JPS6316445B2 - - Google Patents
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- Publication number
- JPS6316445B2 JPS6316445B2 JP60073303A JP7330385A JPS6316445B2 JP S6316445 B2 JPS6316445 B2 JP S6316445B2 JP 60073303 A JP60073303 A JP 60073303A JP 7330385 A JP7330385 A JP 7330385A JP S6316445 B2 JPS6316445 B2 JP S6316445B2
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- Prior art keywords
- oriented electrical
- rolled
- electrical steel
- temperature
- hot
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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- Manufacturing Of Steel Electrode Plates (AREA)
Description
（産業上の利用分野）
本発明は、磁気特性の優れた無方向性電磁鋼板
の製造方法に関するものであり、JIS規格で表さ
れる無方向性電磁鋼板最高級グレードS9〔鉄損
W15/50が2.90w／Kg以下（0.50mm板厚），同じく
2.40w／Kg以下（0.35mm板厚）〕よりもさらに優れ
たS8相当グレード以上の高級無方向性電磁鋼板
の製造方法に関するものである。
無方向性電磁鋼板の高級グレードは、一般に大
型回転機の鉄心材料等に広く使用されており、前
述のS9グレード等が現在用いられている。しか
し、最近は、大型回転機のコスト低減および高効
率化を図るため、鉄心材料として、S9グレード
よりもさらに低い鉄損値を有する高級無方向性電
磁鋼板の開発が強く要求されている。
（従来の技術）
一般に無方向性電磁鋼板の仕上焼鈍工程は、冷
間圧延後の（正常粒）再結晶により、結晶粒成長
の促進および結晶方位の改善を行わしめるもので
あり、鉄損値の低減に重要な役割を果たす工程で
ある。このため、従来からも、無方向性電磁鋼板
の高級グレードの製造に際しては、仕上焼鈍にい
くつかの工夫がなされてきた。例えば、特公昭59
−15966号公報に記載の方法によれば、仕上焼鈍
を前段850℃〜1000℃の温度範囲の低温均熱と後
段1000℃〜1100℃の温度範囲の高温均熱の二段焼
鈍とすることにより、冷間圧延後の（正常粒）再
結晶粒を整粒化し磁気特性の改善を図つている。
（発明が解決しようとする問題点）
無方向性電磁鋼板の磁気特性は、圧延方向（以
後Ｌ方向と記述する）と、板面内で圧延方向に垂
直な方向（以後Ｃ方向と記述する）との試料の合
計によつて測定されるが、一般にＣ方向の磁性が
Ｌ方向の磁性に対して劣つている。無方向性電磁
鋼板の最高級グレードの製造に関しては、このＬ
方向とＣ方向との磁気特性の差、すなわち磁気異
方性に着目し、この磁気異方性の改善により、磁
気特性の向上を図つた技術はない。
そこで、本発明者らは、磁気異方性、すなわ
ち、鉄損W15/50において（Ｃ−Ｌ／Ｃ＋Ｌ×100）％が1
0
％以下と小さくすることが、鋼板全体としての低
鉄損化につながるとの観点から多くの実験を積み
重ね、本発明を完成させた。
（問題点を解決するための手段）
すなわち本発明は、重量％で、Ｃ≦0.005％、
Si2.5〜4.0％、Al≦1.5％、残部Feおよび不可避
的不純物からなる無方向性電磁鋼板用スラブを、
熱間圧延後、熱延板焼鈍し、１回の冷間圧延によ
り或は中間焼鈍をはさむ２回以上の冷間圧延によ
り、最終板厚とした後、仕上焼鈍を行なう無方向
性電磁鋼板の製造方法において、仕上焼鈍を、前
段で鋼板を950℃〜1100℃の温度域に５秒〜１分
間均熱した後、後段で800〜950℃の温度域に10秒
〜２分間保定後冷却することにより磁気異方性を
小さくすることを特徴とする磁気特性の優れた無
方向性電磁鋼板の製造方法である。
また、本発明は、仕上焼鈍における前段均熱の
前にさらに、800〜950℃の温度域で10秒〜２分間
保定を行う場合を含む。また、本発明は前段均熱
後、該均熱温度から700℃までの冷却速度が100
℃／分以下である徐冷却を行う場合も含む。さら
に、本発明は、Ｃ≦0.005％、Si2.5〜4.0％、Al≦
1.5％を含み、不可避的不純物としてのＳ，Ｎ，
Ｏの含有量がそれぞれ0.0020％以下である無方向
性電磁鋼板用スラブを用いる場合を含む。
本発明を第１図に基いて詳細に説明する。
第１図は、Ｃ：0.0027％，Si：3.02％，Al：
0.94％，Ｓ：0.0009％，Ｎ：0.0012％，Ｏ：
0.0016％を含む無方向性電磁鋼板スラブを、加熱
し熱間圧延後、1.8mm厚の熱延板とした後、980℃
で２分間、熱延板焼鈍を行い、0.35mmの製品厚み
まで冷間圧延し、No.１〜４の各仕上焼鈍条件を旋
した場合の鉄損値W15/50と、Ｌ方向とＣ方向の鉄
損値の比（以後Ｌ，Ｃ比と記述する）を示したも
のである。すなわち、第１図から明らかなよう
に、仕上焼鈍において、通常の均熱焼鈍の後段
に、低温保定（No.３に対応）もしくは徐冷却（No.
４に対応）を実施することにより、著しく鉄損値
のＬ，Ｃ比が改善され、低鉄損化が達成できるこ
とを発見した。これは、後段の低温保定もしくは
徐冷却により、再結晶，結晶粒成長後の結晶粒内
が清浄化されること、および、約800℃以上で導
入され、常温にまで持ち越される冷却歪が減少す
ることによると考えられる。この効果は、鋼板の
Ｓ，Ｎ，Ｏ等の不純物元素が少ない高純鋼を用い
ることにより、さらに促進されることも併せて見
出した。
次に、本発明の構成要件の限定理由について述
べる。
まず、スラブの化学成分において、Ｃは磁気特
性を劣化させる元素で、0.005％を超えると、磁
気時効が生じ、磁気特性が著しく劣化するので、
0.005％以下とする。
Siは、鋼の固有抵抗を高めて鉄損を向上させる
元素で、2.5％未満では効果が少ない。しかし、
4.0％を超えると、鋼が脆化し冷延性を劣化させ
る。
Alは、Siと同様に、鋼の固有抵抗を高めて鉄
損を向上させると共に、鋼の脱酸のために添加す
る元素であるが、1.5％を超えると鋼が脆化する。
さらに、Ｓ，Ｎ，Ｏは、含有量が多くなると不
純物を生成し、磁気特性を劣化させる元素である
ので、それぞれ20ppm以下とすることが好まし
い。
（作用）
次に、本発明の特徴とする化学成分を有する無
方向性電磁鋼板用スラブは、転炉で溶製され、連
続鋳造あるいは造塊―分塊圧延により製造され
る。鋼スラブは公知の方法で加熱され熱間圧延さ
れる。熱間圧延後は、熱延板焼鈍の後、一回の冷
間圧延により、最終板厚にするか、あるいは、中
間に焼鈍をはさむ二回以上の冷間圧延により最終
板厚にする。
仕上焼鈍は、前段950℃〜1100℃の温度範囲で
均熱した後、後段800℃〜950℃の温度範囲で保定
する。前段均熱が950℃未満では、再結晶後の結
晶粒が小さく鉄損が劣化する。また、1100℃超で
は、鋼板表面に酸化皮膜が生成し、著しく磁気特
性が劣化する。
さらに、前段均熱時間は、５秒未満では、再結
晶後の結晶粒成長が悪く鉄損が劣化する。また、
１分を超えて保定してもその効果はほとんどな
い。
後段保定が950℃超および800℃未満では、鉄損
値のＬ，Ｃ比が改善されない。
さらに、後段保定時間は、10秒未満および２分
を超える場合には効果が少い。
上記の後段保定の効果は、前段均熱後の冷却
が、700℃までの冷却速度が100℃／分以下である
徐冷却によつて置き代えることができる。700℃
までの冷却速度が100℃／分超では、効果が小さ
い。また、700℃未満の冷却速度は効果に影響を
与えない。
また、前段均熱の前に、さらに、800℃〜950℃
の温度範囲で保定を行うと、均一な再結晶が生
じ、仕上焼鈍後の結晶粒が整粒となり、鉄損が改
善される。800C未満では均一な再結晶が生じ難
く、鉄損が改善されない。また、950℃超では、
結晶粒径および集合組織に変化をきたし磁性が劣
化する。
さらに、前段均熱前の保定時間は、10秒未満で
は、均一な再結晶が生じ難く、鉄損が改善されな
い。また、２分を超えて保定してもその効果はほ
とんどない。
以上述べた本発明を実施することにより、著し
く鉄損値のＬ，Ｃ比が改善され、低鉄損化が達成
できるため、S8相当グレード以上、特にS6，S5
相当グレードに対応する従来にない最高級無方向
性電磁鋼板の製造が可能である。
（実施例）
次に、本発明の実施例について述べる。
実施例 １
Ｃ：0.0028％，Si：3.00％，Al：1.00％，Ｓ：
0.0006％，Ｎ：0.0010％，Ｏ：0.0014％を含む無
方向性電磁鋼板用スラブを、加熱し熱間圧延後
1.8mm厚の熱延板とした後、熱延板焼鈍を950℃で
２分間行い、0.35mmの製品厚みまで冷間圧延し
た。その後、第１表に示す条件で仕上焼鈍を行
い、磁性測定を行つた。その結果を併せて第１表
に示す。
(Industrial Application Field) The present invention relates to a method for manufacturing a non-oriented electrical steel sheet with excellent magnetic properties, and the present invention relates to a method for manufacturing a non-oriented electrical steel sheet with excellent magnetic properties.
W 15/50 is 2.90w/Kg or less (0.50mm plate thickness), same
2.40w/Kg or less (0.35mm plate thickness)] The present invention relates to a method for producing a high-grade non-oriented electrical steel sheet of S8 equivalent grade or higher, which is even better than 2.40w/Kg or less (0.35mm plate thickness). High grade non-oriented electrical steel sheets are generally widely used as iron core materials for large rotating machines, and the above-mentioned S9 grade is currently in use. However, recently, in order to reduce the cost and improve the efficiency of large rotating machines, there has been a strong demand for the development of high-grade non-oriented electrical steel sheets that have an even lower core loss value than S9 grade as core materials. (Prior art) In general, the finish annealing process for non-oriented electrical steel sheets promotes grain growth and improves crystal orientation by recrystallizing (normal grains) after cold rolling, which improves iron loss value. This is a process that plays an important role in reducing For this reason, several improvements have been made to final annealing in the production of high-grade non-oriented electrical steel sheets. For example, Tokuko Sho 59
According to the method described in Publication No. 15966, the final annealing is performed in two stages: a low-temperature soaking in the temperature range of 850°C to 1000°C in the first stage and a high-temperature soaking in the temperature range of 1000°C to 1100°C in the second stage. , the recrystallized grains (normal grains) after cold rolling are sized to improve magnetic properties. (Problems to be Solved by the Invention) The magnetic properties of a non-oriented electrical steel sheet are in the rolling direction (hereinafter referred to as the L direction) and in the direction perpendicular to the rolling direction within the plate surface (hereinafter referred to as the C direction). The magnetism in the C direction is generally inferior to the magnetism in the L direction. Regarding the production of the highest grade of non-oriented electrical steel sheets, this L
There is no technique that focuses on the difference in magnetic properties between the C direction and the C direction, that is, the magnetic anisotropy, and attempts to improve the magnetic properties by improving the magnetic anisotropy. Therefore, the present inventors have determined that (CL/C+L×100)% is 1 in magnetic anisotropy, that is, iron loss W 15/50 .
From the viewpoint that reducing the iron loss to 0% or less leads to lower core loss of the steel plate as a whole, the present invention was completed after conducting many experiments. (Means for solving the problems) That is, the present invention provides C≦0.005% by weight,
A slab for non-oriented electrical steel sheets consisting of 2.5 to 4.0% Si, Al≦1.5%, the balance Fe and unavoidable impurities,
A non-oriented electrical steel sheet that is hot-rolled, then annealed, and then made to the final thickness by one cold rolling or two or more cold rollings with intermediate annealing, and then finish annealed. In the manufacturing method, the final annealing is performed by soaking the steel plate at a temperature range of 950°C to 1100°C for 5 seconds to 1 minute in the first stage, and then cooling it at a temperature range of 800 to 950°C for 10 seconds to 2 minutes in the latter stage. This is a method for producing a non-oriented electrical steel sheet with excellent magnetic properties, which is characterized by reducing magnetic anisotropy. Further, the present invention includes a case where holding is further performed in a temperature range of 800 to 950°C for 10 seconds to 2 minutes before the pre-soaking in the final annealing. In addition, the present invention has a cooling rate of 100℃ from the soaking temperature to 700℃ after the preheating stage.
This also includes cases where slow cooling is performed at a rate of ℃/min or less. Furthermore, the present invention provides C≦0.005%, Si2.5-4.0%, Al≦
Contains 1.5%, S, N, as unavoidable impurities
This includes cases in which slabs for non-oriented electrical steel sheets each having an O content of 0.0020% or less are used. The present invention will be explained in detail based on FIG. Figure 1 shows C: 0.0027%, Si: 3.02%, Al:
0.94%, S: 0.0009%, N: 0.0012%, O:
A non-oriented electrical steel plate slab containing 0.0016% was heated and hot-rolled to form a 1.8mm thick hot-rolled plate, and then heated to 980℃.
The iron loss value W 15/50 , L direction and C It shows the ratio of iron loss values in the directions (hereinafter referred to as L, C ratio). That is, as is clear from Fig. 1, in the final annealing, low temperature holding (corresponding to No. 3) or slow cooling (corresponding to No. 3) or slow cooling (corresponding to No. 3) is performed after normal soaking annealing.
4), it was discovered that the L and C ratio of the iron loss value was significantly improved and a reduction in iron loss could be achieved. This is because the interior of the crystal grains after recrystallization and grain growth is cleaned by holding the temperature at a later stage or slow cooling, and the cooling strain introduced at about 800℃ or higher and carried over to room temperature is reduced. This is thought to be possible. It has also been found that this effect is further promoted by using high-purity steel containing fewer impurity elements such as S, N, and O in the steel plate. Next, reasons for limiting the constituent elements of the present invention will be described. First, in the chemical composition of the slab, C is an element that deteriorates magnetic properties, and if it exceeds 0.005%, magnetic aging will occur and the magnetic properties will deteriorate significantly.
0.005% or less. Si is an element that increases the specific resistance of steel and improves iron loss, and if it is less than 2.5%, it has little effect. but,
If it exceeds 4.0%, the steel becomes brittle and cold rollability deteriorates. Al, like Si, is an element added to increase the specific resistance of steel and improve core loss, as well as to deoxidize the steel, but if it exceeds 1.5%, the steel becomes brittle. Furthermore, since S, N, and O are elements that generate impurities and deteriorate magnetic properties when their contents increase, it is preferable that each of them be 20 ppm or less. (Function) Next, a slab for a non-oriented electrical steel sheet having the chemical composition characteristic of the present invention is melted in a converter and manufactured by continuous casting or ingot-blowing rolling. The steel slab is heated and hot rolled in a known manner. After hot rolling, the hot rolled sheet is annealed and then cold rolled once to achieve the final thickness, or cold rolled two or more times with annealing in between to achieve the final thickness. For final annealing, after soaking in the temperature range of 950°C to 1100°C in the first stage, the temperature is maintained in the temperature range of 800°C to 950°C in the second stage. If the pre-stage soaking is less than 950°C, the crystal grains after recrystallization will be small and the iron loss will deteriorate. Furthermore, at temperatures exceeding 1100°C, an oxide film forms on the surface of the steel sheet, significantly degrading the magnetic properties. Furthermore, if the pre-soaking time is less than 5 seconds, grain growth after recrystallization will be poor and iron loss will deteriorate. Also,
Even if it is held for more than 1 minute, there is almost no effect. When the latter stage holding temperature is higher than 950°C and lower than 800°C, the L and C ratio of the iron loss value is not improved. Further, the second stage retention time is less effective when it is less than 10 seconds or more than 2 minutes. The effect of the above-mentioned second-stage holding can be replaced by cooling after the first-stage soaking by gradual cooling in which the cooling rate up to 700°C is 100°C/min or less. 700℃
If the cooling rate exceeds 100°C/min, the effect will be small. Also, the cooling rate below 700℃ has no effect on the effect. In addition, before soaking in the first stage, further heat to 800℃~950℃
When the temperature is maintained in the temperature range of , uniform recrystallization occurs, the crystal grains after final annealing become regular, and iron loss is improved. If the temperature is less than 800C, uniform recrystallization is difficult to occur and iron loss is not improved. In addition, at temperatures above 950℃,
This causes changes in crystal grain size and texture, resulting in deterioration of magnetism. Furthermore, if the holding time before the first stage soaking is less than 10 seconds, uniform recrystallization is difficult to occur and iron loss is not improved. Moreover, even if it is held for more than 2 minutes, there is almost no effect. By implementing the present invention described above, the L and C ratio of iron loss values is significantly improved and low iron loss can be achieved.
It is possible to manufacture the highest grade non-oriented electrical steel sheet that corresponds to a comparable grade. (Example) Next, an example of the present invention will be described. Example 1 C: 0.0028%, Si: 3.00%, Al: 1.00%, S:
After heating and hot rolling a slab for non-oriented electrical steel sheet containing 0.0006%, N: 0.0010%, O: 0.0014%
After forming a hot-rolled sheet with a thickness of 1.8 mm, the hot-rolled sheet was annealed at 950°C for 2 minutes and cold-rolled to a product thickness of 0.35 mm. Thereafter, final annealing was performed under the conditions shown in Table 1, and magnetic properties were measured. The results are also shown in Table 1.
【表】
No.１〜No.４は比較材で、本発明に比べ、仕上焼
鈍に後段保定がない場合、前段均熱前の保定はあ
るが後段保定がない場合、後段保定温度が低い場
合、そして、前段均熱温度が高い場合にそれぞれ
相当する。No.５，６は本発明材である。比較材で
は、S6相当（W15/501.8w／Kg）は得られない
が、本発明材では、S6相当品が得られることが
明らかである。
実施例 ２
Ｃ：0.0025％，Si：3.24％，Al：0.66％，Ｓ：
0.0007％，Ｎ：0.0012％，Ｏ：0.0015％を含む無
方向性電磁鋼板用スラブを、加熱し熱間圧延後
1.8mm厚の熱延板とした後、950℃で２分間、熱延
板焼鈍を行い、0.50mmの製品厚みまで冷延した。
その後、第２表に示す条件で仕上焼鈍を行い、磁
性測定を行つた。その結果を併せて第２表に示
す。[Table] No. 1 to No. 4 are comparative materials, and compared to the present invention, there is no post-temperature retention in finish annealing, there is retention before soaking in the pre-stage but there is no post-temperature retention, and cases where the post-temperature retention is lower. , and correspond to the case where the pre-stage soaking temperature is high, respectively. Nos. 5 and 6 are materials of the present invention. It is clear that the comparative material does not provide a product equivalent to S6 (W 15/50 1.8w/Kg), but the material of the present invention provides a product equivalent to S6. Example 2 C: 0.0025%, Si: 3.24%, Al: 0.66%, S:
After heating and hot rolling a slab for non-oriented electrical steel sheet containing 0.0007%, N: 0.0012%, O: 0.0015%
After forming a hot-rolled sheet with a thickness of 1.8 mm, the hot-rolled sheet was annealed at 950°C for 2 minutes and cold-rolled to a product thickness of 0.50 mm.
Thereafter, final annealing was performed under the conditions shown in Table 2, and magnetic properties were measured. The results are also shown in Table 2.
【表】
No.１〜No.４は比較材で、本発明に比べ、仕上焼
鈍に後段保定がない場合、前段均熱前の保定はあ
るが後段保定がない場合、後段保定温度が低い場
合、そして、前段均熱温度が高い場合にそれぞれ
相当する。No.５〜７は本発明材である。比較材で
はS5相当（W15/50≦2.10w／Kg）を得るのは困難
であるが、本発明材では、S5相当品を得ること
ができる。
実施例 ３
Ｃ：0.0027％，Si：3.02％，Al：0.97％，Ｓ：
0.0024％，Ｎ：0.0026％，Ｏ：0.0022％を含む無
方向性電磁鋼板用スラブを、加熱し熱間圧延後、
2.0mm厚の熱延板とした後、980℃で２分間、熱延
板焼鈍を行い、0.50mmの製品厚みまで冷延した。
その後、第３表に示す条件で仕上焼鈍を行い、磁
性測定を行つた。その結果を併せて第３表に示
す。本発明材No.２〜No.５では、比較材No.１に比べ
て、著しく鉄損値のＬ，Ｃが改善され、低鉄損化
が達成できることが明らかである。[Table] No. 1 to No. 4 are comparative materials, and compared to the present invention, there is no post-temperature retention in finish annealing, there is retention before soaking in the pre-stage but there is no post-temperature retention, and cases where the post-temperature retention is lower. , and correspond to the case where the pre-stage soaking temperature is high, respectively. Nos. 5 to 7 are materials of the present invention. Although it is difficult to obtain a product equivalent to S5 (W 15/50 ≦2.10w/Kg) with the comparative material, it is possible to obtain a product equivalent to S5 with the material of the present invention. Example 3 C: 0.0027%, Si: 3.02%, Al: 0.97%, S:
After heating and hot rolling a slab for non-oriented electrical steel sheet containing 0.0024%, N: 0.0026%, O: 0.0022%,
After forming a hot-rolled sheet with a thickness of 2.0 mm, the hot-rolled sheet was annealed at 980°C for 2 minutes and cold-rolled to a product thickness of 0.50 mm.
Thereafter, final annealing was performed under the conditions shown in Table 3, and magnetism was measured. The results are also shown in Table 3. It is clear that in the present invention materials No. 2 to No. 5, the iron loss values L and C are significantly improved compared to the comparative material No. 1, and a reduction in iron loss can be achieved.
第１図は仕上焼鈍条件と鉄損値W15/50および鉄
損値のＬ，Ｃ比との関係を示す図である。
FIG. 1 is a diagram showing the relationship between the final annealing conditions, the iron loss value W 15/50 , and the L and C ratio of the iron loss value.
Claims (1)
1.5％、残部Feおよび不可避的不純物からなる無
方向性電磁鋼板用スラブを、熱間圧延後、熱延板
焼鈍し、１回の冷間圧延により或は中間焼鈍をは
さむ２回以上の冷間圧延により最終板厚とした
後、仕上焼鈍を行なう無方向性電磁鋼板の製造方
法において、仕上焼鈍を、前段で鋼板を950〜
1100℃の温度域に５秒〜１分間均熱した後、後段
で800〜950℃の温度域に10秒〜２分間保定後冷却
することにより磁気異方性を小さくすることを特
徴とする磁気特性の優れた無方向性電磁鋼板の製
造方法。 ２ 重量％で、Ｃ≦0.005％、Si2.5〜4.0％、Al≦
1.5％、残部Feおよび不可避的不純物からなる無
方向性電磁鋼板用スラブを、熱間圧延後、熱延板
焼鈍し、１回の冷間圧延により或は中間焼鈍をは
さむ２回以上の冷間圧延により最終板厚とした
後、仕上焼鈍を行なう無方向性電磁鋼板の製造方
法において、仕上焼鈍を、鋼板を800〜950℃の温
度域に10秒〜２分間保定した後、前段で950〜
1100℃の温度域に５秒〜１分間均熱した後、後段
で800〜950℃の温度域に10秒〜２分間保定後冷却
する温度・時間関係とすることにより磁気異方性
を小さくすることを特徴とする磁気特性の優れた
無方向性電磁鋼板の製造方法。 ３ 重量％で、Ｃ≦0.005％、Si2.5〜4.0％、Al≦
1.5％、残部Feおよび不可避的不純物からなる無
方向性電磁鋼板用スラブを、熱間圧延後、熱延板
焼鈍し、１回の冷間圧延により或は中間焼鈍をは
さむ２回以上の冷間圧延により最終板厚とした
後、仕上焼鈍を行なう無方向性電磁鋼板の製造方
法において、仕上焼鈍を、前段で鋼板を950〜
1100℃の温度域に５秒〜１分間均熱した後、該均
熱温度から700℃まで100℃／分以下の冷却速度で
冷却する温度・時間関係とすることにより磁気異
方性を小さくすることを特徴とする磁気特性の優
れた無方向性電磁鋼板の製造方法。 ４ 重量％で、Ｃ≦0.005％、Si2.5〜4.0％、Al≦
1.5％、残部Feおよび不可避的不純物からなる無
方向性電磁鋼板用スラブを、熱間圧延後、熱延板
焼鈍し、１回の冷間圧延により或は中間焼鈍をは
さむ２回以上の冷間圧延により最終板厚とした
後、仕上焼鈍を行なう無方向性電磁鋼板の製造方
法において、仕上焼鈍を、鋼板を800〜950℃の温
度域に10秒〜２分間保定した後、前段で950〜
1100℃の温度域に５秒〜１分間均熱した後、該均
熱温度から700℃まで100℃／分以下の冷却速度で
冷却する温度・時間関係とすることにより磁気異
方性を小さくすることを特徴とする磁気特性の優
れた無方向性電磁鋼板の製造方法。 ５ 不可避的不純物におけるＳ，Ｎ，Ｏの含有量
が、それぞれ0.0020％以下である特許請求の範囲
第１項乃至第４項の何れかに記載の方法。[Claims] 1% by weight, C≦0.005%, Si2.5-4.0%, Al≦
A slab for non-oriented electrical steel sheet consisting of 1.5% Fe and unavoidable impurities is hot-rolled, then hot-rolled and annealed, and then cold-rolled once or twice or more with intermediate annealing in between. In a method for producing non-oriented electrical steel sheets in which finish annealing is performed after rolling to the final thickness, the steel plate is heated to a temperature of 950 to
Magnetism characterized by reducing magnetic anisotropy by soaking in a temperature range of 1100°C for 5 seconds to 1 minute, then cooling in a subsequent stage at a temperature range of 800 to 950°C for 10 seconds to 2 minutes. A method for manufacturing non-oriented electrical steel sheets with excellent properties. 2 Weight%, C≦0.005%, Si2.5-4.0%, Al≦
A slab for non-oriented electrical steel sheet consisting of 1.5% Fe and unavoidable impurities is hot-rolled, then hot-rolled and annealed, and then cold-rolled once or twice or more with intermediate annealing in between. In a method for manufacturing non-oriented electrical steel sheets in which finish annealing is performed after rolling to the final thickness, the final annealing is performed by holding the steel plate in a temperature range of 800 to 950°C for 10 seconds to 2 minutes, and then heating it to 950°C in the previous step.
Magnetic anisotropy is reduced by using a temperature/time relationship in which the material is soaked in a temperature range of 1100°C for 5 seconds to 1 minute, then maintained in a temperature range of 800 to 950°C for 10 seconds to 2 minutes, and then cooled. A method for manufacturing a non-oriented electrical steel sheet with excellent magnetic properties. 3 In weight%, C≦0.005%, Si2.5-4.0%, Al≦
A slab for non-oriented electrical steel sheet consisting of 1.5% Fe and unavoidable impurities is hot-rolled, then hot-rolled and annealed, and then cold-rolled once or twice or more with intermediate annealing in between. In a method for producing non-oriented electrical steel sheets in which finish annealing is performed after rolling to the final thickness, the steel plate is heated to a temperature of 950 to
After soaking in a temperature range of 1100°C for 5 seconds to 1 minute, magnetic anisotropy is reduced by setting a temperature/time relationship in which the material is cooled from the soaking temperature to 700°C at a cooling rate of 100°C/min or less. A method for manufacturing a non-oriented electrical steel sheet with excellent magnetic properties. 4 In weight%, C≦0.005%, Si2.5-4.0%, Al≦
A slab for non-oriented electrical steel sheet consisting of 1.5% Fe and unavoidable impurities is hot-rolled, then hot-rolled and annealed, and then cold-rolled once or twice or more with intermediate annealing in between. In a method for manufacturing non-oriented electrical steel sheets in which finish annealing is performed after rolling to the final thickness, the final annealing is performed by holding the steel plate in a temperature range of 800 to 950°C for 10 seconds to 2 minutes, and then heating it to 950°C in the previous step.
After soaking in a temperature range of 1100°C for 5 seconds to 1 minute, magnetic anisotropy is reduced by setting a temperature/time relationship in which the material is cooled from the soaking temperature to 700°C at a cooling rate of 100°C/min or less. A method for manufacturing a non-oriented electrical steel sheet with excellent magnetic properties. 5. The method according to any one of claims 1 to 4, wherein the contents of S, N, and O in the inevitable impurities are each 0.0020% or less.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60073303A JPS61231120A (en) | 1985-04-06 | 1985-04-06 | Manufacture of nonoriented electrical steel sheet having superior magnetic characteristic |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60073303A JPS61231120A (en) | 1985-04-06 | 1985-04-06 | Manufacture of nonoriented electrical steel sheet having superior magnetic characteristic |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS61231120A JPS61231120A (en) | 1986-10-15 |
| JPS6316445B2 true JPS6316445B2 (en) | 1988-04-08 |
Family
ID=13514256
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP60073303A Granted JPS61231120A (en) | 1985-04-06 | 1985-04-06 | Manufacture of nonoriented electrical steel sheet having superior magnetic characteristic |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS61231120A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1997022723A1 (en) * | 1995-12-19 | 1997-06-26 | Pohang Iron & Steel Co., Ltd. | Process for producing nondirectional electrical steel sheet excellent in close adhesion of insulating film |
Families Citing this family (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1996000306A1 (en) * | 1994-06-24 | 1996-01-04 | Nippon Steel Corporation | Method of manufacturing non-oriented electromagnetic steel plate having high magnetic flux density and low iron loss |
| EP2602335B1 (en) | 2010-08-04 | 2020-03-18 | Nippon Steel Corporation | Manufacturing method of non-oriented electrical steel sheet |
| CN110612358B (en) | 2017-06-02 | 2021-10-01 | 日本制铁株式会社 | Non-oriented electrical steel sheet |
| JP6828816B2 (en) | 2017-06-02 | 2021-02-10 | 日本製鉄株式会社 | Non-oriented electrical steel sheet |
| JP6828814B2 (en) | 2017-06-02 | 2021-02-10 | 日本製鉄株式会社 | Non-oriented electrical steel sheet |
| KR102452923B1 (en) | 2018-03-26 | 2022-10-11 | 닛폰세이테츠 가부시키가이샤 | non-oriented electrical steel sheet |
Family Cites Families (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5296919A (en) * | 1976-02-10 | 1977-08-15 | Kawasaki Steel Co | Annealing of non anisotropic silicon steel sheets |
| JPS5622931A (en) * | 1979-08-01 | 1981-03-04 | Yokogawa Hokushin Electric Corp | Optical analyzer |
| JPS5823411A (en) * | 1981-08-05 | 1983-02-12 | Nippon Steel Corp | Nondirectional electromagnetic steel plate having superior magnetism and manufacture therefor |
| JPS58181822A (en) * | 1982-04-16 | 1983-10-24 | Kawasaki Steel Corp | Manufacture of non-oriented silicon steel sheet having low iron loss |
| JPS5915966A (en) * | 1982-07-19 | 1984-01-27 | Canon Inc | image display device |
| JPS5974223A (en) * | 1982-10-20 | 1984-04-26 | Kawasaki Steel Corp | Production of non-directional silicon steel sheet having excellent magnetic characteristic |
-
1985
- 1985-04-06 JP JP60073303A patent/JPS61231120A/en active Granted
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1997022723A1 (en) * | 1995-12-19 | 1997-06-26 | Pohang Iron & Steel Co., Ltd. | Process for producing nondirectional electrical steel sheet excellent in close adhesion of insulating film |
| CN1060815C (en) * | 1995-12-19 | 2001-01-17 | 浦项综合制铁株式会社 | Process for producing nondirectional electrical steel sheet excellent in close adhesion of insulating film |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS61231120A (en) | 1986-10-15 |
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