers to the magnetic flux density or iron loss evaluated with a normal electromagnetic steel sheet. These values differ depending on the excitation current, AC frequency, etc., and depending on the conditions, there may be cases where large fluctuations including measurement errors are considered. Therefore, in the present invention, B 10 , B 25 , B 50 (unit T), The iron loss shall be either W 15/50 or W 10/400 (unit: W / kg). Preferably, the value of Formula 1 is 20 or less, more preferably 15 or less, more preferably 10 or less, and even more preferably 5 or less, and it is possible to achieve 2 or less under the optimum production conditions according to the present invention.
次に本発明の重要な制限要因である硫化物の状態について説明する。 Next, the state of sulfide, which is an important limiting factor of the present invention, will be described.
本発明では特にＣｕを含有する硫化物の制御が重要である。本発明では（Ｃｕ硫化物であるＳ）／（鋼中Ｓ）≦０．２、または、（Ｃｕ硫化物であるＳ）／（Ｍｎ硫化物であるＳ）≦０．２ と限定する。これは硫化物の中でも磁気特性への悪影響が特に大きいＣｕ硫化物の量を減らすことが重要となるためで、特に本発明鋼で主となるＭｎＳ等のＣｕを含有しない硫化物との比を小さくすることが重要である。十分な効果を得るにはこれらの比を０．１以下とすることが好ましく、さらに好ましくは０．０５以下とする。 In the present invention, control of a sulfide containing Cu is particularly important. In the present invention, (S which is Cu sulfide) / (S in steel) ≦ 0.2 or (S which is Cu sulfide) / (S which is Mn sulfide) ≦ 0.2. This is because it is important to reduce the amount of Cu sulfide that has a particularly large adverse effect on magnetic properties among sulfides, and in particular, the ratio of MnS and other sulfides that do not contain Cu, which is mainly used in the steel of the present invention. It is important to make it smaller. In order to obtain a sufficient effect, the ratio is preferably 0.1 or less, and more preferably 0.05 or less.
ここで（Ｃｕ硫化物であるＳ）とは鋼板を電解抽出して得た残渣中のＣｕ量を定量し、原子比でＣｕ／Ｓ＝２／１としてＳ量に換算したもの、（Ｍｎ硫化物であるＳ）とは鋼板を電解抽出して得た残渣中のＭｎ量を定量し、原子比でＭｎ／Ｓ＝１／１としてＳ量に換算したものである。ただし、Ａｌを含有しない本発明鋼では鋼中のＭｎは少なからず酸化物として存在しており、適当な方法により（Ｍｎ硫化物であるＳ）に換算されるべきＭｎ量を定量化する必要があることは言うまでもないことである。方法が妥当であれば、分析方法は特に限定されるものではない。 Here, (S which is Cu sulfide) is the amount of Cu in the residue obtained by electrolytic extraction of the steel sheet, and converted to S amount as Cu / S = 2/1 in atomic ratio, (Mn sulfide) S), which is a product, is obtained by quantifying the amount of Mn in the residue obtained by electrolytic extraction of a steel sheet, and converting it to the amount of S as Mn / S = 1/1 by atomic ratio. However, in the steel of the present invention that does not contain Al, Mn in the steel is present as an oxide, and it is necessary to quantify the amount of Mn to be converted into (Mn sulfide S) by an appropriate method. It goes without saying that there are. If the method is appropriate, the analysis method is not particularly limited.
硫化物の量とともに直接観察により得られるサイズ、密度等の制御も本発明の効果を得るためには重要となる。特に上述のような化学的な分析では検出できず、分析値が０となるような場合にも直接観察においては微細かつ微量な硫化物が見られる場合もあり、このような微細かつ微量な硫化物を制御することが本発明では重要となることがある。なお、硫化物単独の析出物でなく酸化物や炭化物などと複合析出した場合も対象とする。複合析出物を形成した場合には、一つの析出物の種類および各化合物についてのサイズを特定することは困難であるが、明らかに一つの析出物が硫化物である部分とその他に分けられる場合を除いて一つの硫化物として判定するものとする。 Control of the size, density, etc. obtained by direct observation together with the amount of sulfide is important for obtaining the effects of the present invention. In particular, even when the analytical value cannot be detected by the chemical analysis as described above and the analytical value is 0, a fine and trace amount of sulfide may be seen in direct observation. Controlling things may be important in the present invention. It should be noted that not only sulfides but also composite precipitates with oxides or carbides are considered. When composite precipitates are formed, it is difficult to specify the type of one precipitate and the size of each compound, but when one precipitate is clearly divided into a sulfide part and the other Shall be judged as one sulfide.
硫化物は本発明ではＳＰＥＥＤ法によって得られた抽出レプリカをＥＤＸ付電子顕微鏡にて観察する。組成の判定はＥＤＸにより分析を行い主として観察される非金属元素がＳの場合を硫化物とする。また大きさが小さいためＳの特性スペクトルは明瞭ではなくともＭｎ，Ｃｕ等が検出されかつ、Ｏ等の明瞭なスペクトルが観察されず、かつ硫化物と特定できる他の析出物との形態比較から硫化物とほぼ断定できる析出物も硫化物として本発明で考慮に入れる。大きさが非常に微小でありＥＤＸスペクトルに明瞭な特性スペクトルが現れないものは本発明で考慮すべき硫化物からは除外する。この最小サイズは大体０．０２μｍが限度となる。硫化物の直径および数は偏りがない程度の視野について計測する。視野を写真撮影し、画像解析等を行うことでもサイズ分布を求めることができる。 In the present invention, for the sulfide, an extracted replica obtained by the SPEED method is observed with an electron microscope with EDX. The composition is determined by analysis by EDX, and when the non-metallic element mainly observed is S, the sulfide is determined. In addition, because the size is small, the characteristic spectrum of S is not clear, but Mn, Cu, etc. are detected, no clear spectrum of O, etc. is observed, and from the comparison of the morphology with other precipitates that can be identified as sulfides Precipitates that can be almost determined as sulfides are also taken into account in the present invention as sulfides. Those that are very small in size and do not show a clear characteristic spectrum in the EDX spectrum are excluded from the sulfides to be considered in the present invention. The minimum size is limited to approximately 0.02 μm. The diameter and number of sulfides are measured in a visual field where there is no bias. The size distribution can also be obtained by taking a picture of the field of view and performing image analysis or the like.
また、形状が延伸したものが見られる場合があるが、形状が等方的でないものについては長径と短径の平均をその析出物の直径とする。 Moreover, although what extended the shape may be seen, about the thing where a shape is not isotropic, let the average of a major axis and a minor axis be the diameter of the precipitate.
析出物の数密度はレプリカ作成過程における電解工程において試料表面を通電した全電荷が、Ｆｅの２価イオン（Ｆｅ2+）として鋼板が電解されるのに消費され、電解時に残滓として残る析出物がすべてレプリカ上に補足されるとして計算した。本発明者らの通常のレプリカ作成においては試料表面積において５０Ｃ（クーロン）／ｃｍ2の電気量で電解を行うので、試料表面から１８μｍの厚さ内にある析出物がレプリカ上で観察されることになる。 The number density of the precipitates is consumed when the steel sheet is electrolyzed as Fe divalent ions (Fe 2+ ) in the electrolysis process in the replica making process, and all the precipitates remaining as residues during electrolysis are consumed. Calculated as supplemented on replica. In the ordinary replica production by the present inventors, electrolysis is performed with an electric quantity of 50 C (Coulomb) / cm 2 on the surface area of the sample, so that precipitates within a thickness of 18 μm from the sample surface are observed on the replica. become.
以上のようにして測定された硫化物についてコイルの全部位にわたり、直径０．１０μｍ以下のＣｕを含有する硫化物の数密度が０．５個／μｍ3以下、かつ直径０．０２μｍ以上１．０μｍ以下のＣｕを含有する硫化物について、平均直径が０．０５μｍ以上、直径が０．０５μｍ以下であるものの個数の割合が５０％以下、とすることで良好な磁気特性とコイル内均質性を得ることができる。特定部位で数密度が特定数値以上、特に微細なものの割合が増加するとその部位の特性が劣化し良好なコイル内均質性を得ることができなくなる。 With respect to the sulfide measured as described above, the number density of the sulfide containing Cu having a diameter of 0.10 μm or less is 0.5 pieces / μm 3 or less and the diameter is 0.02 μm or more and 1.0 μm or less over the entire portion of the coil. With respect to the sulfide containing Cu, good magnetic properties and in-coil homogeneity can be obtained by setting the ratio of the number of those having an average diameter of 0.05 μm or more and a diameter of 0.05 μm or less to 50% or less. Can do. If the number density of a specific part is greater than a specific numerical value, and the proportion of particularly fine ones increases, the characteristics of the part deteriorates and good in-coil homogeneity cannot be obtained.
次に、本発明の効果を得ることができる特徴的な熱延条件について説明する。 Next, characteristic hot rolling conditions that can obtain the effects of the present invention will be described.
通常の連続鋳造−スラブ加熱−熱間圧延−冷延・焼鈍という熱履歴での製造工程においては特にスラブ加熱時の加熱炉中の温度履歴が重要となる。通常、スラブは長さ８ｍ、幅１ｍ程度であるが、このような大きさのスラブを炉中に保持して加熱する場合、スラブの部位において少なからず温度差が生ずる。鋳造後の冷却および炉中での加熱はスラブ表面からの熱伝導により行われるため、特に、スラブの端部は過冷却、過加熱されやすくなる。特に加熱中は加熱炉の構造等を考えるとスラブ長手位置における端部、すなわちＴ、Ｂ部で大きな温度不均一を生ずる。 In a manufacturing process with a heat history of normal continuous casting-slab heating-hot rolling-cold rolling / annealing, the temperature history in the heating furnace during slab heating is particularly important. Usually, the slab has a length of about 8 m and a width of about 1 m. However, when a slab having such a size is held in a furnace and heated, a temperature difference is not small at the site of the slab. Since the cooling after casting and the heating in the furnace are performed by heat conduction from the surface of the slab, in particular, the end of the slab is easily overcooled and overheated. In particular, during heating, considering the structure of the heating furnace, a large temperature non-uniformity occurs at the end of the slab longitudinal position, that is, T and B portions.
一般に加熱炉中の温度制御はスラブ全長の平均やＭ部での測定値を代表値として行われるが、本発明の目的を達成するにはＴ、Ｂ部の温度制御が非常に重要となる。すなわち、スラブの全ての部位について温度が１２００℃を超えないように加熱し１１００℃以下の温度で加熱炉から取り出し熱間圧延を開始する必要がある。好ましくはスラブの全ての部位について温度が１１５０℃を超えないように加熱し１０５０℃以下の温度で加熱炉から取り出し熱間圧延を開始する。 In general, the temperature control in the heating furnace is performed by using the average value of the slab total length or the measured value at the M part as a representative value, but the temperature control at the T and B parts is very important in order to achieve the object of the present invention. That is, it is necessary to heat all the parts of the slab so that the temperature does not exceed 1200 ° C., and to take out the hot rolling from the heating furnace at a temperature of 1100 ° C. or less. Preferably, all the portions of the slab are heated so that the temperature does not exceed 1150 ° C., taken out from the heating furnace at a temperature of 1050 ° C. or less, and hot rolling is started.
この温度制御は通常の操業において加熱炉中で測定されている炉温について行うものとする。通常の操業であればこの温度は実スラブの表面層の温度に合致するように調整され、実スラブの表面層温度と大きな乖離はないものである。下限は本発明の目的からは特に制限されないが通常の設備であれば熱延性の観点から上述の全ての温度は８００℃以上であるべきである。上述のようにスラブ端部は加熱されやすいため加熱の上限はスラブ端部について特に重要な意味を有する。温度範囲が発明範囲を外れるとＴ、Ｂ部の磁気特性、特に鉄損が大きく劣化し、コイル内の特性ばらつきが大きくなる。 This temperature control is performed for the furnace temperature measured in the heating furnace in normal operation. In normal operation, this temperature is adjusted to match the temperature of the surface layer of the actual slab, and there is no significant deviation from the surface layer temperature of the actual slab. The lower limit is not particularly limited for the purpose of the present invention, but if it is ordinary equipment, all the above-mentioned temperatures should be 800 ° C. or more from the viewpoint of hot ductility. As described above, since the slab end is easily heated, the upper limit of heating has a particularly important meaning for the slab end. When the temperature range is outside the scope of the invention, the magnetic characteristics of the T and B portions, particularly the iron loss, are greatly deteriorated, and the variation in characteristics within the coil increases.
上述のようにスラブ端部は過加熱されやすいが、スラブ加熱時の温度上昇量が大きいと特に過加熱されやすくなり、各種条件を本発明範囲内に制御することが困難となる。このためには鋳造後のスラブを過度に冷却せず再加熱することが好ましい。しかし、鋳造後再加熱されるまでの最低温度があまりに高いとコイル内の特性変動は小さくなるものの特性の絶対値が劣化してしまうため特定の範囲に制御する必要がある。 As described above, the end of the slab is easily overheated. However, if the amount of temperature rise during slab heating is large, the slab end is particularly easily overheated, and it is difficult to control various conditions within the scope of the present invention. For this purpose, it is preferable to reheat the slab after casting without excessive cooling. However, if the minimum temperature until reheating after casting is too high, the characteristic variation in the coil is reduced, but the absolute value of the characteristic deteriorates, so it is necessary to control it within a specific range.
本発明では連続鋳造後のスラブを９５０℃〜５００℃の温度域まで冷却した後、加熱炉に挿入する。好ましくは９００℃〜５５０℃、さらに好ましくは８５０℃〜６００℃、さらに好ましくは８００℃〜６５０℃である。通常の２００ｍｍ程度の厚さのスラブを空冷する場合であればこの温度域での滞在時間は１０分以上となるが、なんらかの保熱設備を用いてこの温度域での滞在時間を長くすることは本発明の効果にとり好ましい。なお、このスラブの温度はスラブの表面と内部で相当の温度差が生じていると考えられるが、本発明では通常用いられる接触式の温度計または非接触の放射温度計で測定される温度で規定することが可能であるが特に方法が限定されるものではなく、常識的に妥当な方法であれば構わない。 In the present invention, the slab after continuous casting is cooled to a temperature range of 950 ° C. to 500 ° C. and then inserted into a heating furnace. Preferably they are 900 to 550 degreeC, More preferably, it is 850 to 600 degreeC, More preferably, it is 800 to 650 degreeC. If a normal slab with a thickness of about 200 mm is air-cooled, the staying time in this temperature range will be 10 minutes or more, but it is not possible to lengthen the staying time in this temperature range using any heat insulation equipment. It is preferable for the effect of the present invention. The temperature of the slab is considered to have a considerable temperature difference between the surface and the inside of the slab, but in the present invention, it is a temperature measured with a contact-type thermometer or a non-contact radiation thermometer that is usually used. Although it is possible to define the method, the method is not particularly limited, and any method that is reasonable in common sense may be used.
上述のスラブ端部の過加熱を特定範囲に制御しコイル内の材質ばらつきを特定範囲内に抑制するにはスラブ加熱炉中の加熱速度またはスラブ加熱炉内の滞在時間を制御することが好ましい。基本的には徐加熱、長時間加熱が好ましく、スラブ加熱炉中の平均加熱速度が４．０℃／分以下、好ましくは３．５℃／分以下、さらに好ましくは３．０℃／分以下、またスラブ加熱炉内の滞在時間が３００分以上、好ましくは３５０分以上、さらに好ましくは４００分以上である。 In order to control the overheating of the end portion of the slab to a specific range and suppress the material variation in the coil within the specific range, it is preferable to control the heating rate in the slab heating furnace or the residence time in the slab heating furnace. Basically, slow heating and long-time heating are preferable, and the average heating rate in the slab heating furnace is 4.0 ° C./min or less, preferably 3.5 ° C./min or less, more preferably 3.0 ° C./min or less. Moreover, the residence time in a slab heating furnace is 300 minutes or more, Preferably it is 350 minutes or more, More preferably, it is 400 minutes or more.
熱延仕上げ以降の製造工程は何ら特殊なものである必要はなく、通常の無方向性電磁鋼板の製造方法と同様で本発明の効果を得ることができる。 The manufacturing process after the hot rolling finish need not be any special process, and the effects of the present invention can be obtained in the same manner as in the normal method for manufacturing a non-oriented electrical steel sheet.
硫化物の形態を好ましいものにするため仕上げ熱延後の高温での巻取も含めた熱処理により温度を７００℃以上とすると析出物形態がより好ましくなりコイル内全体の特性が向上する。また熱延板焼鈍であれば７００℃以上１１００℃以下で５秒〜１０分の熱処理を行うことでも同様の効果を得ることができる。これ以上の温度ではＣｕ硫化物が溶解し磁気特性が劣化してしまうので注意が必要である。これ以降は一般的には圧下率６５〜９５％の冷間圧延をした後、１０秒〜５分の再結晶焼鈍を行う。なお、本発明の製造方法により仕上焼鈍を経て得られた無方向性電磁鋼板は、その後に歪取焼鈍を行ってもその優れた鉄損値および磁束密度を保持する。 If the temperature is set to 700 ° C. or higher by heat treatment including high-temperature winding after finish hot rolling in order to make the sulfide form preferable, the precipitate form becomes more preferable and the overall characteristics in the coil are improved. Moreover, if it is hot-rolled sheet annealing, the same effect can be acquired also by performing the heat processing for 5 second-10 minutes at 700 to 1100 degreeC. At higher temperatures, Cu sulfide dissolves and magnetic properties deteriorate, so care must be taken. After this, generally, after cold rolling with a rolling reduction of 65 to 95%, recrystallization annealing is performed for 10 seconds to 5 minutes. In addition, the non-oriented electrical steel sheet obtained through finish annealing by the manufacturing method of the present invention retains its excellent iron loss value and magnetic flux density even after performing strain relief annealing.
また本発明の効果は焼鈍後の歪の導入を抑えてモーターとして使用される、いわゆるフルプロセス無方向電磁鋼板はもちろん、焼鈍後にスキンパス圧延を行いモーター等に組み立て後の熱処理工程での歪誘起粒成長現象を用いて特性の改善を行ういわゆるセミプロセス無方向電磁鋼板にも適用可能である。 The effect of the present invention is not only the so-called full-process non-oriented electrical steel sheet, which is used as a motor by suppressing the introduction of strain after annealing, but also strain-induced grains in the heat treatment process after assembling into a motor etc. by performing skin pass rolling after annealing. The present invention can also be applied to a so-called semi-processed non-oriented electrical steel sheet in which characteristics are improved by using a growth phenomenon.
表２に示す成分の鋼を溶製し、これを連続鋳造でスラブとなし、表３に示す条件でそれぞれスラブ加熱と熱間圧延を行い、一部熱延板焼鈍を行い酸洗した後、冷延し、次いで連続焼鈍を実施し製造した製品よりサンプルを採取し評価を行った。一部の材料についてはサンプルを７５０℃×２時間の歪取り焼鈍を行った後、特性を評価した。 After melting the steel of the components shown in Table 2, this was made into a slab by continuous casting, slab heating and hot rolling were performed under the conditions shown in Table 3, respectively, and after partially hot-rolled sheet annealing and pickling, Samples were collected from the products manufactured by cold rolling and then subjected to continuous annealing and evaluated. For some materials, the samples were subjected to strain relief annealing at 750 ° C. for 2 hours, and then the characteristics were evaluated.
注意を要するのは前述したように評価サンプルを採取するＴ部、Ｍ部、Ｂ部の部位は熱延コイルを基準としていることである。通常の製品製造においてはユーザーから注文される製品の量単位（コイル質量）は客先でのハンドリング等を考慮し注文されるため必ずしもスラブの量単位（スラブ質量）とは一致しない。このため、一つのスラブから製造される半製品または最終製品において分割される。例えば通常のスラブ質量は１０〜２０トンであるが、注文されたコイルが５ｔであれば、一つのスラブを熱延して得られた一つの熱延コイルは最終的に二〜四個の製品コイルとして評価、出荷される。この場合も熱延コイルの端部（Ｔ、Ｂ部）および中央部（Ｍ部）に相当する部位で評価する必要がある。本実施例でのＴ部、Ｍ部、Ｂ部は熱延コイルでの各位置に相当する部位に関する特性値である。 It should be noted that, as described above, the portions of the T portion, M portion, and B portion where the evaluation samples are collected are based on the hot rolled coil. In normal product manufacturing, the quantity unit (coil mass) of a product ordered from a user is ordered in consideration of handling at the customer, and therefore does not necessarily match the quantity unit of slab (slab mass). For this reason, it is divided into semi-finished products or final products manufactured from one slab. For example, the normal slab mass is 10 to 20 tons, but if the ordered coil is 5 tons, one hot-rolled coil obtained by hot-rolling one slab finally has 2 to 4 products. It is evaluated and shipped as a coil. In this case as well, it is necessary to evaluate at portions corresponding to the end portions (T and B portions) and the central portion (M portion) of the hot rolled coil. T part, M part, and B part in the present embodiment are characteristic values relating to portions corresponding to respective positions in the hot rolled coil.
得られた各鋼板の析出物の状態と磁気特性を表４に示す。ここで磁気特性は、備考欄に記載の項目について、５５ｍｍ×５５ｍｍの大きさのサンプルでコイルの圧延方向から０°、４５°、９０°の特性を測定し、それぞれの値 Ｘ0、Ｘ45、Ｘ90：に対し、
（Ｘ0＋２×Ｘ45＋Ｘ90）／４
で得られる値により評価した。
Table 4 shows the state of precipitates and magnetic properties of the obtained steel sheets. Here, with respect to the items described in the remarks column, the magnetic properties were measured at 0 °, 45 °, and 90 ° from the coil rolling direction with a sample having a size of 55 mm × 55 mm, and the respective values X 0 , X 45 were measured. , X 90 :
(X 0 + 2 × X 45 + X 90 ) / 4
It evaluated by the value obtained by.
最終的な評価は磁気特性の絶対値およびコイル内の材質ばらつきにより評価した。コイル内の材質ばらつきは特に鉄損において顕著な差が見られるため、コイル内特性の最高値（鉄損劣位）とコイル内のこの結果から、本発明範囲内にある鋼板は磁気特性が優れているばかりでなく、コイル内の材質ばらつきが非常に小さいことが判る。これに対して本発明範囲を外れたものは特性が全体または部分的に不良である。 The final evaluation was based on the absolute value of the magnetic characteristics and the material variation in the coil. Since there is a significant difference in the iron loss especially in the material variation in the coil, the maximum value in the coil (iron loss inferior) and the result in the coil indicate that the steel sheet within the scope of the present invention has excellent magnetic properties. It can be seen that the material variation in the coil is very small. On the other hand, those outside the scope of the present invention are poor in whole or in part.
Claims (6)
（Ｘmax−Ｘmin）／Ｘmin＊１００ ≦２５ ・・・式１
ただし、ＸT、ＸM、ＸBの内の最大値をＸmax
ＸT、ＸM、ＸBの内の最小値をＸmin
磁気特性はＢ10、Ｂ25、Ｂ50（単位Ｔ）、Ｗ15/50、Ｗ10/400（単位Ｗ／ｋｇ）の
いずれか１以上。 0.040% or less, Si:: C mass% 0.05~3.5%, Mn: 1.0% or less and Si / 2 or less, Al: 0.005% or less, S: 0.00 2% Hereinafter, P: 0.15% or less, N: 0.020% or less, Cu: 0.10% or less, and the balance consisting of Fe and unavoidable impurities, (S which is Cu sulfide) / (S in steel) ) ≦ 0.2 and the magnetic characteristic X T at the position 2 m from the front end, the magnetic characteristic X B at the position 2 m from the rear end, and the magnetic characteristic X M at the center at the coil longitudinal position with respect to the hot rolled coil. 1, the number density of sulfides containing Cu having a diameter of 0.02 μm or more and 0.10 μm or less in the steel sheet at each position is 0.5 piece / μm 3 or less. .
(Xmax−Xmin) / Xmin * 100 ≦ 25 (1)
However, the maximum value of X T , X M , and X B is set to Xmax
The minimum value of X T , X M , and X B is Xmin
Magnetic properties B 10, B 25, B 50 ( unit T), W 15/50, W 10/400 any one or more (in W / kg).
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| CN103237907A (en) * | 2010-12-03 | 2013-08-07 | 杰富意钢铁株式会社 | Hot rolling method for silicon-ontaining steel slab |
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| JP4568190B2 (en) * | 2004-09-22 | 2010-10-27 | 新日本製鐵株式会社 | Non-oriented electrical steel sheet |
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| US20160273064A1 (en) * | 2013-04-09 | 2016-09-22 | Nippon Steel & Sumitomo Metal Corporation | Non-oriented electrical steel sheet and method of manufacturing the same |
| JP6475079B2 (en) * | 2014-06-30 | 2019-02-27 | アイシン精機株式会社 | Iron-based soft magnetic material |
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| JP7040109B2 (en) * | 2018-02-22 | 2022-03-23 | 日本製鉄株式会社 | Non-oriented electrical steel sheet |
| JP7284367B2 (en) * | 2018-08-06 | 2023-05-31 | 日本製鉄株式会社 | Non-oriented electrical steel sheet coil and its manufacturing method |
| KR102241985B1 (en) * | 2018-12-19 | 2021-04-19 | 주식회사 포스코 | Non-oriented electrical steel sheet and method for manufacturing the same |
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| CN103237907A (en) * | 2010-12-03 | 2013-08-07 | 杰富意钢铁株式会社 | Hot rolling method for silicon-ontaining steel slab |
| CN103237907B (en) * | 2010-12-03 | 2014-12-10 | 杰富意钢铁株式会社 | Hot rolling method for silicon-ontaining steel slab |
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