JPH07113129B2 - Method for manufacturing silicon steel sheet - Google Patents
Method for manufacturing silicon steel sheetInfo
- Publication number
- JPH07113129B2 JPH07113129B2 JP1515287A JP1515287A JPH07113129B2 JP H07113129 B2 JPH07113129 B2 JP H07113129B2 JP 1515287 A JP1515287 A JP 1515287A JP 1515287 A JP1515287 A JP 1515287A JP H07113129 B2 JPH07113129 B2 JP H07113129B2
- Authority
- JP
- Japan
- Prior art keywords
- rolling
- hot
- steel sheet
- silicon steel
- cold
- 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.)
- Expired - Fee Related
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1222—Hot rolling
Landscapes
- Engineering & Computer Science (AREA)
- Chemical & Material Sciences (AREA)
- Physics & Mathematics (AREA)
- Electromagnetism (AREA)
- Manufacturing & Machinery (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacturing Of Steel Electrode Plates (AREA)
Description
【発明の詳細な説明】 〔産業上の利用分野〕 本発明は、例えば回転機や発電機等の磁心に用いられる
軟磁気特性の優れた高けい素鋼板の製造方法に関する。Description: TECHNICAL FIELD The present invention relates to a method for producing a high silicon steel sheet having excellent soft magnetic properties, which is used for a magnetic core of a rotating machine, a generator, or the like.
けい素鋼板は優れた軟磁気特性を有するものとして、従
来から電力用の磁心や回転機用の材料として多量に使用
されているが、近年、省エネルギー、省資源の観点から
変圧器や回転機などの電気機器の効率化、小型化が強く
要請され、それに伴つてその鉄心用材料であるけい素鋼
板にもより優れた軟磁気特性および鉄損特性が要求され
つつある。Silicon steel sheets have been used in large amounts as magnetic cores for electric power and materials for rotating machines because of their excellent soft magnetic properties, but in recent years, transformers and rotating machines have been used from the viewpoint of energy saving and resource saving. There is a strong demand for efficiency and miniaturization of the electric equipment, and accordingly, the soft magnetic properties and core loss properties of the silicon steel sheet, which is the material for the iron core, are being demanded.
このけい素鋼板の軟磁気特性は、けい素の添加量ととも
に向上し、特に6.5wt%近傍で、最高の透磁率を示し、
さらに固有電気抵抗も高いことから、鉄損も小さくなる
ことが知られている。しかしながら、けい素含有量が4
%を超えると急激に加工性が劣化するために従来の圧延
方法による工業的規模での薄板製造は極めて困難とされ
ていた。The soft magnetic properties of this silicon steel sheet improve with the amount of silicon added, and show the highest magnetic permeability, especially near 6.5 wt%.
Furthermore, since the specific electric resistance is high, it is known that the iron loss is also small. However, the silicon content is 4
When the content exceeds%, the workability is rapidly deteriorated, and it has been considered extremely difficult to manufacture a thin plate on an industrial scale by the conventional rolling method.
この問題点を解決するため本発明者らは種々研究を重ね
た結果、上記の4%を超える高けい素含有鋼についても
適切な圧延条件を選ぶことによつて冷間加工性に優れた
高けい素熱延鋼板を連続的に製造出来ることを知見し、
特願昭60−128323号においてその基本的製造方法につい
て提示した。As a result of various studies conducted by the present inventors in order to solve this problem, as a result of selecting appropriate rolling conditions even for the above-mentioned high silicon-containing steel of more than 4%, high cold workability is achieved. Knowing that silicon hot rolled steel sheets can be manufactured continuously,
The basic manufacturing method was presented in Japanese Patent Application No. 60-128323.
すなわち、この方法は、インゴツトあるいは連続鋳造ス
ラブを分塊圧延または粗圧延する際、適切な圧延条件を
選ぶことによつて結晶数の微細化を達成し、それらを比
較的低温で連続仕上熱延し、熱延板板厚方向の平均結晶
粒界間隔をSi添加量に応じて調整することによつて優れ
た冷間圧延性を付与することに特徴を有するものであ
る。That is, this method achieves grain refinement by selecting appropriate rolling conditions when slab-rolling or rough-rolling an ingot or continuously cast slab, and continuously finishing hot rolling them at a relatively low temperature. However, it is characterized by imparting excellent cold rolling property by adjusting the average grain boundary spacing in the thickness direction of the hot-rolled sheet according to the amount of Si added.
しかしながら、その後さらに試験、研究を積重ねた結
果、以下の事実が判明した。すなわち、連続仕上熱延工
程において上記方法によつて板厚方向の結晶粒径をSi添
加量に応じた臨界値以下に調整するために、仕上熱延前
粒径から推定される必要累積圧下率に応じた歪を加えて
も、冷間加工性に優れた高けい素鋼板を安定的に製造出
来ない事例があるということである。However, as a result of further tests and studies, the following facts were found. That is, in order to adjust the grain size in the plate thickness direction to a critical value or less according to the amount of Si added by the above method in the continuous hot rolling process, the required cumulative rolling reduction estimated from the grain size before hot rolling That is, there is a case where a high silicon steel sheet excellent in cold workability cannot be stably manufactured even if strain corresponding to is added.
本発明者らは、上記問題点を解決すべくその後鋭意実
験、研究を重ねた結果、仕上熱延時に厳密なコントロー
ルをしなければ熱延板板厚方向の組織が不均一となり、
冷延性の劣化を招くことを新たに知見し、これを改善す
るため、上記高けい素鋼板製造法における仕上熱延方法
について、連続仕上熱延時に熱間潤滑剤を使用するこ
と、あるいはこれに加えて適切なロール径を有する熱間
圧延機を使用することによつて、板厚方向でより均一な
熱延板組織が得られ、冷間加工性に優れた高けい素熱延
鋼板を安定且つ効率的に製造し得るとの結論に至つたも
のである。The inventors of the present invention to solve the above problems, as a result of extensive studies and researches thereafter, the structure in the thickness direction of the hot-rolled sheet becomes non-uniform unless strict control is applied during finishing hot-rolling,
To newly discover that it causes deterioration of cold rolling property and improve it, for the finishing hot rolling method in the above-mentioned high silicon steel sheet manufacturing method, using a hot lubricant during continuous finishing hot rolling, or In addition, by using a hot rolling mill with an appropriate roll diameter, a more uniform hot-rolled sheet structure can be obtained in the sheet thickness direction, and stable high-silicon hot-rolled steel sheet with excellent cold workability can be obtained. And it came to the conclusion that it can manufacture efficiently.
すなわち、この発明はC:1wt%以下、Si:4.0〜7.0wt%、
Mn:0.5wt%以下、Al:2wt%以下、残部不可避不純物及び
鉄からなる合金を溶製後、造塊もしくは連続鋳造により
鋳造し、分塊圧延・粗圧延後もしくは粗圧延後仕上熱延
し、表面酸化膜を除去した後、冷間圧延及び焼鈍を行う
ことによりけい素鋼板を製造するに当り、仕上熱延時
に、熱間潤滑剤を用いて圧延することを基本的な特徴と
するものである。さらにまた仕上熱延時に、熱間潤滑剤
を用い、加えて装入板厚の20倍以上の直径を有するロー
ルを用いて圧延することを他の基本的な特徴とするもの
である。That is, the present invention is C: 1 wt% or less, Si: 4.0 ~ 7.0 wt%,
Mn: 0.5 wt% or less, Al: 2 wt% or less, the balance unavoidable impurities and iron alloys are melted and then cast by ingot casting or continuous casting, and then hot rolling after slabbing / rough rolling or after rough rolling. When manufacturing a silicon steel sheet by performing cold rolling and annealing after removing the surface oxide film, the basic characteristic is to use a hot lubricant during finish hot rolling. Is. Still another basic feature is that during the final hot rolling, rolling is performed using a hot lubricant and, in addition, rolling using a roll having a diameter 20 times or more the thickness of the charging plate.
以下本発明法を詳述する。The method of the present invention will be described in detail below.
まず、成分の限定理由を説明する。First, the reasons for limiting the components will be described.
Cは、鉄損を高める有害な成分であり、磁気時効の原因
となるので少ない方が望ましい。しかしながら、CはFe
−Si系平衡状態図のγループ拡大元素であるため、けい
素含有量によつて決まる一定量添加されると冷却途中に
α−γ変態点が現われるようになり、それを利用した熱
処理が可能となるため、ある程度Cを添加することが望
ましい場合がある。本発明では加工性の観点からCが1w
t%以下と限定する。C is a harmful component that increases iron loss and causes magnetic aging. However, C is Fe
Since it is an element that expands the γ loop in the -Si system equilibrium diagram, an α-γ transformation point will appear during cooling when a fixed amount determined by the silicon content is added, and heat treatment using it will be possible. Therefore, it may be desirable to add C to some extent. In the present invention, C is 1 w from the viewpoint of workability.
Limited to t% or less.
Siは、固有電気抵抗を高めて渦電流損を減らし、鉄損を
低下させるのに有効な元素である。本発明ではSi4.0wt
%以上を含有する高けい素鉄合金をその対象とし、これ
を下限とする。一方、Si含有量が7.0wt%を超えると製
造コストが上昇するほか、磁気特性、特に最大透磁率が
劣化するためこれを上限とする。以上の理由からSiの限
定範囲を4.0〜7.0wt%とする。Si is an element effective in increasing the specific electric resistance, reducing the eddy current loss, and reducing the iron loss. In the present invention, Si4.0wt
The target is a high silicon iron alloy containing at least%, and this is the lower limit. On the other hand, if the Si content exceeds 7.0 wt%, the manufacturing cost will increase and the magnetic properties, especially the maximum magnetic permeability will deteriorate, so this is the upper limit. For the above reasons, the limited range of Si is 4.0 to 7.0 wt%.
Mnは、Sによる熱間脆性を抑制するために必要である
が、0.5wt%を超えると固溶硬化により加工性が劣化す
るため、0.5wt%以下の範囲とする。Mn is necessary to suppress hot embrittlement due to S, but if it exceeds 0.5 wt%, the workability deteriorates due to solid solution hardening, so the content is made 0.5 wt% or less.
Alは、鋼の脱酸及び磁気特性を劣化させるNを固定する
のに有効に作用するほか、Siと同様、固有電気抵抗を高
めて、鉄損を低下させる上でも有用な元素である。しか
しながら、多量に添加すると冷間圧延性の劣化及びコス
トの上昇を招くため、その上限を2wt%とする。Al effectively acts to fix N, which deteriorates the deoxidation and magnetic properties of steel, and, like Si, is a useful element for increasing the specific electrical resistance and reducing the iron loss. However, if added in a large amount, the cold rolling property deteriorates and the cost increases, so the upper limit is made 2 wt%.
上記の如く成分調整した溶鋼は、造塊−分塊圧延法もし
くは連続鋳造法(連鋳−分塊圧延の場合もある)によつ
てスラブとし、このスラブを再結晶による組織の微細化
を図りながら粗熱延し、その後、本発明によつて所定の
板厚まで仕上熱延する。この仕上熱延に際し、本発明で
は熱間潤滑剤を使用する。ここで熱間潤滑剤を使用する
のは、仕上熱延前粒径に応じた未再結晶温度域での好ま
しくは1100〜500℃での強圧下熱延により生じ易い板厚
方向の組織の不均一を改善するためである。この本発明
方法によれば、板厚方向に均一に上記温度域での累積圧
下率に応じた歪を加えることが可能となるため優れた冷
間加工性を有する熱延板組織の形成が容易となり、得ら
れる熱延板の冷延性も極めて良好となる。The molten steel whose composition has been adjusted as described above is made into a slab by the ingot-bulk rolling method or the continuous casting method (in some cases, continuous casting-bulk rolling), and the slab is recrystallized to refine the structure. While performing rough hot rolling, then finish hot rolling to a predetermined plate thickness according to the present invention. In the present invention, a hot lubricant is used for this hot rolling. The hot lubricant is used here because of the non-reinforcing structure in the sheet thickness direction, which is likely to be caused by the hot rolling under high pressure rolling, preferably at 1100 to 500 ° C in the non-recrystallization temperature range according to the grain size before hot rolling. This is to improve uniformity. According to this method of the present invention, it is possible to uniformly apply strain according to the cumulative reduction in the temperature range in the plate thickness direction, so that it is easy to form a hot-rolled sheet structure having excellent cold workability. Therefore, the cold-rolling property of the obtained hot-rolled sheet also becomes extremely good.
熱間潤滑剤については、500〜1100℃の温度範囲におい
て10〜10000ポアズ程度の粘性特性が発揮されるもので
あれば、パラフイン系鉱油、ナフテン系鉱油、芳香族系
油、油脂、脂肪酸、合成エステル、アミン・アミド錯
体、メタ及びピロリン酸塩、ガラス質系などの有機質、
無機質を問わずその化学組成、形状、材質等の限定、ま
た原体、混合、希釈の限定は特に設けない。また圧延時
に塗布されるものでも事前でも良く、ロール、鋼材、冷
却水の使用、不使用により作用効果に差がない。For hot lubricants, paraffinic mineral oils, naphthenic mineral oils, aromatic oils, fats, fatty acids, synthetics, as long as viscosity characteristics of about 10 to 10000 Poise are exhibited in the temperature range of 500 to 1100 ° C. Organic substances such as esters, amine-amide complexes, meta and pyrophosphates, glassy systems,
No limitation is imposed on the chemical composition, the shape, the material, etc. of the inorganic material, and the limitation of the raw material, mixing, and dilution. Further, it may be applied at the time of rolling or may be applied in advance, and there is no difference in action and effect depending on the use or non-use of rolls, steel materials and cooling water.
また装入板厚(仕上熱延前板厚)の20倍以上の直径を有
するロールを用いて圧延すれば、上記の熱間潤滑剤によ
ると同様効率的均一化効果が期待される。装入板厚の20
倍未満の直径を有するロールを用いた仕上熱延では、板
厚方向の歪分布が不均一になるために熱延板板厚方向の
組織が不均一となり、冷間圧延性も劣化する。従つて、
かかる観点から第2発明においては熱間潤滑剤を使用
し、さらに装入板厚の20倍以上の直径を有するロールを
用いて仕上熱延するものとする。これにより冷延性の良
好な熱延板組織の制御がより効率的に行える。すなわ
ち、冷間圧延によつて高けい素鋼の薄板を製造するため
には、本発明法によつて仕上熱延し熱延板組織を板厚方
向に関して均一な組織とすれば極めて良好な冷延性を付
与することが可能となる。Further, if rolling is carried out using a roll having a diameter 20 times or more the thickness of the charged sheet (sheet thickness before hot rolling for finishing), the effect of efficient homogenization is expected as with the above hot lubricant. Charge plate thickness of 20
In finish hot rolling using a roll having a diameter less than twice, the strain distribution in the plate thickness direction becomes non-uniform, so that the structure in the plate thickness direction of the hot-rolled plate becomes non-uniform and the cold rolling property also deteriorates. Therefore,
From this point of view, in the second invention, the hot lubricant is used, and the finish hot rolling is performed using the roll having the diameter of 20 times or more the thickness of the charging plate. As a result, the control of the hot-rolled sheet structure having a good cold rolling property can be performed more efficiently. That is, in order to manufacture a thin sheet of high silicon steel by cold rolling, if a finish hot-rolling is performed by the method of the present invention and the hot-rolled sheet structure has a uniform structure in the plate thickness direction, a very good cold Ductility can be imparted.
実施例1. 第1表に示す化学成分からなる厚さ150mmの連続鋳造ス
ラブを1250℃で3時間加熱後、直ちに厚さ30mmまで粗圧
延し、その後、ロール径480mmの2段式熱間圧延機によ
つて、仕上熱間圧延する際、第2表に示すような4種類
の熱間潤滑剤を用いて6パスで熱延し2mm厚とした。こ
の時の仕上入側温度は1100℃、出側温度は850℃であつ
た。Example 1. A continuously cast slab having a thickness of 150 mm and consisting of the chemical components shown in Table 1 was heated at 1250 ° C. for 3 hours and immediately rough-rolled to a thickness of 30 mm, and then two-stage hot rolling with a roll diameter of 480 mm. Using a machine, during hot rolling for finishing, hot rolling was performed in 6 passes using 4 types of hot lubricants as shown in Table 2 to a thickness of 2 mm. At this time, the finishing inlet temperature was 1100 ° C and the outlet temperature was 850 ° C.
なお、比較例として熱間潤滑剤を使用せずに、上記パス
スケジユールと同様の熱延を行つた。As a comparative example, hot rolling was performed in the same manner as in the above pass schedule without using a hot lubricant.
得られた熱延板を酸洗してから0.35mmまで冷間圧延し、
その冷間圧延性(5点評価による冷間圧延性)を判定し
た。結果を第3表に示す。これによれば、いずれも熱間
潤滑剤を使用した場合には極めて優れた冷間圧延性を示
すことが明らかである。The obtained hot rolled sheet was pickled and then cold rolled to 0.35 mm,
The cold rolling property (cold rolling property by 5-point evaluation) was determined. The results are shown in Table 3. According to this, it is clear that when any of the hot lubricants is used, they exhibit extremely excellent cold rolling property.
実施例2. 第1表と同様の化学成分からなる厚さ150mmの分塊圧延
スラブを用いて、加熱後30mm厚まで粗圧延した後、それ
ぞれ300mm、480mm、600mm、820mmのロール径を有するロ
ールを用いて第2表のガラス質粉末を使用して、仕上熱
延し(仕上出側温度810℃)、2mm厚の熱延コイルとし
た。酸洗後、0.35mm厚まで冷間圧延し、その冷延性(実
施例1と同様)を評価した。結果を第1図に示す。これ
によれば、装入板厚(仕上熱延前板厚)の20倍以上のロ
ール径を用い、さらに熱間潤滑剤を用いた場合の冷間圧
延性は、無潤滑の場合と比較して、より優れた冷間加工
性を示すことがわかる。 Example 2. Using a slab of slab having the same chemical composition as in Table 1 and having a thickness of 150 mm, after heating, roughly rolling to a thickness of 30 mm, and then rolls having roll diameters of 300 mm, 480 mm, 600 mm, and 820 mm, respectively. Using the glassy powder shown in Table 2, a hot rolled finish coil (finishing outlet side temperature: 810 ° C.) was used to obtain a hot rolled coil having a thickness of 2 mm. After pickling, it was cold rolled to a thickness of 0.35 mm and its cold ductility (similar to Example 1) was evaluated. The results are shown in Fig. 1. According to this, the cold rolling property when using a roll diameter 20 times or more of the charging plate thickness (plate thickness before hot rolling) and using a hot lubricant is better than that without lubrication. It can be seen that it exhibits more excellent cold workability.
実施例3. Siを6.5wt%(目標値)含む鉄合金に、C,Al,Mn,Pを各々
添加し、且つFe,Si,C,Mn,P,Al以外の不純物元素総量を
0.05wt%以下としたインゴツトを作成した。これを均熱
炉に熱塊装入して1100〜1250℃で均熱し、60〜80%の圧
下率の分塊圧延を行つた。この圧延後、加熱炉に熱片装
入して1100〜1250℃に加熱し、60〜90%の圧下率で粗圧
延を行つて、厚さ30mmの板とした。そして板温が1100〜
900℃の時に仕上熱延を開始し、2mmの熱延板に仕上げ
た。この仕上熱延は、ロール径が300〜1800mmのロール
を用い、第2表中種類(1)のガラス質粉末を熱間潤滑
剤として使用して行い、また比較のため同様のロールを
用い熱間潤滑剤を使用しないで圧延を行つた。熱延板の
脱スケールを行つた後、75%の圧下率で冷間圧延を行
い、冷間圧延性を実施例(1)と同じ基準で評価した。
なお、冷間圧延は板温が20〜250℃の範囲で行つた。Example 3 C, Al, Mn, and P were added to an iron alloy containing Si at 6.5 wt% (target value), and the total amount of impurity elements other than Fe, Si, C, Mn, P, and Al was determined.
An ingot with 0.05 wt% or less was prepared. This was put into a soaking pit in a hot mass, soaked at 1100 to 1250 ℃, and slabbing with a rolling reduction of 60 to 80%. After this rolling, hot pieces were charged into a heating furnace, heated to 1100 to 1250 ° C., and roughly rolled at a rolling reduction of 60 to 90% to obtain a plate having a thickness of 30 mm. And the plate temperature is 1100 ~
Finishing hot rolling was started at 900 ° C, and a 2 mm hot rolled sheet was finished. This finishing hot rolling is performed by using a roll having a roll diameter of 300 to 1800 mm, using the glassy powder of type (1) in Table 2 as a hot lubricant, and using a similar roll for comparison. Rolling was carried out without using a lubricant. After descaling the hot-rolled sheet, cold rolling was performed at a reduction rate of 75%, and the cold rollability was evaluated according to the same criteria as in Example (1).
The cold rolling was performed at a plate temperature of 20 to 250 ° C.
第2図に冷間圧延性(第1図における5点評価による冷
間圧延性)が「評点5」となる(仕上熱延ロール径/板
厚)比を示す。これによれば、Al,C,Mn,Pの各含有量が
増すと良好な冷延性を得るに必要なロール径が増大する
傾向があるが、本発明に従い仕上圧延に熱間潤滑剤を用
い且つ(ロール径/板厚)比を20以上とすることにより
良好な冷間圧延性が得られることが判る。FIG. 2 shows a ratio (cold hot-rolling roll diameter / plate thickness) at which the cold rolling property (cold rolling property based on the 5-point evaluation in FIG. 1) becomes “rating 5”. According to this, as the content of each of Al, C, Mn, and P increases, the roll diameter necessary for obtaining good cold rolling tends to increase, but a hot lubricant is used for finish rolling according to the present invention. Further, it can be seen that good cold rolling property can be obtained by setting the ratio of (roll diameter / plate thickness) to 20 or more.
実施例4. 第4表の組成範囲の鉄−けい素合金を溶解した。そして
この際、Fe,Si,C,Mn,P,Alの各成分値を分析してその他
の不純物元素(主なものとしては、Cr,Ti,W,Mo,Co,Cu,
S,B,As)の総量を求め、その総量を変化させて不純物元
素総量の異なる種々のインゴツトを作つた。このインゴ
ツトを均熱炉に熱塊装入して1100〜1250℃で均熱し、60
〜80%の圧下率の分塊圧延を行つた。圧延後、加熱炉に
熱片装入して1100〜1250℃に加熱し、圧下率60〜90%の
粗圧延を行い、厚さ30mmの板厚とした。そして板温が11
00〜900℃の段階で仕上熱延を開始して2mmの熱延板とし
た。この仕上熱延は直径700mmのロールを用い、第2表
中種類(1)のガラス質粉末を熱間潤滑剤として使用し
て行い、また比較のため同様のロールを用い熱間潤滑剤
を使用しないで圧延を行つた。Example 4 An iron-silicon alloy having the composition range shown in Table 4 was melted. At this time, the component values of Fe, Si, C, Mn, P, and Al are analyzed to analyze other impurity elements (mainly, Cr, Ti, W, Mo, Co, Cu,
The total amount of (S, B, As) was obtained, and the total amount was varied to make various ingots with different total amounts of impurity elements. This ingot was charged into a soaking pit with hot mass and soaked at 1100 to 1250 ℃,
Slab rolling with a reduction of ~ 80% was performed. After the rolling, the heating piece was charged into a heating furnace and heated to 1100 to 1250 ° C., and rough rolling was performed at a reduction rate of 60 to 90% to obtain a plate thickness of 30 mm. And the plate temperature is 11
Finish hot rolling was started at the stage of 00 to 900 ° C to obtain a 2 mm hot rolled sheet. This finishing hot rolling was performed using a roll with a diameter of 700 mm, using the glassy powder of type (1) in Table 2 as the hot lubricant, and using a similar roll for comparison for comparison. Rolled without doing.
第3図は合金中の不純物元素総量と冷間加工性(5点評
価による冷間圧延性)との関係を示すもので、不純物元
素総量が増すと冷延性が若干劣化する傾向があるが、本
発明によつて熱間潤滑剤を用い且つ(ロール径/板厚)
比を20以上とすることにより良好な冷間加工性が得られ
ることが示されている。FIG. 3 shows the relationship between the total amount of impurity elements in the alloy and the cold workability (cold rollability based on a 5-point evaluation). The cold ductility tends to deteriorate slightly as the total amount of impurity elements increases, According to the present invention, a hot lubricant is used and (roll diameter / plate thickness)
It has been shown that by setting the ratio to 20 or more, good cold workability can be obtained.
〔発明の効果〕 以上述べたようにこの発明によれば、仕上熱延時の熱延
組織制御が容易となり飛躍的に冷間加工性に優れた高け
い素鋼板を安定且つ効率的に製造できる。 [Advantages of the Invention] As described above, according to the present invention, it is possible to easily control the hot rolling structure during finish hot rolling, and to stably and efficiently manufacture a high silicon steel sheet having dramatically excellent cold workability.
第1図は(ロール径/装入板厚)比と冷間圧延性の関係
を示すグラフである。第2図は仕上圧延に熱間潤滑剤を
使用した場合と使用しない場合について、合金中におけ
る添加元素別の濃度と冷間圧延性が良好となる(ロール
径/装入板厚)比との関係を示したものである。第3図
は仕上圧延に熱間潤滑剤を使用した場合と使用しない場
合について、合金中の不純物総量と冷間圧延性との関係
を示したものである。FIG. 1 is a graph showing the relationship between (roll diameter / charging plate thickness) ratio and cold rollability. Fig. 2 shows the relationship between the concentration of each additive element in the alloy and the cold rollability (roll diameter / charging plate thickness) ratio with and without the use of hot lubricant in finish rolling. It shows the relationship. FIG. 3 shows the relationship between the total amount of impurities in the alloy and the cold rollability with and without the use of a hot lubricant for finish rolling.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 稲垣 淳一 東京都千代田区丸の内1丁目1番2号 日 本鋼管株式会社内 (72)発明者 日裏 昭 東京都千代田区丸の内1丁目1番2号 日 本鋼管株式会社内 (72)発明者 二宮 弘憲 東京都千代田区丸の内1丁目1番2号 日 本鋼管株式会社内 ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Junichi Inagaki 1-2-2 Marunouchi, Chiyoda-ku, Tokyo Nihon Kokan Co., Ltd. Nihon Steel Tube Co., Ltd. (72) Inventor Hironori Ninomiya 1-2 1-2 Marunouchi, Chiyoda-ku, Tokyo Nihon Steel Tube Co., Ltd.
Claims (6)
%以下、Al:2wt%以下、残部鉄及び不可避不純物からな
る合金を溶製後、造塊もしくは連続鋳造により鋳造し、
分塊圧延・粗圧延後もしくは粗圧延後仕上熱延し、表面
酸化膜を除去した後、冷間圧延及び焼鈍を行うことによ
りけい素鋼板を製造するに際し、仕上熱延時に熱間潤滑
剤を用いることを特徴とするけい素鋼板の製造方法。1. C: 1 wt% or less, Si: 4.0-7.0 wt%, Mn: 0.5 wt
% Or less, Al: 2 wt% or less, the balance consisting of iron and unavoidable impurities, and then cast by ingot casting or continuous casting,
After slabbing / rough rolling or after rough rolling, hot rolling is performed to remove the surface oxide film, and then cold rolling and annealing are performed to produce a silicon steel sheet. A method for manufacturing a silicon steel sheet, which is characterized by being used.
いることを特徴とする特許請求の範囲(1)記載のけい
素鋼板の製造方法。2. A method for producing a silicon steel sheet according to claim 1, wherein the hot lubricant is used in a temperature range of 500 to 1100 ° C.
の粘性を有する熱間潤滑剤を用いることを特徴とする特
許請求の範囲(2)記載のけい素鋼板の製造方法。3. A method for producing a silicon steel sheet according to claim 2, wherein a hot lubricant having a viscosity of 10 to 10,000 poise in a temperature range of 500 to 1100 ° C. is used.
%以下、Al:2wt%以下、残部鉄及び不可避不純物からな
る合金を溶製後、造塊もしくは連続鋳造により鋳造し、
分塊圧延・粗圧延後もしくは粗圧延後仕上熱延し、表面
酸化膜を除去した後、冷間圧延及び焼鈍を行うことによ
りけい素鋼板を製造するに際し、仕上熱延時に、熱間潤
滑剤を用いると共に、装入板厚の20倍以上の直径を有す
るロールを用いて圧延することを特徴とするけい素鋼板
の製造方法。4. C: 1 wt% or less, Si: 4.0-7.0 wt%, Mn: 0.5 wt
% Or less, Al: 2 wt% or less, the balance consisting of iron and unavoidable impurities, and then cast by ingot casting or continuous casting,
After slabbing / rough rolling or after rough rolling, hot rolling is performed to remove the surface oxide film, and then cold rolling and annealing are performed to produce a silicon steel sheet. And a rolling method using a roll having a diameter 20 times or more the thickness of the charging plate, and a method for manufacturing a silicon steel sheet.
いることを特徴とする特許請求の範囲(4)記載のけい
素鋼板の製造方法。5. The method for producing a silicon steel sheet according to claim 4, wherein the hot lubricant is used in the temperature range of 500 to 1100 ° C.
の粘性を有する熱間潤滑剤を用いることを特徴とする特
許請求の範囲(5)記載のけい素鋼板の製造方法。6. The method for producing a silicon steel sheet according to claim 5, wherein a hot lubricant having a viscosity of 10 to 10000 poise in a temperature range of 500 to 1100 ° C. is used.
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP1817386 | 1986-01-31 | ||
JP61-18173 | 1986-01-31 |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS62278227A JPS62278227A (en) | 1987-12-03 |
JPH07113129B2 true JPH07113129B2 (en) | 1995-12-06 |
Family
ID=11964217
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP1515287A Expired - Fee Related JPH07113129B2 (en) | 1986-01-31 | 1987-01-27 | Method for manufacturing silicon steel sheet |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH07113129B2 (en) |
Families Citing this family (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH01225723A (en) * | 1988-03-04 | 1989-09-08 | Nkk Corp | Production of non-oriented silicon steel sheet having excellent magnetic characteristic |
JPH01225726A (en) * | 1988-03-07 | 1989-09-08 | Nkk Corp | Production of non-oriented flat rolled magnetic steel sheet |
BE1006599A6 (en) * | 1993-01-29 | 1994-10-25 | Centre Rech Metallurgique | Method of manufacturing a plate hot rolled steel having high magnetic properties. |
-
1987
- 1987-01-27 JP JP1515287A patent/JPH07113129B2/en not_active Expired - Fee Related
Also Published As
Publication number | Publication date |
---|---|
JPS62278227A (en) | 1987-12-03 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP2009185386A (en) | Method for producing non-grain-oriented electrical steel sheet | |
KR102244171B1 (en) | Non-oriented electrical steel sheet and manufacturing method thereof | |
WO2015107967A1 (en) | Non-directional electromagnetic steel sheet having excellent magnetic properties | |
KR910000010B1 (en) | Method of producing silicon fron sheet having excellent soft magnetic properties | |
KR20020035827A (en) | Method for producing non-grain oriented electric sheet steel | |
KR20210003908A (en) | Non-oriented electrical steel sheet and its manufacturing method | |
JPH10121213A (en) | Grain oriented silicon steel sheet excellent in iron loss characteristic in low magnetic field as compared with high magnetic field, and its production | |
JP2509018B2 (en) | Manufacturing method of non-oriented electrical steel sheet with high magnetic flux density and low iron loss | |
US5330586A (en) | Method of producing grain oriented silicon steel sheet having very excellent magnetic properties | |
JP2008156741A (en) | Method for manufacturing non-oriented electromagnetic steel sheet with high magnetic flux density | |
JP6146582B2 (en) | Method for producing non-oriented electrical steel sheet | |
JP2020056105A (en) | Method for manufacturing grain-oriented electrical steel sheet | |
JP3375998B2 (en) | Manufacturing method of non-oriented electrical steel sheet | |
JP2020033640A (en) | Production method of non-oriented electromagnetic steel sheet | |
JP4422220B2 (en) | Non-oriented electrical steel sheet with high magnetic flux density and low iron loss and method for producing the same | |
JPH07113129B2 (en) | Method for manufacturing silicon steel sheet | |
JP3483265B2 (en) | Method for producing non-oriented electrical steel sheet with high magnetic flux density and low iron loss | |
JPH07113128B2 (en) | Method for manufacturing silicon steel sheet | |
JPH09316535A (en) | Nonoriented silicon steel sheet excellent in magnetic property and its production | |
JPH0657332A (en) | Manufacture of non-oriented silicon steel sheet having high magnetic flux density and low iron loss | |
JP3294367B2 (en) | Non-oriented electrical steel sheet having high magnetic flux density and low iron loss and method of manufacturing the same | |
JP2000054084A (en) | Silicon-containing hot rolled sheet excellent in magnetic property, and its manufacture | |
JP4191806B2 (en) | Method for producing non-oriented electrical steel sheet | |
JP2870817B2 (en) | Manufacturing method of semi-process non-oriented electrical steel sheet with excellent magnetic properties | |
JPH03215627A (en) | Production of nonoriented silicon steel sheet |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
LAPS | Cancellation because of no payment of annual fees |