JPS62222025A - Manufacture of nonoriented electrical sheet superior in brittleness resistance and magnetic characteristic after stress relief annealing - Google Patents
Manufacture of nonoriented electrical sheet superior in brittleness resistance and magnetic characteristic after stress relief annealingInfo
- Publication number
- JPS62222025A JPS62222025A JP6303486A JP6303486A JPS62222025A JP S62222025 A JPS62222025 A JP S62222025A JP 6303486 A JP6303486 A JP 6303486A JP 6303486 A JP6303486 A JP 6303486A JP S62222025 A JPS62222025 A JP S62222025A
- Authority
- JP
- Japan
- Prior art keywords
- annealing
- rolling
- stress relief
- relief annealing
- less
- 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.)
- Granted
Links
- 238000000137 annealing Methods 0.000 title claims abstract description 40
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 13
- 238000005096 rolling process Methods 0.000 claims abstract description 18
- 238000000034 method Methods 0.000 claims abstract description 9
- 238000005097 cold rolling Methods 0.000 claims abstract description 8
- 238000004080 punching Methods 0.000 claims abstract description 6
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 5
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 3
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 17
- 229910000565 Non-oriented electrical steel Inorganic materials 0.000 claims description 14
- 229910052742 iron Inorganic materials 0.000 claims description 6
- 230000009467 reduction Effects 0.000 claims description 5
- 230000000717 retained effect Effects 0.000 claims description 5
- 229910000831 Steel Inorganic materials 0.000 abstract description 15
- 239000010959 steel Substances 0.000 abstract description 15
- 238000005098 hot rolling Methods 0.000 abstract description 7
- 230000008569 process Effects 0.000 abstract description 5
- 238000004804 winding Methods 0.000 abstract description 3
- 239000013078 crystal Substances 0.000 description 9
- 239000000463 material Substances 0.000 description 8
- 230000003647 oxidation Effects 0.000 description 8
- 238000007254 oxidation reaction Methods 0.000 description 8
- 229910000976 Electrical steel Inorganic materials 0.000 description 5
- 239000011162 core material Substances 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 244000299461 Theobroma cacao Species 0.000 description 3
- 235000009470 Theobroma cacao Nutrition 0.000 description 3
- 229910052717 sulfur Inorganic materials 0.000 description 3
- 239000002344 surface layer Substances 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000000465 moulding Methods 0.000 description 2
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 239000003245 coal Substances 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000004907 flux Effects 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 230000001590 oxidative effect Effects 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 230000035699 permeability Effects 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000010008 shearing Methods 0.000 description 1
- 238000004904 shortening Methods 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- 239000013589 supplement Substances 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
Landscapes
- Manufacturing Of Steel Electrode Plates (AREA)
Abstract
Description
【発明の詳細な説明】
(産業上の利用分野)
本発明はセミプロセス無方向性電磁鋼板の製造に係わり
、歪取焼鈍後の耐脆性と磁気特性のすぐれた無方向性電
磁鋼板の製造方法に関する。[Detailed Description of the Invention] (Industrial Application Field) The present invention relates to the production of semi-processed non-oriented electrical steel sheets, and a method for producing non-oriented electrical steel sheets with excellent brittle resistance and magnetic properties after stress relief annealing. Regarding.
(従来の技術)
無方向性電磁鋼板は、モーターや変圧器の鉄心などに使
用されるが、その製造法によりフルプロセス材とセミプ
ロセス材がある。フルプロセス材は、鋼板製造者側で1
回以上の冷延および焼鈍を施したもので、いわゆる最終
仕上焼鈍まで行なわれたものである。(Prior Art) Non-oriented electrical steel sheets are used for cores of motors and transformers, and are divided into full process materials and semi-process materials depending on the manufacturing method. For fully processed materials, the steel sheet manufacturer
It has been cold rolled and annealed more than once, up to so-called final finish annealing.
一万セミプロセス材は、1回以上の冷延及び必女により
焼鈍を鋼板製造者11111で行ない、鋼板製造者側1
1で、所定の形状に打抜きや剪呵那工後に、歪取焼鈍を
施し、所定の磁気特性を現出させるものである。10,000 semi-processed materials are cold-rolled and annealed one or more times by the steel plate manufacturer 11111, and the steel plate manufacturer side 1
1, after punching and shearing into a predetermined shape, strain relief annealing is performed to develop predetermined magnetic properties.
このセミプロセス材の打抜きや、切断加工による出が、
玉取焼鈍により除かれ、かつこの焼鈍で結晶粒の成長な
どがあることから、一般にフルプロセス材よυ鉄損が低
い。The punching and cutting process of this semi-processed material is
Since it is removed by Tamatori annealing and the growth of crystal grains occurs during this annealing, the iron loss is generally lower than that of full process materials.
セミプロセス無方向性電磁鋼板の製造に関しては従来か
ら各種提案されている。例えば特開昭51−215]1
3号公報では、鉄損が低く磁束密度もすぐれたものを製
造するように、最終冷延の圧下率を65〜70%と高め
て、歪取焼鈍を行っている。Various proposals have been made regarding the production of semi-processed non-oriented electrical steel sheets. For example, JP-A-51-215]1
In Publication No. 3, in order to produce a product with low core loss and excellent magnetic flux density, the final cold rolling reduction is increased to 65 to 70% and strain relief annealing is performed.
特開昭56−98420号公報では、5nr0.03〜
0.40%含有させた珪素鋼を熱間圧延し、この熱延鋼
板を709〜1000℃で焼鈍し、700〜400℃ま
で5℃/分以下の冷却速度で冷却し、その後冷間圧延、
焼鈍して、鉄損の低下と透磁率の向上を図っている。In Japanese Patent Application Laid-Open No. 56-98420, 5nr0.03~
Silicon steel containing 0.40% is hot rolled, this hot rolled steel plate is annealed at 709 to 1000°C, cooled to 700 to 400°C at a cooling rate of 5°C/min or less, and then cold rolled,
Annealing is used to reduce iron loss and improve magnetic permeability.
また特開昭57−203718号公報では、Cf O,
OO5%以下に極低炭とし、Sも0.010チ以下に低
減し1.u2o、15%以上含有する珪素鋼、あるいは
前記のC,Sを含み、MをO,OO5〜0.1%、13
i 0.0 OI O〜O,OO50%含有する珪素
mk熱間圧延し、この熱延鋼板を800℃以上で焼鈍し
、冷間圧延のち、s o O”C以上の温度で、2分以
内の高温短時間焼鈍を行って、内部酸化を生じさせず、
かつ結晶粒を大きくし、鉄損の低下と1.f1重密度の
向上を図っている。Furthermore, in Japanese Patent Application Laid-Open No. 57-203718, Cf O,
Ultra-low coal with OO of 5% or less and S content of 0.010 or less.1. U2O, silicon steel containing 15% or more, or containing the above-mentioned C, S, M O, OO5-0.1%, 13
i 0.0 OI O~O, Silicon mk containing 50% OO is hot rolled, this hot rolled steel plate is annealed at 800℃ or higher, and after cold rolling, it is heated at a temperature of s o O”C or higher for less than 2 minutes. High-temperature, short-time annealing is performed to prevent internal oxidation.
In addition, the crystal grains are made larger, reducing iron loss and 1. We are trying to improve the f1 density.
これらの提案により、セミプロセス無方向性電磁鋼板は
、磁気特性の改善がなされ、良好なものが夷遺されるよ
うになっている。As a result of these proposals, the magnetic properties of semi-processed non-oriented electrical steel sheets have been improved, and good ones are now available.
しかし、モーター、変圧器等の電気機器は、省エネルギ
ータイプにすること、あるいは高性能化することが要請
されている。このため、これらの電気機器の鉄心材料と
して、供されるセミプロセス無方向性電磁鋼板は、その
磁気特性の改善は、継続的に検討しなけれはならないと
いうのが冥情である。However, electric devices such as motors and transformers are required to be energy-saving types or to have higher performance. For this reason, it is necessary to continuously study how to improve the magnetic properties of semi-processed non-oriented electrical steel sheets, which are used as core materials for these electrical devices.
(発明が解決しようとする問題点)
ところで、変圧器等の鉄心は、無方向性電磁鋼板から、
所定の形状に打抜き加工されて、足取焼鈍が施される。(Problems to be solved by the invention) By the way, the iron core of transformers, etc. is made of non-oriented electrical steel sheet.
It is punched into a predetermined shape and subjected to foot annealing.
この歪取焼鈍においては、磁気特性全向上させるために
脱炭雰囲気で行われるが一敗的である。This strain relief annealing is carried out in a decarburizing atmosphere in order to completely improve the magnetic properties, but it is a failure.
かかる雰囲気下で焼鈍することにより、炭素が一層低減
され、また結晶粒の成長も促されて、磁気特性が良好と
なる。しかし歪取焼鈍後の鉄心(無方向性電磁鋼板)は
脆化し、例えば該鉄心を変圧器に組立時などに、クラッ
クが発生することが散見される。By annealing in such an atmosphere, carbon content is further reduced, crystal grain growth is also promoted, and magnetic properties are improved. However, the iron core (non-oriented electrical steel sheet) after strain relief annealing becomes brittle, and cracks are sometimes observed when the iron core is assembled into a transformer, for example.
またかかる無方向性電磁鋼板では、その製造コストを低
くし、安価にすることが一方で必要であり、また、その
製造工程を、1つでも省略し、生産性を高めることが重
要である。In addition, it is necessary to reduce the manufacturing cost of such non-oriented electrical steel sheets, and it is also important to omit at least one manufacturing process to increase productivity.
(問題点を解決するだめの手段)
本発明は歪取焼鈍後に脆化せず、所望の電気機器例えば
変圧器のコアに、クラックなどのトラブルを生じること
なく組立成形され、また磁気特性もすぐれ、安価にして
生産性よく無方向性電磁鋼板を得ることを目的とする。(Means for Solving the Problems) The present invention does not become brittle after strain relief annealing, can be assembled and molded into the core of a desired electrical device, such as a transformer, without causing troubles such as cracks, and has excellent magnetic properties. The purpose is to obtain non-oriented electrical steel sheets at low cost and with high productivity.
本発明の要旨は重量係で1、C:0.020%以下、S
i:1.0%以下、Mn : 0.75%以上1.50
%以下、M:O,lO%超o、 a o %以下、B:
O,0O03チ以上0.0100%以下、残部が鉄およ
び不可避的不純物からなるスラブを、仕上圧延の出側温
度を900℃以上、巻取温度をSOO℃以上で熱間圧延
し1巻取り後、その保有熱で焼鈍し、1回または中間焼
鈍をはさんで、スキンパス圧延r含む2回以上の冷間圧
延を行い、そのままあるいは焼鈍、打抜き加工後、歪取
焼鈍を行うことを特徴とする。The gist of the present invention is 1 in terms of weight, C: 0.020% or less, S
i: 1.0% or less, Mn: 0.75% or more 1.50
% or less, M: O, lO% or less, a o % or less, B:
A slab consisting of O,0O03% or more and 0.0100% or less, the balance being iron and unavoidable impurities, is hot rolled at a finish rolling exit temperature of 900°C or higher and a coiling temperature of SOO°C or higher, after 1 coiling. The material is annealed with its retained heat, cold rolled once or twice or more including skin pass rolling with an intermediate annealing in between, and then subjected to strain relief annealing either as is or after annealing and punching. .
次に本発明について詳細に述べる。Next, the present invention will be described in detail.
本発明者達は、磁気特性がすぐれ、歪取焼鈍後に脆化せ
ず、安価に生産性よく無力同性電磁鋼板を製造すべく検
討した。その結果、Cを0.020チ以下とした珪素鋼
に、Mn f 0.75〜150%、Mを0.10%超
〜0.60%以下と、ともに多口に含有させ、さらにB
をO,OOO3〜O,OI O0%含有させると、磁気
特性はすぐれていて、かつ歪取焼鈍の雰囲気が、脱炭性
あるいは酸化性であっても、内部酸化が生じなくて耐脆
性がすぐれ、鉄心に組立成形時などでクラックが光生じ
ないことを知見した。The inventors of the present invention have conducted studies to produce a powerless isostatic electrical steel sheet that has excellent magnetic properties, does not become brittle after strain relief annealing, and is inexpensive and highly productive. As a result, silicon steel with a C content of 0.020 mm or less was made to contain a large amount of Mnf from 0.75 to 150%, M from more than 0.10% to 0.60%, and B.
When O, OOO3 to O, OI O0% is contained, the magnetic properties are excellent, and even if the atmosphere for strain relief annealing is decarburizing or oxidizing, internal oxidation does not occur and the brittle resistance is excellent. It was discovered that no cracks were formed in the iron core during assembly and molding.
また熱間圧延において、仕上圧延の出9III温度を9
00 ’C以上、巻取温度を800℃以上として、巻取
後その保有熱を利用して焼鈍すると、製造コストの低下
および生産性の向上が図られる。In addition, in hot rolling, the finish rolling temperature is set to 9
If the coiling temperature is set at 00'C or higher and the coiling temperature is 800C or higher and annealing is performed using the retained heat after winding, manufacturing costs can be reduced and productivity can be improved.
次に本発明の構成要件について説明する。Next, the constituent elements of the present invention will be explained.
Cは、磁気特性をよくするためには少ないほうが好まし
く、また磁気時効の原因となるので、0.020%以下
とする。In order to improve the magnetic properties, it is preferable to have a small amount of C, and since it causes magnetic aging, the content should be 0.020% or less.
Slは、固有抵抗を増加して、鉄損の改善を図るために
含有されるものであるが、本発明ではセミプロセス無方
向性電磁鋼板を対象としているので、その加工性を良好
とするために、1.0%以下とする。Sl is included to increase specific resistance and improve core loss, but since the present invention is aimed at semi-processed non-oriented electrical steel sheets, it is included to improve workability. The content shall be 1.0% or less.
Mn は磁気特性を改善する作用があり、このために
は、0.75%以上含有させる必要がある。−万、この
含有量が多くなると、熱間圧延後の焼鈍時、あるいは中
間焼鈍時に、フェライト−オーステナイト変態を生じや
すく、磁気特性の劣化を招くことかめるので、1.5o
%以下とする。Mn has the effect of improving magnetic properties, and for this purpose it is necessary to contain it in an amount of 0.75% or more. - If this content increases, ferrite-austenite transformation is likely to occur during annealing after hot rolling or during intermediate annealing, leading to deterioration of magnetic properties, so 1.5o
% or less.
AEi/j固有抵抗を高め、鉄損を低くめる作用があり
、このためにO,l O%超とする。一方、その含有量
が過多になると、磁気特性が劣化するので、0.60チ
以下とする。AEi/j has the effect of increasing specific resistance and lowering iron loss, and for this purpose O,l is set to exceed O%. On the other hand, if the content is too large, the magnetic properties will deteriorate, so the content should be 0.60 or less.
Bは歪取焼鈍において、鋼板の内部酸化を防止し、脆化
を防ぐ作用があり、このためには0.0003係以上の
含有が必要である。一方、この含有量が多いと、熱間圧
延前のスラブに割れが生じることがあるので、0.01
00%以下とする。B has the effect of preventing internal oxidation of the steel plate and preventing embrittlement during strain relief annealing, and for this purpose, it must be contained in an amount of 0.0003 or more. On the other hand, if this content is large, cracks may occur in the slab before hot rolling, so 0.01
00% or less.
S、P、Ti、Zrなどの不純物として不可避的に含ま
れる成分は、できるだけ少ないほうが好ましい。It is preferable that components unavoidably included as impurities such as S, P, Ti, and Zr be as small as possible.
前記成分からなるスラブは、公知の加熱温度例えば11
00〜1400℃に加熱され、熱間圧延される。この熱
間圧延では、仕上圧延の出側温度を900°C以上とし
、巻取温度を800℃以上とする。前記仕上圧延の出側
温度が低いと、磁気特性が劣化するとともに、熱延板で
の結晶粒の形態が悪くなる。これを防ぐために前記出側
温度を900℃以上とする。A slab consisting of the above components is heated at a known heating temperature, e.g.
It is heated to 00 to 1400°C and hot rolled. In this hot rolling, the finish rolling exit temperature is set at 900°C or higher, and the coiling temperature is set at 800°C or higher. If the exit temperature of the finish rolling is low, the magnetic properties will deteriorate and the morphology of the crystal grains in the hot rolled sheet will deteriorate. In order to prevent this, the outlet temperature is set to 900° C. or higher.
巻取温度については、その後の別途の熱延板焼鈍を省略
し、省工程を図りながら、磁気特性tよくするために、
800℃以上の温度にてコイルに巻取る。Regarding the coiling temperature, in order to omit the subsequent separate hot-rolled sheet annealing and save process steps, we also improved the magnetic properties.
Wind it into a coil at a temperature of 800°C or higher.
前記成分の熱延板を、SOO℃以上の温度で巻取り、コ
イルにすると、その保有熱が、結晶粒の整流化および成
長が達成される。また必要に応じて、補助的に加熱装置
を作用させて、保有熱に相乗させて自己焼鈍を行っても
よい。When a hot-rolled sheet of the above components is wound up to form a coil at a temperature of SOO° C. or higher, the heat retained therein achieves rectification and growth of crystal grains. Further, if necessary, a heating device may be used to supplement the retained heat to perform self-annealing.
次いで1回の冷間圧延、または中間焼鈍をはさんで、2
回以上の冷間圧延により、所望の・板厚にされる。この
冷間圧延は、圧下率を2〜12チで行うスキンパス圧延
を含むものである。スキンパス圧延する場合、その圧下
率が少ないと、歪取焼鈍などのその後の焼鈍で結晶粒の
成長が少なく、磁気特性が良好とならないので2−以上
とする。Then, after one cold rolling or intermediate annealing, 2
The desired thickness is obtained by cold rolling more than once. This cold rolling includes skin pass rolling performed at a rolling reduction of 2 to 12 inches. In the case of skin pass rolling, if the rolling reduction rate is small, the growth of crystal grains will be small in subsequent annealing such as strain relief annealing, and the magnetic properties will not be good, so it is set to 2- or more.
一方、圧下率が高くなりすぎると、結晶粒の成長が弱く
なるので12チ以下とする。その後、冷間圧延のまま、
あるいは焼鈍して、所定の形状をする鉄心、例えばEI
ココアに打抜き加工される。On the other hand, if the rolling reduction rate becomes too high, the growth of crystal grains becomes weak, so it is set to 12 inches or less. After that, as cold rolled,
Or an iron core that is annealed and shaped into a predetermined shape, such as EI.
Cocoa is stamped.
打抜き加工後は歪を除去するとともに、磁気特性rよく
するために、歪取焼鈍が例えば700〜900℃で行わ
れる。この歪取焼鈍では結晶粒の成長あるいは鋼中のC
f減少し、また不純物の除去を図るために脱炭雰囲気で
行われるが、本発明ではB2前記の如く含有させている
ので、内部酸化とくに粒界酸化が生ぜず、鋼は脆化しな
い。また内部酸化が生じないので、磁気特性の劣化がな
く、歪取焼鈍本来の結晶粒成長およびC除去などの機能
と相乗して、磁気特性がすぐれている。After punching, strain relief annealing is performed at, for example, 700 to 900° C. in order to remove strain and improve magnetic properties. In this strain relief annealing, the growth of crystal grains or C in the steel
The process is carried out in a decarburizing atmosphere in order to reduce f and remove impurities, but in the present invention, since B2 is contained as described above, internal oxidation, especially grain boundary oxidation, does not occur and the steel does not become brittle. Furthermore, since no internal oxidation occurs, there is no deterioration in magnetic properties, and the magnetic properties are excellent due to the effects of strain relief annealing, such as crystal grain growth and carbon removal.
さらに、本発明ではMn + kt f前記の如くとも
に多く含有しているので、この点からも磁気特性はすぐ
れる。Furthermore, since the present invention contains a large amount of both Mn + ktf as described above, the magnetic properties are excellent from this point as well.
(冥施例)
第1表に示す鋼組成の供試鋼を、第2表に示す条件で処
理加工して、無方向性成磁鋼板を製造した。得られた無
方向性電磁鋼板の磁気特性、加工性を調査し、その結果
を第2表にまとめて示す。(Example) Test steels having the steel compositions shown in Table 1 were processed under the conditions shown in Table 2 to produce non-oriented magnetic steel sheets. The magnetic properties and workability of the obtained non-oriented electrical steel sheets were investigated, and the results are summarized in Table 2.
第2表に示す結果からも明らかなように、本発明による
方法により得られた電磁鋼板の特性は、例えば、Mn、
AM、B 等の成分や熱間圧延条件等全制御しなかった
従来例と比較して、格段に優れたものであることが明ら
かである。As is clear from the results shown in Table 2, the characteristics of the electrical steel sheet obtained by the method according to the present invention are, for example, Mn,
It is clear that this is much better than the conventional example in which components such as AM and B, hot rolling conditions, etc. were not fully controlled.
さらに本発明によるものは、繰返し曲げ特性や、EIコ
コア型時の成型加工性が著しく優れている。Furthermore, the material according to the present invention has excellent repeated bending properties and moldability in EI cocoa molding.
これは、写真1.2からBを添加することにより、表面
層近くの酸化は、従来例と変わらないが、粒界の酸化度
合が従来例より格段に小さいことがわかる。From Photo 1.2, it can be seen that by adding B, the oxidation near the surface layer is the same as in the conventional example, but the degree of oxidation at the grain boundaries is much smaller than in the conventional example.
(発明の効果)
本発明によると、以上のように歪取焼鈍後の鋼板は脆化
がなく、EIココアど所望の電気像器に問題なく成型加
工される。磁気特性はすぐれており、さらに熱延し、巻
取後の自己保有熱を利用して焼鈍されるので、別途の焼
鈍工程が省略され、製造工程が短縮されて生産性が向上
するとともに。(Effects of the Invention) According to the present invention, as described above, the steel plate after strain relief annealing is free from embrittlement and can be formed into a desired electric imager such as EI cocoa without any problem. It has excellent magnetic properties and is further annealed using its own heat after hot rolling and winding, so a separate annealing process is omitted, shortening the manufacturing process and improving productivity.
製造に要する熱エネルギーが低減される。Thermal energy required for manufacturing is reduced.
第1図は本発明の一実施例の試料符号1(スキンパス圧
延工程を経て製造したもの)の鋼板表面層部の顕微鏡組
織写真、第2図は比較例による試料符号7の鋼板表面層
部の顕微鏡組織写真を示す。Fig. 1 is a microscopic microstructure photograph of the surface layer of a steel plate of sample code 1 (manufactured through a skin pass rolling process) according to an example of the present invention, and Fig. 2 is a photograph of the surface layer of a steel plate of sample code 7 according to a comparative example. A microscopic tissue photograph is shown.
Claims (1)
以下、Mn:0.75%以上1.50%以下、Al:0
.10%超0.60%以下、B:0.0003%以上0
.0100%以下、残部が鉄および不可避的不純物から
なるスラブを、仕上圧延温度を900℃以上、巻取温度
を800℃以上で熱間圧延し、巻取り後、その保有熱を
利用して焼鈍し、1回または中間焼鈍をはさんで、スキ
ンパス圧延を含む2回以上の冷間圧延を行い、そのまま
あるいは焼鈍、打抜き加工後、歪取焼鈍を行うことを特
徴とする歪取焼鈍後の耐脆性と磁気特性のすぐれた無方
向性電磁鋼板の製造方法。 2、スキンパス圧延の圧下率が、2〜12%であること
を特徴とする特許請求の範囲第1項記載の無方向性電磁
鋼板の製造方法。[Claims] 1. In weight%, C: 0.020% or less, Si: 1.0%
Below, Mn: 0.75% or more and 1.50% or less, Al: 0
.. Over 10% but not more than 0.60%, B: 0.0003% or more 0
.. A slab consisting of 0.0100% or less, the balance consisting of iron and unavoidable impurities is hot rolled at a finish rolling temperature of 900°C or higher and a coiling temperature of 800°C or higher, and after coiling, it is annealed using the retained heat. , cold rolling is performed once or twice or more including skin pass rolling with intermediate annealing in between, and strain relief annealing is performed either directly or after annealing and punching. and a method for manufacturing non-oriented electrical steel sheets with excellent magnetic properties. 2. The method for producing a non-oriented electrical steel sheet according to claim 1, wherein the rolling reduction ratio of the skin pass rolling is 2 to 12%.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP6303486A JPS62222025A (en) | 1986-03-20 | 1986-03-20 | Manufacture of nonoriented electrical sheet superior in brittleness resistance and magnetic characteristic after stress relief annealing |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP6303486A JPS62222025A (en) | 1986-03-20 | 1986-03-20 | Manufacture of nonoriented electrical sheet superior in brittleness resistance and magnetic characteristic after stress relief annealing |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS62222025A true JPS62222025A (en) | 1987-09-30 |
JPS6316447B2 JPS6316447B2 (en) | 1988-04-08 |
Family
ID=13217638
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP6303486A Granted JPS62222025A (en) | 1986-03-20 | 1986-03-20 | Manufacture of nonoriented electrical sheet superior in brittleness resistance and magnetic characteristic after stress relief annealing |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS62222025A (en) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2011162821A (en) * | 2010-02-08 | 2011-08-25 | Nippon Steel Corp | Method for producing non-oriented electromagnetic steel sheet excellent in magnetic characteristic in rolling direction |
Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5743132A (en) * | 1980-08-28 | 1982-03-11 | Toshiba Corp | High-frequency heater |
JPS57203718A (en) * | 1981-06-10 | 1982-12-14 | Nippon Steel Corp | Manufacture of nondirectional electrical steel plate extremely excellent in its magnetic characteristic |
JPS58117828A (en) * | 1981-12-28 | 1983-07-13 | Nippon Steel Corp | Production of semi-process nondirectional electrical sheet having low iron loss and high magnetic flux density |
JPS60159157A (en) * | 1984-01-30 | 1985-08-20 | Nippon Yakin Kogyo Co Ltd | Fe-ni alloy having excellent hot workability |
-
1986
- 1986-03-20 JP JP6303486A patent/JPS62222025A/en active Granted
Patent Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5743132A (en) * | 1980-08-28 | 1982-03-11 | Toshiba Corp | High-frequency heater |
JPS57203718A (en) * | 1981-06-10 | 1982-12-14 | Nippon Steel Corp | Manufacture of nondirectional electrical steel plate extremely excellent in its magnetic characteristic |
JPS58117828A (en) * | 1981-12-28 | 1983-07-13 | Nippon Steel Corp | Production of semi-process nondirectional electrical sheet having low iron loss and high magnetic flux density |
JPS60159157A (en) * | 1984-01-30 | 1985-08-20 | Nippon Yakin Kogyo Co Ltd | Fe-ni alloy having excellent hot workability |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2011162821A (en) * | 2010-02-08 | 2011-08-25 | Nippon Steel Corp | Method for producing non-oriented electromagnetic steel sheet excellent in magnetic characteristic in rolling direction |
Also Published As
Publication number | Publication date |
---|---|
JPS6316447B2 (en) | 1988-04-08 |
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