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- JP2013540900A5 JP2013540900A5 JP2013530533A JP2013530533A JP2013540900A5 JP 2013540900 A5 JP2013540900 A5 JP 2013540900A5 JP 2013530533 A JP2013530533 A JP 2013530533A JP 2013530533 A JP2013530533 A JP 2013530533A JP 2013540900 A5 JP2013540900 A5 JP 2013540900A5
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- 229910000831 Steel Inorganic materials 0.000 claims description 85
- 239000010959 steel Substances 0.000 claims description 85
- 238000005096 rolling process Methods 0.000 claims description 45
- 238000005098 hot rolling Methods 0.000 claims description 22
- 239000007788 liquid Substances 0.000 claims description 22
- 229910052710 silicon Inorganic materials 0.000 claims description 20
- 239000000498 cooling water Substances 0.000 claims description 15
- 229910000565 Non-oriented electrical steel Inorganic materials 0.000 claims description 14
- 239000012535 impurity Substances 0.000 claims description 14
- 238000009749 continuous casting Methods 0.000 claims description 13
- 229910052748 manganese Inorganic materials 0.000 claims description 13
- 239000000203 mixture Substances 0.000 claims description 13
- 238000004519 manufacturing process Methods 0.000 claims description 12
- 239000000126 substance Substances 0.000 claims description 12
- 238000005097 cold rolling Methods 0.000 claims description 11
- 229910052698 phosphorus Inorganic materials 0.000 claims description 11
- 229910052782 aluminium Inorganic materials 0.000 claims description 10
- 229910052757 nitrogen Inorganic materials 0.000 claims description 10
- 229910052760 oxygen Inorganic materials 0.000 claims description 9
- 229910052717 sulfur Inorganic materials 0.000 claims description 8
- 238000000137 annealing Methods 0.000 claims description 6
- 238000003723 Smelting Methods 0.000 claims description 2
- 239000011248 coating agent Substances 0.000 claims description 2
- 238000000576 coating method Methods 0.000 claims description 2
- 238000005554 pickling Methods 0.000 claims description 2
- 238000007670 refining Methods 0.000 claims description 2
- 238000010128 melt processing Methods 0.000 claims 1
- 239000000161 steel melt Substances 0.000 claims 1
- 238000010438 heat treatment Methods 0.000 description 28
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 23
- 230000001965 increased Effects 0.000 description 20
- 239000000047 product Substances 0.000 description 17
- 238000005266 casting Methods 0.000 description 16
- 239000011572 manganese Substances 0.000 description 14
- 238000003756 stirring Methods 0.000 description 14
- 238000001953 recrystallisation Methods 0.000 description 11
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 10
- 239000010703 silicon Substances 0.000 description 10
- 239000000835 fiber Substances 0.000 description 9
- 229910052742 iron Inorganic materials 0.000 description 9
- 238000000034 method Methods 0.000 description 9
- 230000005389 magnetism Effects 0.000 description 8
- 230000001276 controlling effect Effects 0.000 description 7
- 230000001939 inductive effect Effects 0.000 description 5
- 238000004804 winding Methods 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 4
- 229910017083 AlN Inorganic materials 0.000 description 3
- PIGFYZPCRLYGLF-UHFFFAOYSA-N aluminum nitride Chemical compound [Al]#N PIGFYZPCRLYGLF-UHFFFAOYSA-N 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 3
- 229910052799 carbon Inorganic materials 0.000 description 3
- 238000001816 cooling Methods 0.000 description 3
- 230000000875 corresponding Effects 0.000 description 3
- PWHULOQIROXLJO-UHFFFAOYSA-N manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 238000010606 normalization Methods 0.000 description 3
- 229910000976 Electrical steel Inorganic materials 0.000 description 2
- -1 MnS Chemical class 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 239000012467 final product Substances 0.000 description 2
- 230000004907 flux Effects 0.000 description 2
- 238000011068 load Methods 0.000 description 2
- 238000003760 magnetic stirring Methods 0.000 description 2
- OAICVXFJPJFONN-UHFFFAOYSA-N phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 2
- 239000011574 phosphorus Substances 0.000 description 2
- 238000011084 recovery Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 230000003247 decreasing Effects 0.000 description 1
- 238000007599 discharging Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000001035 drying Methods 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000003475 lamination Methods 0.000 description 1
- 229910000529 magnetic ferrite Inorganic materials 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 238000010309 melting process Methods 0.000 description 1
- TWXTWZIUMCFMSG-UHFFFAOYSA-N nitride(3-) Chemical compound [N-3] TWXTWZIUMCFMSG-UHFFFAOYSA-N 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000003303 reheating Methods 0.000 description 1
- 238000002791 soaking Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 150000003568 thioethers Chemical class 0.000 description 1
- 210000001519 tissues Anatomy 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
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Description
本発明は、無方向性電磁鋼板およびその製造方法、特に、優れた磁力を有する波状欠陥のない中級鋼種無方向性電磁鋼板およびその製造方法に関する。 TECHNICAL FIELD The present invention relates to a non-oriented electrical steel sheet and a method for producing the same, and more particularly to a medium grade steel non-oriented electrical steel sheet having an excellent magnetic force and having no wavy defects, and a method for producing the same.
先行技術の説明
無方向性電磁鋼板にシリコン量が高い場合、完成品の帯鋼の表面に、一般に「波状欠陥」と呼ばれる波形起伏が圧延方向に沿って現われる。この欠陥は、完成品の帯鋼の積層係数を著しく減少し、完成品の帯鋼の磁性を悪化させ、絶縁膜層間の電気抵抗を低下させ、したがって製造された最終製品の使用性能および使用寿命を低下させる。したがって、多くのユーザは、完成品帯鋼には波状欠陥が存在しないように、明確に要求している。
Description of prior art
If the amount of silicon in the non-oriented electrical steel sheet is high, the surface of the finished strip of appearing undulations called "wavy defect" In general along the rolling direction. This defect decreased significantly lamination coefficient of the finished strip of, exacerbate the magnetism of the finished strip of, reduces the electrical resistance of the insulating film layers, used performance and use of the final product produced in accordance Reduce lifespan . Therefore, many users specifically require that the finished strip steel has no wavy defects.
波状欠陥の発生の仕組みは以下のように説明され得る。スラブ中の等軸晶率は低いが、柱状晶は大きく成長している。柱状晶の成長方向＜００１＞は、（００１）の法線方向であり、熱流の勾配が最大な方向でもある。大きな柱状晶は、動的回復と再結晶化が遅いため、熱間圧延処理において完全に破砕されることができない。それに、スラブの柱状晶は熱流束の方向に成長し、方向性のある大きな柱状晶を形成しやすいため、圧延処理において不均質な変形を引起す。熱間圧延処理の後、スラブの厚み方向の中心は、主に繊維組織であり、これらの繊維組織は、以降の処理においてオーステナイトおよびフェライトは相転移しないため、以降の冷間圧延およびアニーリング処理において再結晶することができず、繊維組織は均質になれずに完成品に残り、最終的に起伏のある波状欠陥を形成する。 The mechanism of occurrence of the wavy defect can be explained as follows. Etc. JikuAkiraritsu low in the slab, but columnar crystals are size Kunar length. The growth direction <001> of the columnar crystals is the normal direction of (001), and is also the direction in which the gradient of heat flow is maximum. Large columnar crystals cannot be completely crushed in the hot rolling process due to slow dynamic recovery and recrystallization. In addition , the columnar crystal of the slab grows in the direction of the heat flux and tends to form a large directional columnar crystal, which causes inhomogeneous deformation in the rolling process. After the hot rolling treatment, the center in the thickness direction of the slab is mainly a fiber structure, and these fiber structures do not undergo phase transition of austenite and ferrite in the subsequent treatment, so in the subsequent cold rolling and annealing treatment It cannot be recrystallized , the fiber structure does not become homogeneous and remains in the finished product, eventually forming undulating wavy defects.
波状欠陥を対処する従来の方法は、主に以下のとおりである。たとえば特開昭４９−３９５２６では、電磁撹拌法を利用することによってスラブ中の等軸晶率を向上させる。たとえば特開昭４８−４９６１７、中国特許出願ＣＮ１０１２７５１９８、ＣＮ１５４８５６９、ＣＮ１０１１３９６８１等では、鋼中の炭素含有量およびマンガン含有量を増加することによって、熱間圧延処理における相転移温度を低下させる。たとえば特開昭５３−１４６０９および特開平２−１９２８５３では、低温鋳込みを利用することによってスラブ中の等軸晶率を向上させ得る。たとえば特開昭４９−２７４２０、特開昭４９−３８８１３、特開昭５３−２３３２、特開昭６１−６９９２３、中国特許出願ＣＮ１６１１６１６、およびＣＮ１５４８５６９では、スラブの吐出し温度を上昇させ、スラブの加熱速度を調整し、仕上げ圧延処理における最終圧延温度を制御し、熱間圧延処理における第１および最終段階の圧下率の減少を制御することによって、帯鋼を十分に再結晶させる。たとえば特開昭６１−１２７８１７等では、焼きならし処理を利用することによって帯鋼を十分に再結晶化させる。 Traditional way to deal with wave-like defect is mainly as follows. For example, in JP 49-39526, to improve the equiaxed Akiraritsu in the slab by utilizing electromagnetic stirring method. For example JP 48-49617, in Chinese patent application CN101275198, CN1548569, CN101139681, etc., by increasing the carbon content and manganese content in the steel, to lower the phase transition temperature in the hot rolling process. For example, in Japanese Patent Laid-Open No. 53-14609 and Japanese Patent Laid-Open No. 2-192853, the equiaxed crystal ratio in the slab can be improved by using low temperature casting . For example JP 49-27420, JP 49-38813, JP 53-2332, Sho 61-69923, in Chinese patent application CN1611616, and CN1548569, raise the discharged temperature of the slab, the slab adjust the heating rate to control the final rolling temperature in the finish rolling process, by controlling the reduction of the rolling reduction of the first and final step in the hot rolling process, to sufficiently recrystallize the strip. For example, in JP 61-127817, etc., to sufficiently recrystallize the strip by the utilizing normalizing process.
前述の方法は、技術、費用、ならびに完成品および表面の磁力に対する要望に応じて、単独でまたは同時に使用され得る。これらの方法は、下記に述べる特徴および要件をそれぞれ有する。 The methods described above can be used alone or simultaneously depending on the technology, cost, and demand for the finished product and surface magnetism. Each of these methods has the characteristics and requirements described below.
電磁撹拌法を利用することによって、スラブ中の等軸晶率を向上させることができる。この方法は電磁撹拌法を利用する。この方法は、電磁力を用いて柱状晶を破砕するため、最も効果的である。特に、電磁撹拌を２回以上利用すると、スラブ中の柱状晶率を著しく低下させ、スラブ中の等軸晶率を向上させることになり、中心領域において二次柱状晶を効果的に防止することもできる。この方法の主な欠点は、撹拌効果が鋼中のシリコン含有量と電磁撹拌回数とに依存する点である。シリコンの含有量が低い鋼の場合、最初の電磁撹拌後、スラブ中の等軸結晶は比較的容易に塊状を形成して大きくなり、再び大きな柱状晶を形成する。したがって、２回以上の電磁撹拌が必要となり、液体鋼の凝固作用を厳密に制御する必要もある。また、電磁撹拌法を利用すると、製造費用は高額になる。 By utilizing the electromagnetic stirring method, the equiaxed crystal ratio in the slab can be improved . This method uses an electromagnetic stirring method. This method is most effective because the columnar crystals are crushed using electromagnetic force. In particular, the use more than twice the conductive magnetic stirring, columnar Akiraritsu in slabs significantly reduce, will improve the equiaxed Akiraritsu in the slab effectively prevent secondary columnar structure in the central region You can also. The main drawback of this method is that the stirring effect depends on the silicon content in the steel and the number of electromagnetic stirrings. In the case of steel with a low silicon content, after the first electromagnetic stirring, the equiaxed crystals in the slab are relatively easily formed into lumps and become large, and again form large columnar crystals. Therefore, two or more times of electromagnetic stirring are required, and it is also necessary to strictly control the solidification action of the liquid steel. In addition, when the electromagnetic stirring method is used, the manufacturing cost becomes high.
鋼中の炭素含有量およびマンガン含有量を増加することによって、熱間圧延処理における相転移温度を低下させることができる。この方法は、主に、鋼中の炭素含有量およびマンガン含有量を増加することによって、加熱および熱間圧延処理の際にスラブに相転移を生じさせ、よって、動的回復および再結晶化を加速し、大きな変形結晶粒を除去する。この方法の主な欠点は、アニーリング処理において脱炭する必要があるため、内側酸化層および内側窒化層を生成しやすくなり、鋼の磁性を悪化させることである。 By increasing the carbon content and manganese content in the steel, the phase transition temperature in the hot rolling process can be lowered . This method mainly causes a phase transition in the slab during heating and hot rolling processes by increasing the carbon and manganese content in the steel, thus providing dynamic recovery and recrystallization. Accelerate and remove large deformed crystal grains. The main disadvantage of this method is that it is necessary to decarburize in the annealing process, so that it becomes easier to form an inner oxide layer and an inner nitride layer, and deteriorates the magnetism of the steel.
低温鋳込みを利用することによって、スラブ中の等軸晶率を向上させることができる。この方法は、主に鋳込み処理において液体鋼の過熱温度を減少させることによって、スラブ中の柱状晶率を低下させ、等軸晶の占有比率を向上させる。この方法の主な欠点は、液体鋼の過熱温度の範囲が非常に低く要求されるため、効果的に制御することができず、連続鋳造処理に影響を及ぼすことである。 By using low-temperature casting , the equiaxed crystal ratio in the slab can be improved . In this method, the columnar crystal ratio in the slab is lowered and the occupation ratio of equiaxed crystals is improved mainly by reducing the superheating temperature of the liquid steel in the casting process. The main drawback of this method is that the superheat temperature range of the liquid steel is required to be very low and cannot be effectively controlled, affecting the continuous casting process.
スラブの吐出し温度を上昇させ、スラブの加熱速度を調整し、仕上げ圧延処理における最終圧延温度を制御し、熱間圧延処理における第１および最終段階の圧下率の減少を制御することによって、帯鋼は十分に再結晶化することができる。この方法は、主に、スラブの吐出し温度を上昇させ、スラブの加熱速度を調整し、仕上げ圧延処理における最終圧延温度を制御し、熱間圧延処理における第１および最終段階の圧下率の減少を制御することによって、スラブ中の大きな柱状晶を破砕し、大きな変形結晶粒の成長を防止し、帯鋼を十分に再結晶化させる。この方法の主な欠点は、スラブの吐出し温度を上昇させることによって、ＭｎＳ、ＡｌＮなどの不純物の固溶が酷くなり、したがって完成品の帯鋼の磁性を悪化させることである。帯鋼の再結晶化を保証するために、鋼中のＳ、Ｎなどの不純物元素の含有量が厳密に要求される。また、熱間圧延処理における第１および最終段階の圧下率の減少は、圧延機の性能によって制限される。 By increasing the discharge temperature of the slab, adjusting the heating rate of the slab, controlling the final rolling temperature in the finish rolling process, and controlling the reduction of the rolling reduction in the first and final stages in the hot rolling process , Steel can be fully recrystallized. This method is mainly to increase the discharge temperature of the slab, by adjusting the heating rate of the slab, to control the final rolling temperature that put the finishing rolling process, the rolling reduction of the first and final step in the hot rolling process By controlling the decrease in size, the large columnar crystals in the slab are crushed, the growth of large deformed crystal grains is prevented, and the steel strip is sufficiently recrystallized. The main drawback of this method is that by increasing the discharge temperature of the slab, MnS, solid solution of AlN of any impurity is severe, therefore it is to worsen the magnetic properties of the strip of the finished product. In order to guarantee recrystallization of the strip steel, the content of impurity elements such as S and N in the steel is strictly required. Further, the reduction of the rolling reduction in the first and final stages in the hot rolling process is limited by the performance of the rolling mill .
焼きならし処理を利用することによって、帯鋼を十分に再結晶化することができる。一次冷間圧延法を利用する場合、シリコンの含有量が高い鋼は、焼きならし処理を行なう必要がある。焼きならしの目的の１つは、熱間圧延した鋼板内部の再結晶率を上昇させることによって、波状欠陥の発生を防止することである。この方法の主な欠点は、製造費用が非常に高くなるため、付加価値が比較的低い低級または中級鋼種のケイ素鋼には適用できないことである。 By utilizing the normalizing treatment, the steel strip can be sufficiently recrystallized. When the primary cold rolling method is used, steel having a high silicon content needs to be subjected to normalization. One of the purposes of normalization is to prevent the occurrence of wavy defects by increasing the recrystallization rate inside the hot-rolled steel sheet . The main drawback of this method is that it is very expensive to manufacture and cannot be applied to silicon steels of lower or intermediate grades with relatively low added value.
発明の開示
本発明の目的は、波状欠陥のない無方向性電磁鋼板およびその製造方法を提供することである。連続鋳込み処理におけるスラブの冷却速度、加熱炉中のスラブの長さ方向の温度差を厳密に制御し、スラブを仕上げする前の降温を制御することによって、波状欠陥のない中級鋼種無方向性電磁鋼板を製造することができる。製造方法において、操作が容易であり、鋼板の生産費用が低くなり、エネルギーが節約され、環境保護に寄与し、製造された鋼板が優れた磁性を有する。また、連続鋳込み処理においてスラブの鋳造速度を常用速度にすることができるため、液体鋼を比較的高い過熱温度に維持することができ、熱間圧延および再加熱処理においてスラブの吐出し温度を低くすることができ、圧延の最終温度、巻取温度などを常用温度に維持することができるため、熱間圧延処理において帯鋼に焼きならし処理を行なう必要はない。
DISCLOSURE OF THE INVENTION An object of the present invention is to provide a non-oriented electrical steel sheet having no wavy defects and a method for producing the same. The cooling rate of the slab in the continuous casting processing, strictly controlling the temperature difference in the longitudinal direction of the slab in the heating furnace, by controlling the cooling before increasing specifications slab, no wavy defects Intermediate grades non-oriented Steel sheet can be manufactured. In the manufacturing method, the operation is easy, the production cost of the steel sheet is reduced, energy is saved, the environment is protected, and the manufactured steel sheet has excellent magnetism. Moreover, since the casting speed of the slab can be set to a normal speed in the continuous casting process, the liquid steel can be maintained at a relatively high superheating temperature, and the discharge temperature of the slab can be lowered in the hot rolling and reheating processes. Since the final temperature of rolling, the coiling temperature, and the like can be maintained at ordinary temperatures, it is not necessary to normalize the strip steel in the hot rolling process .
上記目的を達成するために、本発明の技術的解決案は、波状欠陥のない中級鋼種無方向性電磁鋼板を提供し、その化学組成の重量パーセントは、Ｃが０．００５％未満、Ｓｉが１．２〜２．２％、Ｍｎが０．２〜０．４％、Ｐが０．２％未満、Ｓが０．００５％未満、Ａｌが０．２〜０．６％、Ｎが０．００５％未満、Ｏが０．００５％未満、残りはＦｅおよび不可避的不純物である。 To achieve the above object, technical solving solution of the present invention is to provide a no wavy defects Intermediate grades non-oriented electrical steel sheet, percent by weight of the chemical composition, C is less than 0.005%, Si is 1.2 to 2.2%, Mn is 0.2 to 0.4%, P is less than 0.2%, S is less than 0.005%, Al is 0.2 to 0.6%, N Is less than 0.005%, O is less than 0.005%, the rest is Fe and inevitable impurities.
本発明の他の設計案において、Ｃは０．００５％未満である。Ｃは、結晶粒の成長を強く抑制し、帯鋼の鉄損の増大をもたらし、重大な磁気的老化を生じさせ易い元素である。一方、Ｃは、γ相領域をさらに増大することができるため、焼きならし処理において、α相領域とγ相領域との間の遷移量を増大し、よって、Ａｃｌ点を著しく減少させ、かつ結晶構造を細分化することができる。したがって、Ｃは０．００５％未満に制御されることが必要である。 In another design scheme of the invention, C is less than 0.005%. C is an element that strongly suppresses the growth of crystal grains, increases the iron loss of the steel strip, and easily causes significant magnetic aging. On the other hand, C can further increase the γ-phase region, so that in the normalization process, the amount of transition between the α-phase region and the γ-phase region is increased, thus significantly reducing the Acl point, and The crystal structure can be subdivided. Therefore, C needs to be controlled to less than 0.005%.
Ｓｉは１．２％〜２．２％である。Ｓｉは、鋼の抵抗率を増大させるための効果的な元素である。Ｓｉの含有量が１．２％より低い場合、鋼の電磁性能が悪くなる。一方Ｓｉの含有量が２．２％より高い場合、熱間圧延処理において相転移ができなくなり、冷間加工性が悪くなる。 Si is 1.2% to 2.2%. Si is an effective element for increasing the resistivity of steel. Si content is 1.2% lower than if the steel of the electromagnetic performance deteriorates. On the other hand, when the content of Si is higher than 2.2%, phase transition cannot be performed in the hot rolling process, and cold workability is deteriorated.
Ａｌは０．２％〜０．６％である。Ａｌは、鋼の抵抗率を増大させる有効的な元素である。Ａｌの含有量が０．２％より低い場合、電磁性能が安定せず、Ａｌの含有量が０．６％より高い場合、溶融処理および鋳込み処理が困難となり、製造費用も増大する。 Al is 0.2% to 0.6%. Al is an effective element that increases the resistivity of steel. If the content of Al is less than 0.2%, conductive magnetic performance is not stable, the content of Al is higher if than 0.6%, it becomes difficult to melt process and cast process, also increases manufacturing costs.
Ｍｎは０．２％〜０．４％である。元素ＳｉおよびＡｌと同様に、Ｍｎは、鋼の抵抗率を増大させ、かつ電気鋼の表面状態を向上させることができる。したがって０．２％以上のＭｎを追加することが必要である。一方、Ｍｎの含有量が０．４％より高い場合、溶融処理および鋳込み処理が困難となり、製造費用も増大する。 Mn is 0.2% to 0.4%. Like the elements Si and Al, Mn can increase the resistivity of the steel, to improve the surface condition of and electrical steel. Therefore, it is necessary to add 0.2% or more of Mn. On the other hand, when the content of Mn is higher than 0.4%, the melting process and the casting process are difficult, and the manufacturing cost is increased.
Ｐは０．２％未満である。鋼に一定量のリンを追加することは、鋼板の加工性を向上させることができるが、リンの含有量が０．２％より高くなると、鋼板の冷間圧延加工性が悪化する。 P is less than 0.2%. Adding a certain amount of phosphorus to the steel can improve the workability of the steel sheet, but if the phosphorus content is higher than 0.2% , the cold rolling workability of the steel sheet deteriorates.
Ｓは０．００５％未満である。Ｓの含有量が０．００５％より高い場合、ＭｎＳなどの硫化物の堆積量が大幅に増え、結晶粒の成長が強く妨げられ、鉄損が悪化する。 S is less than 0.005%. High If the content is higher than 0.005% of S, the deposition amount of e increased significantly of sulfides such as MnS, growth of the crystal grain is strongly hindered, iron loss is worse.
Ｎは０．００５％未満である。Ｎの含有量が０．００５％より高い場合、ＡｌＮなどの窒化物の堆積量が大幅に増え、結晶粒の成長が強く妨げられ、鉄損が悪化する。 N is less than 0.005%. High if the content is higher than 0.005% of N, deposit amount example increased significantly nitrides such as AlN, growth of crystal grain is strongly hindered, iron loss is deteriorated.
Ｏは０．００５％未満である。Ｏの含有量が０．００５％より高い場合、Ａｌ２Ｏ３などの酸化物の不純物量が大幅に増え、結晶粒の成長が強く妨げられ、鉄損が悪化する。 O is less than 0.005%. O high if the content is higher than 0.005%, the amount of impurities example increased significantly oxides such as Al 2 O 3, the growth of crystal grain is strongly hindered, iron loss is deteriorated.
本発明の波状欠陥のない無方向性電磁鋼板を製造するための方法は、
１）無方向性電磁鋼板の化学組成の重量パーセントは、Ｃ＜０．００５％、Ｓｉは１．２〜２．２％、Ｍｎは０．２〜０．４％、Ｐ＜０．２％、Ｓ＜０．００５％、Ａｌは０．２〜０．６％、Ｎ＜０．００５％、Ｏ＜０．００５％、残りはＦｅおよび不可避的不純物であり、上記化学組成に従って、鋼鉄溶融処理、回転炉製錬、ＲＨ精製、ならびに連続鋳込みによってスラブが得られるステップを含み、連続鋳込みの際に、二次冷却水の流量は１００〜１９０ｌ／分に制御され、液体鋼の平均過熱温度は１０〜４５℃に制御され、さらに、
２）スラブが加熱され、熱間圧延されるステップを含み、
スラブの吐出し温度は１０５０〜１１５０℃であり、スラブが加熱される際に、その長さ方向の任意二点間の温度差は２５℃より低く、熱間圧延処理は粗圧延処理および仕上げ圧延処理を含み、仕上げ圧延処理における入口温度は９７０℃以上であり、さらに、
３）酸洗い、冷間圧延、アニーリング、およびコーティングによって、無方向性電磁鋼板の完成品が得られるステップを含む。
The method for producing the non-oriented electrical steel sheet without wavy defects of the present invention is as follows:
1) The weight percent of the chemical composition of the non-oriented electrical steel sheet is C <0.005%, Si is 1.2-2.2%, Mn is 0.2-0.4%, P <0.2%. S <0.005%, Al 0.2-0.6%, N <0.005%, O <0.005%, the rest are Fe and unavoidable impurities, steel according to the above chemical composition Including steps of melting treatment, rotary furnace smelting , RH refining, and continuous casting to obtain a slab. During continuous casting, the flow rate of secondary cooling water is controlled to 100 to 190 l / min, and the average superheating of liquid steel The temperature is controlled at 10-45 ° C., and
2) comprising a step in which the slab is heated and hot rolled;
Discharge temperature of the slab is from 1,050 to 1150 ° C., when the slab is heated, the temperature difference between any two points in the length direction of that is lower than 25 ° C., hot rolling process rough rolling process and finishing includes a rolling treatment, an inlet temperature in the finishing rolling process is at 970 ° C. or higher, further,
3) including a step of obtaining a finished product of non- oriented electrical steel sheet by pickling, cold rolling, annealing, and coating.
本発明の波状欠陥のない中級鋼種の無方向性電磁鋼板およびその製造方法は、以下の工程を含む。 The non-oriented electrical steel sheet of intermediate grade without wavy defects of the present invention and the manufacturing method thereof include the following steps.
鋳込み処理において、液体鋼の平均過熱温度は、１０〜４５℃に制御される。連続鋳込み処理において、スラブ中の等軸晶率を向上させ、スラブ中の柱状晶が大きく成長するのを回避するために、冷却水の流量が１００〜１９０ｌ／分に調整される。 In the casting process, the average superheating temperature of the liquid steel is controlled at 10 to 45 ° C. In the continuous casting processing, improve the equiaxed Akiraritsu in the slab, in order to avoid columnar crystals in the slab grow larger, the flow amount of the cooling water is adjusted to 100～190L / min.
帯鋼を不十分に再結晶化させるようにスラブの表面温度に影響を及ぼす比較的低い温度は避けるべきである。したがって、スラブが加熱される際に、その長さ方向の任意二点間の温度差は２５℃より低くなるように制御される。スラブの透かし点間の温度差は２５℃以内に制限され、スラブの均熱段における滞在時間は、スラブの両面の温度を等しくなるに、４５分以上にする。 Relatively low temperatures that affect the surface temperature of the slab so as to cause the steel strip to recrystallize poorly should be avoided. Therefore, when the slab is heated, the temperature difference between any two points in the length direction is controlled to be lower than 25 ° C. The temperature difference between the slab watermarks is limited to 25 ° C., and the residence time in the slab soaking stage is 45 minutes or more to equalize the temperature on both sides of the slab.
スラブの吐出し温度は１１５０℃以下に下げることができ、ＭｎＳ、ＡｌＮなどの不純物が固溶することによって完成品帯鋼の磁性を悪化することを防止する。スラブは、熱間圧延によって、厚さ２．０ｍｍ〜２．８ｍｍの熱圧延した鋼板に圧延される。再結晶化を充分にさせるために、粗圧延処理および仕上げ圧延処理の前に、保温装置を利用して、スラブと中間鋼片とを各々保温する。仕上げ圧延処理における入口温度は、９７０℃以上に制御され、最終圧延温度は約８５０℃に制御され、巻取温度は約６００℃に制御される。 Discharge temperature of the slab can be reduced to 1150 ℃ below, MnS, AlN of any impurities is prevented from deterioration of the magnetic properties of the finished product steel strip by solid solution. The slab is rolled into a hot-rolled steel plate having a thickness of 2.0 mm to 2.8 mm by hot rolling . In order to ensure sufficient recrystallization, the slab and the intermediate steel slab are each kept warm using a heat retaining device before the rough rolling process and the finish rolling process. Inlet temperature in the finishing rolling process is controlled in 9 70 ° C. or higher, the final rolling temperature is controlled to about 850 ° C., the coiling temperature is controlled to about 600 ° C..
熱圧延した鋼板は、０．５ｍｍの厚さを有する帯鋼に圧延され、次いで乾燥雰囲気の中で連続アニーリングされる。帯鋼に連続アニーリング処理を行う間に、予熱段で快速昇温することによって、加熱速度を１０００℃／分以上にし、かつ炉内の雰囲気を制御することによって、鋼の電磁性能をさらに向上させる。 Hot rolled steel plate is rolled to strip that have a thickness of 0.5 mm, then a continuous A kneeling in Drying atmosphere. While carrying out continuous annealing treatment on the strip steel, the heating performance is increased to 1000 ° C./min or more by rapidly raising the temperature in the preheating stage, and the atmosphere in the furnace is controlled to further improve the electromagnetic performance of the steel. .
本発明において、組成に対する制御条件に基づいて、鋼中のシリコン含有量が２．２％を越えた後、電磁撹拌を利用しないまたは弱い電磁撹拌を利用する場合、シリコンの含有量が比較的高いため、スラブ中の柱状晶は大きく成長し、電磁撹拌の力が柱状晶を破砕するのには十分でなく、さらに、破砕された柱状晶の一部が再び凝集して成長することになるため、スラブ中の細かい等軸結晶の比率が比較的低くなり、大きく成長した柱状晶の比率が比較的高くなる。したがって、完成品帯鋼の表面の波状欠陥を制御するために、電磁撹拌の強さを強くする必要がある。 In the present invention , based on the control conditions for the composition, when the silicon content in the steel exceeds 2.2%, when the electromagnetic stirring is not used or when the weak magnetic stirring is used , the silicon content is relatively high. Therefore, the columnar crystals in the slab grow large, and the force of electromagnetic stirring is not sufficient to crush the columnar crystals , and further, some of the crushed columnar crystals will aggregate again and grow. The proportion of fine equiaxed crystals in the slab is relatively low, and the proportion of columnar crystals that have grown large is relatively high. Therefore, in order to control the undulating surface defects of the finished product steel strip, Ru need to strongly the intensity of the electromagnetic stirring.
本発明において、シリコンの含有量が２．２％未満である場合、シリコンの含有量は、スラブの冷却速度に比べて、柱状晶の成長に影響が弱いであるため、連続鋳込み処理における冷却水の流量を調整することによって、柱状晶の成長方向におけるスラブの熱流勾配を減少させ、大きく成長する柱状晶の比率を効果的に減少することができる。さらに、スラブの加熱処理において、スラブがローラー軌道に接触する場所におけるスラブの温度が比較的低いであり、スラブの内部の繊維組織の再結晶化を影響し、繊維組織が均質にならず完成品に残ることを考慮して、スラブの透かし点の温度を厳密に制御する必要がある。仕上げ圧延処理における入口温度を向上させる主な理由は、圧延処理において、柱状晶の破砕および除去を容易にし、熱間圧延した帯鋼中の繊維組織の再結晶化率を向上させるためである。 In the present invention, when the silicon content is less than 2.2%, the silicon content has less influence on the growth of columnar crystals compared to the cooling rate of the slab. By adjusting the flow rate of slab, the heat flow gradient of the slab in the growth direction of the columnar crystals can be reduced, and the ratio of the columnar crystals that grow greatly can be effectively reduced . Furthermore, in the heat treatment of the slab, the temperature of the slab where the slab contacts the roller track is relatively low, which affects the recrystallization of the fiber structure inside the slab, and the fiber structure does not become homogeneous and is a finished product. Therefore, it is necessary to strictly control the temperature of the slab watermark . The main reason for improving the inlet temperature in the finish rolling process is to facilitate the crushing and removal of columnar crystals in the rolling process and to improve the recrystallization rate of the fiber structure in the hot-rolled steel strip .
また、シリコンの含有量が１．２％以下の場合、熱間圧延処理において、γ相からα相への相転移は十分であるため、その後の完成品の表面に波状欠陥が生じることはない。 In addition, when the silicon content is 1.2% or less , the phase transition from the γ phase to the α phase is sufficient in the hot rolling process , so that no wavy defect is generated on the surface of the subsequent finished product. .
また、２対または３対の電磁撹拌ロールが利用される場合、スラブ中の等軸晶率を増加するために、強い電磁撹拌力によってスラブ中の柱状晶をできる限りに破砕し、細かい等軸結晶に変化させる。また、熱処理においてスラブの吐出し温度を大幅に上昇させることによって、スラブの内部でγ相からα相への相転移を生じさせるとともに、高温状態を利用してスラブの内部の再結晶化構造を拡大させることによってスラブの再結晶率を向上させる。以上のやり方は、設備投資およびエネルギ消費を増加する他に、電磁撹拌が液体鋼の過熱温度と正確にマッチすることが困難であることもある。液体鋼の過熱温度が不適切に制御された場合、電磁撹拌の制御が安定せず、予期する影響を得ることは困難である。また、スラブの吐出し温度を上昇させることによって、加熱炉の加熱負荷分布が進み、スラブの高温加熱時間が比較的長くなり、完成品帯鋼の磁性に影響を及ぼす。高級シリコン鋼種の場合、この方法は、帯鋼の縁部に品質欠陥をもたらすことがある。 In addition, when two or three pairs of electromagnetic stirring rolls are used, in order to increase the equiaxed crystal ratio in the slab, the columnar crystals in the slab are crushed as much as possible by a strong electromagnetic stirring force, and fine equiaxed Change to crystals. Further, by increasing considerably the temperature discharging of the slab in the heat treatment, with causing phase transition from γ phase within the slab to α phase, using a high-temperature state recrystallization of internal slab structure The recrystallization rate of the slab is improved by expanding the slab. In addition to increasing capital investment and energy consumption , the above approach may make it difficult for electromagnetic stirring to accurately match the superheat temperature of liquid steel. If superheat of the liquid steel has been improperly controlled, not a cheap Teise control of the electromagnetic stirring, it is difficult to obtain the effect expected to. Further, by increasing the discharge temperature of the slab, the heating load distribution of the heating furnace advances, the high temperature heating time of the slab becomes relatively long, and affects the magnetism of the finished product strip steel . In the case of high grade silicon steel grades , this method can lead to quality defects at the edge of the strip.
本発明は、特別な化学組成の条件下で、連続鋳込み処理における冷却水の流量を、スラブの熱流束勾配が柱状晶の成長方向に沿って減少するように調整することができ、したがって、大きく成長する柱状晶の比率を効果的に減少させることができる。より重要なことは、この方法は、液体鋼の過熱温度の変化に影響されず、したがって比較的広い範囲に適用することができる。また、冷却水の流量の調整および制御は比較的簡単であり、実施の困難度は低く、安定性が良い。さらに、スラブ吐出し温度を低くすることによって、設備負荷が軽減され、鋼中の細かい不純物の析出によって最終製品の磁性に対する影響を防止さすることができる。より低い温度でスラブを加熱するときに、スラブ中の透かし点の温度を調整することによって、熱間圧延処理におけるスラブの繊維組織の再結晶化率を上昇させ、かつ熱間圧延した帯鋼におけるスラブの組織の均質性を向上させることができ、完成品帯鋼の表面の波状欠陥を減少させることに寄与する。 The present invention is, under the conditions of a particular chemical composition, it is possible to adjust the flow rate of the cooling water in the continuous casting process, as the heat flux gradients in the slab decreases along the growth direction of the columnar grain, therefore, greatly the ratio of columnar crystals you growth can be effectively reduced. More importantly, this method is not affected by changes in the superheat temperature of the liquid steel and can therefore be applied over a relatively wide range. In addition, the adjustment and control of the flow rate of the cooling water is relatively simple, the difficulty of implementation is low, and the stability is good. Furthermore, by lowering the slab discharge temperature, the equipment load is reduced, and the influence of the final product on magnetism can be prevented by the precipitation of fine impurities in the steel. When heating the slab at a lower temperature, the recrystallization rate of the slab fiber structure in the hot rolling process is increased by adjusting the temperature of the watermark in the slab, and in hot rolled steel strip The homogeneity of the structure of the slab can be improved, which contributes to the reduction of wavy defects on the surface of the finished product strip steel.
発明の詳細な説明
以下、実施例および図面を参照し、本発明をさらに説明する。
Detailed Description of the Invention
The present invention will be further described below with reference to examples and drawings.
第１の実施例
連続鋳造タンディッシュにおける液体鋼の化学組成は、以下のように制御される。Ｃは０．００１％、Ｓｉは１．２２％、Ｍｎは０．２５％、Ｐは０．０２％、Ｓは０．００３％、Ａｌは０．３３％、Ｎは０．００１％、Ｏは０．００４％、残りはＦｅおよび不可避的不純物である。液体鋼の平均過熱温度は３４．６℃であり、鋳造速度は１．０７ｍ／分であり、冷却水の流量は１８５Ｌ／分であり、スラブの温度降下速度は１１．６分／℃であり、鋳造機の出口におけるスラブの表面温度は７１０℃であり、等軸晶率は４３％である。加熱炉において、透かし点の間の温度差は２２℃であり、スラブの均一加熱段における滞留時間は４６分である。圧延処理は１１２５℃にて３時間加熱した後に行われ、仕上げ圧延処理において、入口の温度は９７８℃であり、最終圧延温度は８５６℃であり、巻取温度は５６７℃である。熱間圧延した鋼板は、一次冷間圧延によって、０．５ｍｍ厚さの帯鋼に圧延され、次いで乾燥雰囲気の中で連続的にアニーリングされる。完成品帯鋼の表面に波状欠陥は発生せず、鉄損は４．７４３Ｗ／ｋｇであり、磁気誘導は１．７２７Ｔである。
Chemical composition of the liquid steel in the first embodiment the continuous casting Zota tundish is controlled as follows. C is 0.001%, Si is 1.22%, Mn is 0.25%, P is 0.02%, S is 0.003%, Al is 0.33%, N is 0.001%, O 0.004% or the remainder being F e and inevitable impurities. The average superheat temperature of liquid steel is 34.6 ° C., the casting speed is 1.07 m / min, the flow rate of cooling water is 185 L / min, and the temperature drop rate of slab is 11.6 min / ° C. Yes, the surface temperature of the slab at the exit of the casting machine is 710 ° C., and the equiaxed crystal ratio is 43%. In the heating furnace, the temperature difference between the watermark point is 22 ° C., the residence time in the uniform heating stage of the slab is 46 minutes. The rolling process is performed after heating at 1125 ° C. for 3 hours. In the finish rolling process, the inlet temperature is 978 ° C., the final rolling temperature is 856 ° C., and the winding temperature is 567 ° C. The hot-rolled steel sheet is rolled into a 0.5 mm-thick strip by primary cold rolling , and then continuously annealed in a dry atmosphere . No wavy defects are generated on the surface of the finished steel strip , the iron loss is 4.743 W / kg, and the magnetic induction is 1.727 T.
第２の実施例
連続鋳造タンディッシュにおける液体鋼の化学組成は以下のように制御される。Ｃは０．００２％、Ｓｉは１．４２％、Ｍｎは０．３０％、Ｐは０．０６％、Ｓは０．００２％、Ａｌは０．２５％、Ｎは０．００２％、Ｏは０．００２％、残りはＦｅおよび不可避的不純物である。液体鋼の平均過熱温度は３１．４℃であり、鋳造速度は１．０４ｍ／分であり、冷却水の流量は１７５Ｌ／分であり、スラブの温度降下速度は９．６分／℃であり、鋳造機の出口におけるスラブの表面温度は６８０℃であり、等軸晶率は５７％である。加熱炉において、透かし点の間の温度差は２２℃であり、スラブの均一加熱段における滞留時間は４８分である。圧延処理は１１３５℃にて３時間加熱した後に行われ、仕上げ圧延処理において、入口の温度は９７３℃であり、最終圧延温度は８５３℃であり、巻取温度は５６３℃である。熱間圧延した鋼板は、一次冷間圧延によって、０．５ｍｍ厚さの帯鋼に圧延され、次いで乾燥雰囲気の中で連続的にアニーリングされる。完成品帯鋼の表面に波状欠陥は発生せず、鉄損は３．１３０Ｗ／ｋｇであり、磁気誘導は１．７４１Ｔである。
Chemical composition of the liquid steel in the second embodiment the continuous casting Zota tundish is controlled as follows. C is 0.002%, Si is 1.42%, Mn is 0.30%, P is 0.06%, S is 0.002%, Al is 0.25%, N is 0.002%, O Is 0.002%, the rest is Fe and inevitable impurities. The average superheat temperature of the liquid steel is 31.4 ° C., the casting speed is 1.04 m / min, the flow rate of cooling water is 175 L / min, and the temperature drop rate of the slab is 9.6 min / ° C. Yes, the surface temperature of the slab at the exit of the casting machine is 680 ° C., and the equiaxed crystal ratio is 57%. In the heating furnace, the temperature difference between the watermark point is 22 ° C., the residence time in the uniform heating stage of the slab is 48 minutes. The rolling process is performed after heating at 1135 ° C. for 3 hours. In the finish rolling process, the inlet temperature is 973 ° C., the final rolling temperature is 853 ° C., and the winding temperature is 563 ° C. The hot-rolled steel sheet is rolled into a 0.5 mm-thick strip by primary cold rolling , and then continuously annealed in a dry atmosphere . No wavy defects occur on the surface of the finished steel strip , the iron loss is 3.130 W / kg, and the magnetic induction is 1.741T.
第３の実施例
連続鋳込みタンディッシュにおける液体鋼の化学組成は以下のように制御される。Ｃは０．００２％、Ｓｉは１．４９％、Ｍｎは０．４９％、Ｐは０．０２％、Ｓは０．００３％、Ａｌは０．５９％、Ｎは０．００１％、Ｏは０．００２％、残りはＦｅおよび不可避的不純物である。液体鋼の平均過熱温度は２８．７℃であり、鋳造速度は０．９９ｍ／分であり、冷却水の流量は１８９Ｌ／分であり、スラブの温度降下速度は８．７分／℃であり、鋳造機の出口におけるスラブの表面温度は６６０℃であり、等軸晶率は６３％である。加熱炉において、透かし点間の温度差は２４℃であり、スラブの均一加熱段における滞留時間は５３分である。圧延処理は１１０２℃にて３時間加熱した後に行われ、仕上げ圧延処理において、入口の温度は９８３℃であり、最終圧延温度は８５４℃であり、巻取温は５７５℃である。熱間圧延した鋼板は、一次冷間圧延によって、０．５ｍｍ厚さの帯鋼に圧延され、次いで乾燥雰囲気の中で連続的にアニーリングされる。完成品帯鋼の表面に波状欠陥は発生せず、鉄損は３．５５９Ｗ／ｋｇであり、磁気誘導は１．７３７Ｔである。
Third embodiment
The chemical composition of the liquid steel in the continuous casting tundish is controlled as follows. C is 0.002%, Si is 1.49%, Mn is 0.49%, P is 0.02%, S is 0.003%, Al is 0.59%, N is 0.001%, O Is 0.002%, the rest is Fe and inevitable impurities. The average superheat temperature of liquid steel is 28.7 ° C., the casting speed is 0.99 m / min, the flow rate of cooling water is 189 L / min, and the temperature drop rate of slab is 8.7 min / ° C. Yes, the surface temperature of the slab at the exit of the casting machine is 660 ° C., and the equiaxed crystal ratio is 63%. In the heating furnace, the temperature difference between the watermarks is 24 ° C., and the residence time in the uniform heating stage of the slab is 53 minutes. The rolling process is performed after heating at 1102 ° C. for 3 hours. In the finish rolling process, the inlet temperature is 983 ° C., the final rolling temperature is 854 ° C., and the winding temperature is 575 ° C. The hot-rolled steel sheet is rolled into a 0.5 mm-thick strip by primary cold rolling , and then continuously annealed in a dry atmosphere . No wavy defects are generated on the surface of the finished steel strip , the iron loss is 3.559 W / kg, and the magnetic induction is 1.737 T.
第４の実施例
連続鋳込みタンディッシュにおける液体鋼の化学組成は以下のように制御される。Ｃは０．００１％、Ｓｉは２．１２％、Ｍｎは０．２５％、Ｐは０．０１％、Ｓは０．００２％、Ａｌは０．３６％、Ｎは０．００１％、Ｏは０．００４％、残りはＦｅおよび不可避的不純物である。液体鋼の平均過熱温度は３１．２℃であり、鋳造速度は０．９５ｍ／分であり、冷却水の流量は１７３Ｌ／分であり、スラブの温度降下速度は１３．２分／℃であり、鋳造機の出口におけるスラブの表面温度は６８０℃であり、等軸晶率は５９％である。加熱炉において、透かし点の間の温度差は２０℃であり、スラブの均一加熱段における滞留時間は４８分である。圧延処理は１０９７℃にて３時間加熱した後に行われ、仕上げ圧延処理において、入口の温度は９７２℃であり、最終圧延温度は８４４℃であり、巻取温度は５８３℃である。熱間圧延した鋼板は、一次冷間圧延によって、０．５ｍｍ厚さの帯鋼に圧延され、次いで乾燥雰囲気の中で連続的にアニーリングされる。完成品帯鋼の表面に波状欠陥は発生せず、鉄損は２．８３３Ｗ／ｋｇであり、磁気誘導は１．７２６Ｔである。
Fourth embodiment
The chemical composition of the liquid steel in the continuous casting tundish is controlled as follows. C is 0.001%, Si is 2.12%, Mn is 0.25%, P is 0.01%, S is 0.002%, Al is 0.36%, N is 0.001%, O 0.004% or the remainder being F e and inevitable impurities. The average superheat temperature of liquid steel is 31.2 ° C., the casting speed is 0.95 m / min, the flow rate of cooling water is 173 L / min, and the temperature drop rate of slab is 13.2 min / ° C. Yes, the surface temperature of the slab at the exit of the casting machine is 680 ° C., and the equiaxed crystal ratio is 59%. In the heating furnace, the temperature difference between the watermark point is 20 ° C., the residence time in the uniform heating stage of the slab is 48 minutes. The rolling process was performed after heating at 1097 ° C. for 3 hours. In the finish rolling process, the inlet temperature was 972 ° C., the final rolling temperature was 844 ° C., and the winding temperature was 583 ° C. The hot-rolled steel sheet is rolled into a 0.5 mm-thick strip by primary cold rolling , and then continuously annealed in a dry atmosphere . No wavy defects are generated on the surface of the finished steel strip , the iron loss is 2.833 W / kg, and the magnetic induction is 1.726 T.
比較例
連続鋳込みタンディッシュにおける液体鋼の化学組成は以下のように制御される。Ｃは０．００１％、Ｓｉは１．４７％、Ｍｎは０．３２％、Ｐは０．０２％、Ｓは０．００３％、Ａｌは０．２５％、Ｎは０．００２％、Ｏは０．００２％、残りはＦｅおよび不可避的不純物である。液体鋼の平均過熱温度は２８．９℃であり、鋳造速度は１．０３ｍ／分であり、冷却水の流量は２５７Ｌ／分であり、スラブの温度降下速度は１７．４分／℃であり、鋳造機の出口におけるスラブの表面温度は５８０℃であり、等軸晶率は２８％である。加熱炉において、透かし点の間の温度差は３７℃であり、スラブの均一加熱段における滞留時間は４１分である。圧延処理は１１５３℃にて３時間加熱した後に行われ、仕上げ圧延処理において、入口の温度は９４７℃であり、最終圧延温度は８４７℃であり、巻取温度は５６７℃である。熱間圧延した鋼板は、一次冷間圧延によって、０．５ｍｍ厚さの帯鋼に圧延され、次いで乾燥雰囲気の中で連続的にアニーリングされる。完成品帯鋼の表面の波状欠陥の発生の比率は９０％以上と高くなり、鉄損は３．２７３Ｗ／ｋｇであり、磁気誘導は１．７３６Ｔである。
Comparative example
The chemical composition of the liquid steel in the continuous casting tundish is controlled as follows. C is 0.001%, Si is 1.47%, Mn is 0.32%, P is 0.02%, S is 0.003%, Al is 0.25%, N is 0.002%, O Is 0.002%, the rest is Fe and inevitable impurities. The average superheat temperature of liquid steel is 28.9 ° C, the casting speed is 1.03m / min, the flow rate of cooling water is 257L / min, and the temperature drop rate of slab is 17.4min / ° C The surface temperature of the slab at the exit of the casting machine is 580 ° C., and the equiaxed crystal ratio is 28%. In the heating furnace, the temperature difference between the watermark point is 37 ° C., the residence time in the uniform heating stage of the slab is 41 minutes. The rolling process is performed after heating at 1153 ° C. for 3 hours. In the finish rolling process, the inlet temperature is 947 ° C., the final rolling temperature is 847 ° C., and the winding temperature is 567 ° C. The hot-rolled steel sheet is rolled into a 0.5 mm-thick strip by primary cold rolling , and then continuously annealed in a dry atmosphere . The ratio of occurrence of the wavy surface defects of the finished product steel strip is increased to 90% or more, the iron loss is 3.273W / kg, the magnetic induction is 1.736T.
図１は、冷却水の流量とスラブ中の等軸晶率との関係を示す。図１に見られるように、電磁撹拌を利用しない前提下、冷却水の流量を減少させ、１９０Ｌ／分以下に厳密に制御することによって、スラブ中の等軸晶率は著しく増加する。実施例では、液体鋼の過熱温度が比較的高いときにスラブ中の等軸晶率が制御されることができた。これらの実施例のうち第４の実施例では、冷却水の流量が１７３Ｌ／分である場合、スラブ中の等軸晶率は５９％であった。比較例では、冷却水の流量が２５７Ｌ／分である場合、スラブ中の等軸晶率はわずか２８％であった。また第３の実施例では、液体鋼の加熱温度を低くすることによって、スラブ中の等軸晶率の制御はより良くなり、６３％であった。 FIG. 1 shows the relationship between the flow rate of cooling water and the equiaxed crystal ratio in the slab. As seen in Figure 1, under the premise that does not use electromagnetic撹拌 reduces the flow rate of the cooling water, by strictly controlling the 190 L / min or less, equal JikuAkiraritsu in slab significantly increases. In the examples, the equiaxed crystal ratio in the slab could be controlled when the superheating temperature of the liquid steel was relatively high . Among these examples, in the fourth example, when the flow rate of the cooling water was 173 L / min, the equiaxed crystal ratio in the slab was 59 %. In the comparative example, when the cooling water flow rate was 257 L / min, the equiaxed crystal ratio in the slab was only 28% . In the third embodiment, by lowering the heating temperature of the liquid steel, control etc. JikuAkiraritsu in the slab becomes better, and Tsu der 63%.
図２は、熱間圧延の仕上げ圧延処理において入口温度と、完成品の波状欠陥の発生率との関係を示す。統計結果は、熱間圧延の仕上げ圧延処理において入口温度を９７０℃より高くまで上昇させることによって、熱間圧延処理においてスラブの繊維組織の再結晶化率が著しく増大されるため、完成品帯鋼に波状欠陥の発生率を大幅に減少させるということをしめした。比較例では、帯鋼の熱間圧延仕上げ圧延処理において、入口温度は９７０℃未満であり、完成品帯鋼の表面に波状欠陥が発生する比率は９０％以上と高くなる。いくつかの実施例では、帯鋼の熱間圧延仕上げ圧延処理において、入口温度は９７０℃を超えており、完成品帯鋼の表面には波状欠陥は発生しない。 FIG. 2 shows the relationship between the inlet temperature and the rate of occurrence of wavy defects in the finished product in the finish rolling process of hot rolling . The statistical results show that the recrystallization rate of the fiber structure of the slab is significantly increased in the hot rolling process by raising the inlet temperature to higher than 970 ° C. in the finish rolling process of the hot rolling, so that the finished steel strip It was shown that the incidence of wavy defects was greatly reduced . In the comparative example, the hot rolling finish rolling process of strip steels, the inlet temperature is less than 970 ° C., the ratio of wavy defects are generated on the surface of the finished steel strip is 90% or more and higher due. In some embodiments, in the hot strip finish rolling process of the steel strip, the inlet temperature exceeds 970 ° C., and no wavy defects occur on the surface of the finished strip steel .
図３は、スラブの吐出し温度と完成品の磁性との関係を示す。スラブの吐出し温度が高くなることにつれて、完成品の磁性が悪化する。 FIG. 3 shows the relationship between the discharge temperature of the slab and the magnetism of the finished product. Discharge temperature of the slab as it higher due, magnetic properties of the finished product is deteriorated.
図４および図５は、異なる透かし点温度に対応する、熱間圧延した帯鋼の金属相組織を示す図である。透かし点温度は、第１〜第４の実施例においてすべて２５℃未満であり、したがって熱間圧延した帯鋼の再結晶化組織は非常に均質であり、繊維組織は完全に消える。これに対し、比較例では透かし点における温度は３７℃まで高くなり、熱間圧延した帯鋼の繊維組織が明らかであり、その後の冷間圧延およびアニーリング処理において再結晶化しにくくなり、構造が均質になることができず、完成品に残り、最終的に起伏のある波状欠陥を形成する。 4 and 5 are diagrams showing the metal phase structure of hot-rolled steel strip corresponding to different watermark temperatures. The watermark temperature is all below 25 ° C. in the first to fourth examples, so that the recrystallized structure of the hot rolled steel strip is very homogeneous and the fiber structure disappears completely. In contrast, the temperature becomes as high 37 ° C. in the watermark point ratio Comparative Examples are apparent hot fibrous tissue of rolled strip steel, hardly re-crystallized in the subsequent cold rolling and annealing treatment, structure It cannot be homogenous and remains in the finished product, eventually forming undulating wavy defects.
Claims (2)
１）無方向性電磁鋼板の化学組成の重量パーセントは、Ｃ＜０．００５％、Ｓｉは１．２〜２．２％、Ｍｎは０．２〜０．４％、Ｐ＜０．２％、Ｓ＜０．００５％、Ａｌは０．２〜０．６％、Ｎ＜０．００５％、Ｏ＜０．００５％、残りはＦｅおよび不可避的不純物であり、前記化学組成に従って、鋼鉄溶融処理、回転炉製錬、ＲＨ精製、ならびに連続鋳込みによってスラブが得られるステップを備え、連続鋳込みの際に、二次冷却水の流量は１００〜１９０ｌ／分に制御され、液体鋼の平均過熱温度は１０〜４５℃に制御され、さらに、
２）スラブが加熱され、熱間圧延されるステップを備え、
スラブの吐出し温度は１０５０〜１１５０℃であり、スラブが加熱される際に、その長さ方向の任意二点間の温度差は２５℃より低く、熱間圧延処理は粗圧延処理および仕上げ圧延処理を含み、仕上げ圧延処理において、入口温度は９７０℃以上であり、さらに、
３）酸洗い、冷間圧延、アニーリング、およびコーティングによって、無方向性電磁鋼板の完成品が得られるステップを備える、方法。 A method for producing a non-oriented electrical steel sheet without wavy defects according to claim 1,
1) The weight percent of the chemical composition of the non-oriented electrical steel sheet is C <0.005%, Si is 1.2-2.2%, Mn is 0.2-0.4%, P <0.2%. , S <0.005%, Al is 0.2~0.6%, N <0.005%, O <0.005%, the remainder being F e and inevitable impurities, according to the chemical composition, the steel melt processing, rotary furnace smelting, comprising the step of slab is obtained by the RH refining, and cast continuously, during the continuous casting, the flow of secondary cooling water is controlled to 100～190L / min, the average of the liquids steel The superheating temperature is controlled at 10 to 45 ° C., and
2) comprising a step in which the slab is heated and hot rolled;
Discharge temperature of the slab is from 1,050 to 1150 ° C., when the slab is heated, the temperature difference between the arbitrary two points of its length is lower than 25 ° C., hot rolling process So圧Nobesho sense and wherein the finishing rolling process, the finish rolling process, the inlet temperature is 970 ° C. or higher, further,
3) A method comprising the steps of obtaining a finished non- oriented electrical steel sheet by pickling, cold rolling, annealing, and coating.
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| CN2010102989655A CN102443734B (en) | 2010-09-30 | 2010-09-30 | Non-oriented electrical steel plate without corrugated defect and its manufacturing method |
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| PCT/CN2011/072766 WO2012041053A1 (en) | 2010-09-30 | 2011-04-14 | Non-oriented electric steel plate without corrugated fault and production method thereof |
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| JP (1) | JP2013540900A (en) |
| KR (1) | KR20130049822A (en) |
| CN (1) | CN102443734B (en) |
| MX (1) | MX357357B (en) |
| RU (1) | RU2550440C2 (en) |
| WO (1) | WO2012041053A1 (en) |
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| JP5942712B2 (en) * | 2012-09-06 | 2016-06-29 | 新日鐵住金株式会社 | Scum weir, thin slab manufacturing method, thin slab manufacturing equipment |
| CN102925795A (en) * | 2012-10-23 | 2013-02-13 | 鞍钢股份有限公司 | Production method for controlling transverse and longitudinal electromagnetic properties of low and medium grade products of non-oriented electrical steel |
| CN104073714A (en) * | 2013-03-28 | 2014-10-01 | 宝山钢铁股份有限公司 | Good-surface high magnetic strength low iron loss orientation-free electrical steel plate and preparation method thereof |
| CN104164544A (en) * | 2013-05-17 | 2014-11-26 | 宝山钢铁股份有限公司 | Method for manufacturing non-oriented electrical steel plate without line-shaped projection defects |
| CN104726763B (en) * | 2013-12-23 | 2017-04-12 | 鞍钢股份有限公司 | Hot rolling method of electrical steel |
| CN104073715B (en) * | 2014-06-19 | 2016-04-20 | 马钢(集团)控股有限公司 | A kind of manufacture method of high-magnetic strength non-oriented electrical steel |
| CN104342604B (en) * | 2014-11-10 | 2016-11-30 | 五行科技股份有限公司 | A kind of high intensity band manufacture method |
| CN104789862A (en) * | 2015-03-20 | 2015-07-22 | 宝山钢铁股份有限公司 | High-magnetic-induction low-iron-loss non-oriented electrical steel plate with good surface state and manufacturing method thereof |
| KR101901313B1 (en) | 2016-12-19 | 2018-09-21 | 주식회사 포스코 | Non-oriented electrical steel sheet and method for manufacturing the same |
| CN111719078B (en) * | 2019-03-19 | 2021-06-15 | 江苏集萃冶金技术研究院有限公司 | Production method of non-oriented silicon steel for eliminating corrugated defects |
| CN109825775B (en) * | 2019-04-04 | 2020-03-27 | 中山市中圣金属板带科技有限公司 | Cold-rolled non-oriented electrical steel 35WD1900 and production method thereof |
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| JP7047987B2 (en) * | 2020-02-20 | 2022-04-05 | 日本製鉄株式会社 | Hot-rolled steel sheet for non-oriented electrical steel sheet |
| CN111560554A (en) * | 2020-05-06 | 2020-08-21 | 包头钢铁（集团）有限责任公司 | Preparation method of rare earth non-oriented silicon steel |
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| CN115198203B (en) * | 2021-04-09 | 2024-02-13 | 宝山钢铁股份有限公司 | Non-oriented electrical steel plate free of normalizing intermediate annealing and manufacturing method thereof |
| CN115704073B (en) * | 2021-08-09 | 2024-01-09 | 宝山钢铁股份有限公司 | Non-oriented electrical steel plate with good surface state and manufacturing method thereof |
| CN114369761B (en) * | 2022-01-07 | 2022-11-25 | 山西太钢不锈钢股份有限公司 | Thin non-oriented silicon steel and preparation method thereof |
| CN114393185B (en) * | 2022-01-27 | 2023-08-15 | 马鞍山钢铁股份有限公司 | Method for improving equiaxial crystal rate of non-oriented electrical steel casting blank at high continuous casting speed |
| CN116117096B (en) * | 2023-01-04 | 2023-07-18 | 安庆新普电气设备有限公司 | High equiaxial crystal rate non-oriented electrical steel continuous casting billet and preparation method thereof |
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2010
- 2010-09-30 CN CN2010102989655A patent/CN102443734B/en active Active
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2011
- 2011-04-14 US US13/823,311 patent/US20130224064A1/en not_active Abandoned
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- 2011-04-14 KR KR1020137008046A patent/KR20130049822A/en active Search and Examination
- 2011-04-14 JP JP2013530533A patent/JP2013540900A/en active Pending
- 2011-04-14 EP EP11827949.6A patent/EP2623626B1/en active Active
- 2011-04-14 RU RU2013114859/02A patent/RU2550440C2/en active
- 2011-04-14 WO PCT/CN2011/072766 patent/WO2012041053A1/en active Application Filing
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