JP2853552B2 - Non-oriented electrical steel sheet with excellent magnetic properties and manufacturing method - Google Patents
Non-oriented electrical steel sheet with excellent magnetic properties and manufacturing methodInfo
- Publication number
- JP2853552B2 JP2853552B2 JP6010589A JP1058994A JP2853552B2 JP 2853552 B2 JP2853552 B2 JP 2853552B2 JP 6010589 A JP6010589 A JP 6010589A JP 1058994 A JP1058994 A JP 1058994A JP 2853552 B2 JP2853552 B2 JP 2853552B2
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- weight
- magnetic properties
- oriented electrical
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Classifications
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
- H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
- H01F1/147—Alloys characterised by their composition
- H01F1/14766—Fe-Si based alloys
- H01F1/14775—Fe-Si based alloys in the form of sheets
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- Physics & Mathematics (AREA)
- Electromagnetism (AREA)
- Chemical & Material Sciences (AREA)
- Dispersion Chemistry (AREA)
- Engineering & Computer Science (AREA)
- Power Engineering (AREA)
- Manufacturing Of Steel Electrode Plates (AREA)
- Soft Magnetic Materials (AREA)
Description
【０００１】[0001]
【産業上の利用分野】この発明は、磁気特性の優れた無
方向性電磁鋼板とその製造方法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a non-oriented electrical steel sheet having excellent magnetic properties and a method for producing the same.
【０００２】[0002]
【従来の技術】従来より、無方向性電磁鋼板は発電機や
電動機などの回転機に多く使用される磁性材料の一つと
してよく知られている。この無方向性電磁鋼板は、一般
にはＬＤ転炉で溶製してから、連続鋳造を経て製造され
た不純物や介在物の著しく少ないけい素鋼スラブを熱間
圧延→酸洗→冷間圧延→連続焼鈍→表面処理の各工程を
経て製造されている。2. Description of the Related Art Conventionally, non-oriented electrical steel sheets are well known as one of magnetic materials often used in rotating machines such as generators and electric motors. This non-oriented electrical steel sheet is generally melted in an LD converter, and then hot rolled, pickled, cold rolled, and then silicon steel slabs, which are produced through continuous casting and have significantly less impurities and inclusions. It is manufactured through continuous annealing → surface treatment.
【０００３】ここに、磁気特性の優れた無方向性電磁鋼
板を製造するには、熱間圧延を行ったのち、冷間圧延に
先立ってこの熱延鋼板に焼鈍を施し結晶粒を粗大化する
ことが有効であるとされていた。その際には、フルプロ
セスの場合は仕上連続焼鈍で、セミプロセスの場合は歪
取り焼鈍で、それぞれ結晶粒の粗大化が行われていた。Here, in order to produce a non-oriented electrical steel sheet having excellent magnetic properties, after hot rolling, the hot-rolled steel sheet is annealed prior to cold rolling to coarsen crystal grains. Was to be effective. At that time, in the case of the full process, the finish continuous annealing was performed, and in the case of the semi-process, the strain relief annealing was performed to coarsen the crystal grains.
【０００４】そして、結晶粒の成長を妨げる酸化物や窒
化物、硫化物などの非金属介在物の量を極力低減する
か、または粗大化させて無害化することが有効とされて
いる。例えば、高けい素鋼板の製造方法で素材中のＳ、
Ｎ、Ｏを抑制することにより低鉄損の鋼板を得る方法
(特開昭59−74223 号公報、特開昭60−141829号公報な
ど) が提案されている。[0004] It is effective to reduce the amount of nonmetallic inclusions such as oxides, nitrides, and sulfides that hinder the growth of crystal grains as much as possible or to make them coarse to render them harmless. For example, in the method of manufacturing high silicon steel sheet,
Method for obtaining steel sheet with low iron loss by suppressing N and O
(JP-A-59-74223, JP-A-60-141829, etc.) have been proposed.
【０００５】しかし、従来の磁気特性の優れた無方向性
電磁鋼板はいずれも真空脱ガス処理、介在物除去処理あ
るいは粗大化処理を行うなど製造コストの上昇は免れな
かった。上記のごとく、従来、無方向性電磁鋼板の磁気
特性の改善は、コストダウンを考慮することなく行われ
ていた。[0005] However, conventional non-oriented electrical steel sheets having excellent magnetic properties have been inevitably increased in production cost by performing vacuum degassing treatment, inclusion removal treatment or coarsening treatment. As described above, conventionally, the magnetic properties of non-oriented electrical steel sheets have been improved without considering cost reduction.
【０００６】かかる現状に鑑み、本発明者は、コスト低
減とともに磁気特性の改善を図った無方向性電磁鋼板と
その製造方法を提案した。すなわち、本発明者は、特開
平３−20413 号公報において、Ｃ、Ｎ、Ｖの各含有量を
抑制することにより磁気特性を改善する試みを提案し
た。それによれば、Ｃ:0.01 ％以下、Ｎ:0.005％以下、
Ｖ:0.01 ％以下というようにこれらの元素の含有量を特
定範囲内に抑制するのである。In view of this situation, the present inventor has proposed a non-oriented electrical steel sheet which has reduced costs and improved magnetic properties and a method of manufacturing the same. That is, the present inventor has proposed in Japanese Patent Application Laid-Open No. Hei 3-20413 an attempt to improve the magnetic properties by suppressing the contents of C, N, and V. According to it, C: 0.01% or less, N: 0.005% or less,
V: The content of these elements is suppressed to a specific range such as 0.01% or less.
【０００７】[0007]
【発明が解決しようとする課題】しかしながら、その後
の研究開発によって、そのようにして製造される無方向
性電磁鋼板の中に磁気特性の不良なものがときどき発生
することが判明した。したがって、この発明の目的は、
優れた磁気特性を安定して発揮できる安価な無方向性電
気鋼板およびその製造方法を提供することである。However, subsequent research and development has revealed that some non-oriented electrical steel sheets produced in this manner sometimes have poor magnetic properties. Therefore, the purpose of this invention is
An object of the present invention is to provide an inexpensive non-oriented electrical steel sheet capable of stably exhibiting excellent magnetic properties and a method for manufacturing the same.
【０００８】[0008]
【課題を解決するための手段】そこで、本発明者は、上
述のような目的を達成すべく、磁気特性が不安定化する
原因を探究しているうちに、含有されるsol.AlおよびＶ
元素が影響していることに気付き、さらに種々研究の結
果、鋼中のsol.Alが極めて少ない領域でＶをむしろ積極
的に添加することでSi含有量を4.0 ％以下というように
高けい素領域でも磁気特性の改善・安定化が図られるこ
とを見い出し、この発明を完成した。In order to achieve the above-mentioned object, the present inventor has searched for the cause of the instability of the magnetic characteristics and found that the sol.
He noticed that the element had an effect, and as a result of various studies, it was found that the addition of V in the region where the amount of sol. It has been found that the magnetic characteristics can be improved and stabilized in the region, and the present invention has been completed.
【０００９】ここに、この発明は、重量％で、Ｃ:0.01
％以下、Si:4.0％以下、Mn:1.0％以下、sol.Al:0.005％
以下、Ｎ:0.01％以下、Ｖ:0.05 〜1.0 ％、残部Feおよ
び不可避的不純物から成る鋼組成を有する磁気特性に優
れた無方向性電磁鋼板である。[0009] Here, the present invention relates to the following:
%, Si: 4.0% or less, Mn: 1.0% or less, sol.Al: 0.005%
A non-oriented electrical steel sheet having excellent magnetic properties and having a steel composition comprising N: 0.01% or less, V: 0.05 to 1.0%, balance Fe and unavoidable impurities.
【００１０】また、別の面からは、この発明は、上記鋼
組成を有するけい素鋼スラブに通常の熱間圧延を施して
得た熱延鋼板を酸洗したのち、冷間圧延を施して所定板
厚に仕上げ、さらに650 〜1000 ℃で仕上連続焼鈍を行
う、無方向性電磁鋼板の製造方法である。この発明の好
適態様によれば、上記熱延鋼板を600 〜1000℃で焼鈍し
てから酸洗または酸洗後焼鈍するようにしてもよい。In another aspect, the present invention provides a hot rolled steel sheet obtained by subjecting a silicon steel slab having the above steel composition to ordinary hot rolling to pickling, followed by cold rolling. This is a method for producing a non-oriented electrical steel sheet, which is finished to a predetermined thickness and further subjected to finish continuous annealing at 650 to 1000 ° C. According to a preferred aspect of the present invention, the hot-rolled steel sheet may be annealed at 600 to 1000 ° C., and then annealed with pickling or annealed after pickling.
【００１１】[0011]
【作用】この発明にかかる無方向性電磁鋼板は、sol.Al
が極めて少ない領域で、Ｃ、Ｎの含有量を抑制し、Ｖを
添加しているため、バナジウム炭窒化物を生成し、Ｃ、
Ｎを固定する。かかるバナジウム炭窒化物はＶ:0.05％
以上の添加により粗大化するため、鋼母地の結晶粒の粒
成長性を阻害しなくなる。その結果、優れた磁気特性を
得るのに必要な粗大結晶粒が容易に得られる。この発明
の無方向性電磁鋼板の化学成分は次の理由により限定し
た。The non-oriented electrical steel sheet according to the present invention is sol.Al
In a region where the amount of C is extremely small, the contents of C and N are suppressed and V is added, so that vanadium carbonitride is generated,
N is fixed. Such vanadium carbonitride has V: 0.05%
Since the coarsening is performed by the above addition, the grain growth of the crystal grains of the steel matrix is not hindered. As a result, coarse crystal grains necessary for obtaining excellent magnetic properties can be easily obtained. The chemical components of the non-oriented electrical steel sheet of the present invention were limited for the following reasons.
【００１２】Ｃ:Ｃは磁気時効を引き起こし磁気特性の
劣化を招くため0.01重量％以下とした。好ましくは、0.
005 重量％以下である。C: Since C causes magnetic aging and causes deterioration of magnetic properties, C is set to 0.01% by weight or less. Preferably, 0.
005% by weight or less.
【００１３】Si:Siは鉄損低減に不可欠な元素である
が、前述のように0.005 ％以下というsol.Al領域ではSi
が4.0 重量％を超えると冷間圧延ができなくなるので4.
0 重量％以下とした。好ましくは、3.2 重量％以下であ
る。Si: Although Si is an element indispensable for reducing iron loss, as described above, in the sol.
If it exceeds 4.0% by weight, cold rolling cannot be performed.
0% by weight or less. Preferably, it is not more than 3.2% by weight.
【００１４】Mn:Mnも鉄損低減に有効な元素であるが、
1.0 重量％を超える濃度の添加はA3変態点の低下を招き
熱間圧延後の集合組織が磁気特性に不利となるため1.0
重量％以下とした。好ましくは、0.5 重量％以下であ
る。Mn: Mn is also an effective element for reducing iron loss.
1.0 1.0 Since the texture after the hot rolling is disadvantageous in magnetic properties causes deterioration of addition A 3 transformation point of concentration greater than wt%
% By weight or less. Preferably, it is at most 0.5% by weight.
【００１５】sol.Al:sol.Alは結晶粒の成長に大きな影
響を及ぼし、磁気特性の優れた結晶粒の大きな鋼板はso
l.Alをほとんど含有しないが、または約0.3 重量％とい
うように過度に含有するものが最もよいとされる。Sol.Al: sol.Al has a great influence on the growth of crystal grains.
l. Al is hardly contained, or excessively contained at about 0.3% by weight.
【００１６】このようにsol.Alを過度に含有するもの
は、有害な析出物となるＶよりもAlがＮと結合しやすい
ため、有害な炭窒化バナジウムは析出しない。しかも、
AlN の粗大な析出物として無害化される。しかし、過度
のAl添加は磁気特性の異方性が大きくなり、無方向性電
磁鋼板としては望ましくなく、またコストの高騰を招
く。そこで、この発明ではsol.Alは0.005 重量％以下の
ほとんど含有しない範囲に限定した。As described above, in the case where sol.Al is excessively contained, harmful vanadium carbonitride does not precipitate because Al is more easily bonded to N than V which is a harmful precipitate. Moreover,
Detoxified as coarse precipitates of AlN. However, excessive addition of Al increases the anisotropy of the magnetic properties, which is not desirable as a non-oriented electrical steel sheet, and raises the cost. Therefore, in the present invention, the content of sol. Al is limited to a range of 0.005% by weight or less and almost no content.
【００１７】Ｎ、Ｖ:ＮおよびＶは磁気特性に有害な微
細なバナジウム炭窒化物の析出を阻止するため、Ｎは0.
01％以下、好ましくは0.005 ％以下とし、Ｖは0.05％以
上1.0 ％以下とする。より好ましくは、Ｎ:0.003％以
下、Ｖ:0.05 〜0.2 ％である。N, V: Since N and V prevent the deposition of fine vanadium carbonitride, which is detrimental to the magnetic properties, N is set to 0.
01% or less, preferably 0.005% or less, and V is 0.05% or more and 1.0% or less. More preferably, the N content is 0.003% or less, and the V content is 0.05 to 0.2%.
【００１８】図１のグラフは、後述する実施例における
本発明材１を基本組成とし、Ｖ含有量を変えた0.3 ％Si
鋼に750 ℃×２時間で歪取焼鈍を行った後の鉄損値Ｗ
15/50とＶの含有量の関係を示す。The graph of FIG. 1 shows that the material 1 of the present invention in the examples described later has a basic composition and that the V content is changed to 0.3% Si.
Iron loss value W after performing strain relief annealing on steel at 750 ° C for 2 hours
The relation between 15/50 and the V content is shown.
【００１９】このグラフからも分かるように、前述の特
開平２−20413 号公報に示されたＶ含有量0.01％以下で
特性は良好であるが、同様にこの発明のＶ含有量0.05％
以上1.0 ％以下の領域でも磁気特性が良好となっている
ことが分かる。As can be seen from this graph, although the characteristics are good at a V content of 0.01% or less as disclosed in the above-mentioned JP-A-2-20413, similarly, the V content of the present invention is 0.05%.
It can be seen that the magnetic properties are good even in the region of not less than 1.0%.
【００２０】従来技術としての前者は、微細なＶ炭窒化
物の総量を抑制することで良好な磁気特性を得ているの
に対し、この発明では、Ｖ:0.05 〜1.0 ％というように
積極的に添加し、むしろＶ炭窒化物を粗大化させること
で良好な磁気特性を得るのである。The former as a prior art obtains good magnetic properties by suppressing the total amount of fine V carbonitrides, whereas the present invention actively pursues V: 0.05 to 1.0%. In addition, good magnetic properties can be obtained by coarsening the V carbonitride.
【００２１】次に、同様にして磁束密度Ｂ50とＶ含有量
との関係を求め、その結果を図２にグラフで示す。鉄損
の場合と同様の傾向がみられ、Ｖ:0.05 ％以上で全く従
来考えられていた傾向と逆の傾向が見られる。Next, the relationship between the magnetic flux density B 50 and the V content is determined in the same manner, and the results are shown in a graph in FIG. The same tendency as in the case of iron loss is observed. At V: 0.05% or more, a tendency opposite to the tendency completely considered conventionally is observed.
【００２２】この発明にかかる無方向性電磁鋼板も、従
来と同様に、LD転炉によって溶製され、続いて例えば連
続鋳造法で得られた高純度のけい素鋼スラブを熱間圧
延、冷間圧延、そして仕上げ連続焼鈍さらに適宜表面処
理を経て製造される。The non-oriented electrical steel sheet according to the present invention is also melted by an LD converter in the same manner as in the prior art, and then a high-purity silicon steel slab obtained, for example, by a continuous casting method is hot-rolled and cold-rolled. It is produced through cold rolling, finish continuous annealing, and further appropriately surface treatment.
【００２３】かかる製造過程における熱延鋼帯の焼鈍温
度は、熱延鋼帯の再結晶温度以上であれば十分で通常 6
00〜1000℃、好ましくは 650〜950 ℃である。熱延板の
焼鈍後には酸洗を行い、次いで冷間圧延を行えばよい。
必要により、焼鈍前に酸洗を行い不活性ガスまたは純水
素雰囲気下で焼鈍を行ってもよい。The annealing temperature of the hot-rolled steel strip in the production process is sufficient if it is equal to or higher than the recrystallization temperature of the hot-rolled steel strip.
The temperature is from 100 to 1000C, preferably from 650 to 950C. After annealing of the hot rolled sheet, pickling may be performed, and then cold rolling may be performed.
If necessary, acid cleaning may be performed before annealing, and annealing may be performed in an inert gas or pure hydrogen atmosphere.
【００２４】また、冷間圧延後に行う仕上連続焼鈍も再
結晶温度以上であればよく、一般に650 〜1000℃あれば
よく、好ましくは 700〜1000℃である。ただし、高温加
熱が好ましくないときには、この加熱温度の上限を 900
℃とする。次に、実施例によってこの発明の作用効果を
さらに具体的に説明する。The continuous continuous annealing performed after the cold rolling may be performed at a temperature not lower than the recrystallization temperature, generally at 650 to 1000 ° C., preferably 700 to 1000 ° C. However, when high-temperature heating is not desirable, the upper limit of this heating temperature is 900
° C. Next, the operation and effect of the present invention will be described more specifically with reference to examples.
【００２５】[0025]
(実施例１)本例では、Ｃ:0.003重量％、Si:0.3重量％、
Mn:0.3重量％、sol.Al＜0.001 重量％、Ｎ:0.002重量
％、Ｖ:0.13 重量％、残部実質的にFeよりなるけい素鋼
スラブ (本発明材１と称す) と、比較のためＣ:0.003重
量％、Si:0.3重量％、Mn:0.3重量％、sol.Al＜0.001 重
量％、Ｎ:0.005重量％、Ｖ:0.014重量％、残部実質的に
Feより成るけい素鋼スラブ (比較材１と称す) に通常の
熱間圧延を施し、板幅1000mm、板厚2.3 mmの熱延鋼帯を
得た。そして、引続き酸洗したのち冷間圧延を施して板
厚0.5 mmに仕上げ、さらに720 ℃×１分間均熱の条件で
仕上連続焼鈍を施した。(Example 1) In this example, C: 0.003% by weight, Si: 0.3% by weight,
Mn: 0.3% by weight, sol.Al <0.001% by weight, N: 0.002% by weight, V: 0.13% by weight, the balance being substantially Fe and a silicon steel slab (referred to as material 1 of the present invention). C: 0.003% by weight, Si: 0.3% by weight, Mn: 0.3% by weight, sol.Al <0.001% by weight, N: 0.005% by weight, V: 0.014% by weight, balance substantially
Normal hot rolling was performed on a silicon steel slab made of Fe (referred to as comparative material 1) to obtain a hot-rolled steel strip having a width of 1000 mm and a thickness of 2.3 mm. Then, after pickling, the sheet was cold-rolled to a sheet thickness of 0.5 mm, and further subjected to continuous annealing at 720 ° C. × 1 minute soaking.
【００２６】(実施例２)実施例１の本発明材１と同成分
の熱延鋼帯 (本発明材２と称す) および実施例１の比較
例１と同成分の熱延鋼帯 (比較材２と称す) を酸洗した
のち680 ℃×20時間の条件で熱延板焼鈍を施した。そし
て、引続き酸洗したのち冷間圧延を施して板厚0.5 mmに
仕上げ、さらに720 ℃×１分間均熱の条件で仕上連続焼
鈍を施した。Example 2 A hot-rolled steel strip having the same composition as the material 1 of the present invention in Example 1 (referred to as Material 2 of the present invention) and a hot-rolled steel strip having the same composition as Comparative Example 1 of Example 1 The material 2) was pickled and then annealed at 680 ° C. for 20 hours. Then, after pickling, the sheet was cold-rolled to a sheet thickness of 0.5 mm, and further subjected to continuous annealing at 720 ° C. × 1 minute soaking.
【００２７】(実施例３)Ｃ:0.007重量％、Si:2.7重量
％、Mn:0.7重量％、sol.Al＜0.003 重量％、Ｎ:0.001重
量％、Ｖ:0.8重量％、残部実質的にFeからなるけい素鋼
スラブ (本発明材３と称す) および比較のためＣ:0.007
重量％、Si:2.7重量％、Mn:0.7重量％、sol.Al＜0.003
重量％、Ｎ:0.01 重量％、Ｖ:0.027重量％、残部実質的
にFeからなるけい素鋼スラブ (比較材３と称す) に通常
の熱間圧延を施し、板幅1000mm、板厚2.3 mmの熱延鋼帯
を得た。(Example 3) C: 0.007% by weight, Si: 2.7% by weight, Mn: 0.7% by weight, sol.Al <0.003% by weight, N: 0.001% by weight, V: 0.8% by weight, balance substantially Silicon steel slab of Fe (referred to as Inventive Material 3) and C: 0.007 for comparison
Wt%, Si: 2.7 wt%, Mn: 0.7 wt%, sol.Al <0.003
%, N: 0.01% by weight, V: 0.027% by weight, the balance being substantially hot-rolled on a silicon steel slab (referred to as comparative material 3) consisting essentially of Fe, with a width of 1000 mm and a thickness of 2.3 mm Hot rolled steel strip was obtained.
【００２８】そして、引続き950 ℃×３分間均熱の条件
で熱延板焼鈍を施し酸洗したのち、冷間圧延を施して板
厚0.5 mmに仕上げ、さらに980 ℃×１分間均熱の条件で
仕上連続焼鈍を施した。Then, after hot-rolled sheet annealing and pickling under the condition of soaking at 950 ° C. × 3 minutes, the sheet is cold-rolled to a thickness of 0.5 mm, and further soaked at 980 ° C. for 1 minute. And subjected to finish continuous annealing.
【００２９】(実施例４)Ｃ:0.002重量％、Si:1.1重量
％、Mn:0.5重量％、sol.Al＜0.001 重量％、Ｎ:0.004重
量％、Ｖ:0.070重量％、全部実質的にFeからなるけい素
鋼スラブ (本発明材４と称す) および比較のためＣ:0.0
02重量％、Si:1.1重量％、Mn:0.5重量％、sol.Al＜0.00
1 重量％、Ｎ:0.004重量％、Ｖ:0.018重量％、残部実質
的にFeからなるけい素鋼スラブ (比較材４と称す) に通
常の熱間圧延を施し、板幅1000mm、板厚2.3 mmの熱延鋼
帯を得た。そして、引続き酸洗したのち冷間圧延を施し
て板厚0.5 mmに仕上げ、さらに890 ℃×１分間均熱の条
件で仕上連続焼鈍を施した。(Example 4) C: 0.002% by weight, Si: 1.1% by weight, Mn: 0.5% by weight, sol.Al <0.001% by weight, N: 0.004% by weight, V: 0.070% by weight, all substantially Silicon steel slab of Fe (referred to as material 4 of the present invention) and C: 0.0 for comparison
02% by weight, Si: 1.1% by weight, Mn: 0.5% by weight, sol.Al <0.00
1% by weight, N: 0.004% by weight, V: 0.018% by weight, the remainder being substantially hot-rolled on a silicon steel slab (comparative material 4) consisting essentially of Fe, with a width of 1000 mm and a thickness of 2.3 mm hot-rolled steel strip was obtained. Then, after pickling, the sheet was cold-rolled to a sheet thickness of 0.5 mm, and further subjected to finish continuous annealing under the condition of 890 ° C. × 1 minute soaking.
【００３０】上記実施例１〜４のそれぞれの方法により
製造された各無方向性電磁鋼板からそれぞれ試料を採取
してエプスタイン試験をフルプロセス材として切断した
まま、および750 ℃×２Hrの条件で歪取り焼鈍を施した
セミプロセス材として測定し、鉄損を調べた。その結果
を各実施例ごとに比較して表１に示す。Samples were taken from each of the non-oriented electrical steel sheets manufactured by the methods of Examples 1 to 4, and were subjected to the strain while being cut in the Epstein test as a full process material and at 750 ° C. × 2 hours. It was measured as a semi-processed material that had been annealed, and the iron loss was examined. The results are shown in Table 1 for each example.
【００３１】[0031]
【表１】 [Table 1]
【００３２】上記結果より各実施例ごとに本発明と比較
例を比較するに、いずれも本発明の鉄損は改善されてお
り磁気特性が優れていることがわかる。From the above results, comparing the present invention with the comparative examples for each example, it can be seen that the iron loss of the present invention is improved and the magnetic properties are excellent.
【００３３】[0033]
【発明の効果】この発明によれば、以上詳述したよう
に、Alをほとんど含有しない範囲で、かつＣ、Ｎの含有
量を低く抑制し、Ｖを一定量含有させることにより磁気
特性の優れた無方向性電磁鋼板をコスト高をもたらすこ
となく得ることができるのであって、この発明の実用上
の意義は特に大きい。According to the present invention, as described in detail above, the magnetic properties are improved by suppressing the contents of C and N to a low level and containing a certain amount of V in a range containing almost no Al. The non-oriented electrical steel sheet can be obtained without increasing the cost, and the practical significance of the present invention is particularly large.
【図１】鉄損とＶ含有量の関係を示すグラフである。FIG. 1 is a graph showing the relationship between iron loss and V content.
【図２】磁束密度とＶ含有量の関係を示すグラフであ
る。FIG. 2 is a graph showing a relationship between a magnetic flux density and a V content.
───────────────────────────────────────────────────── フロントページの続き (58)調査した分野(Int.Cl.6，ＤＢ名) C22C 38/00 303 C21D 8/12 C22C 38/12 H01F 1/16──────────────────────────────────────────────────続 き Continued on the front page (58) Field surveyed (Int. Cl. 6 , DB name) C22C 38/00 303 C21D 8/12 C22C 38/12 H01F 1/16
Claims (3)
％以下、 sol.Al:0.005％以下、 Ｎ:0.01 ％以下、 Ｖ:0.05
〜1.0 ％、 残部鉄および不可避不純物から成る鋼組成を有する磁気
特性の優れた無方向性電磁鋼板。[Claim 1] By weight%, C: 0.01% or less, Si: 4.0% or less, Mn: 1.0%
% Or less, sol.Al: 0.005% or less, N: 0.01% or less, V: 0.05
Non-oriented electrical steel sheet with excellent magnetic properties, having a steel composition consisting of ~ 1.0%, balance iron and unavoidable impurities.
％以下、 sol.Al:0.005％以下、 Ｎ:0.01 ％以下、 Ｖ:0.05
〜1.0 ％、 残部Feおよび不可避不純物から成る鋼組成を有する鋼
を、熱間圧延、冷間圧延、そして650 〜1000℃で仕上焼
鈍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. In% by weight, C: 0.01% or less, Si: 4.0% or less, Mn: 1.0%
% Or less, sol.Al: 0.005% or less, N: 0.01% or less, V: 0.05
Non-directional electromagnetic with excellent magnetic properties, characterized by hot rolling, cold rolling, and finish annealing at 650 to 1000 ° C. a steel having a steel composition of up to 1.0%, balance Fe and unavoidable impurities. Steel plate manufacturing method.
600 〜1000℃で焼鈍を行ってから酸洗を行い、次いで冷
間圧延を行う、請求項２記載の磁気特性の優れた無方向
性電磁鋼板の製造方法。3. A hot rolled sheet obtained after the hot rolling
3. The method for producing a non-oriented electrical steel sheet having excellent magnetic properties according to claim 2, wherein the steel sheet is annealed at 600 to 1000 ° C., then pickled, and then cold-rolled.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6010589A JP2853552B2 (en) | 1994-02-01 | 1994-02-01 | Non-oriented electrical steel sheet with excellent magnetic properties and manufacturing method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6010589A JP2853552B2 (en) | 1994-02-01 | 1994-02-01 | Non-oriented electrical steel sheet with excellent magnetic properties and manufacturing method |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH07216516A JPH07216516A (en) | 1995-08-15 |
| JP2853552B2 true JP2853552B2 (en) | 1999-02-03 |
Family
ID=11754438
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP6010589A Expired - Fee Related JP2853552B2 (en) | 1994-02-01 | 1994-02-01 | Non-oriented electrical steel sheet with excellent magnetic properties and manufacturing method |
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| Country | Link |
|---|---|
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2007069776A1 (en) * | 2005-12-15 | 2007-06-21 | Jfe Steel Corporation | Highly strong, non-oriented electrical steel sheet and method for manufacture thereof |
| JP2007186791A (en) * | 2005-12-15 | 2007-07-26 | Jfe Steel Kk | High strength non-oriented electrical steel sheet and method for manufacture the same |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP5130637B2 (en) * | 2006-03-22 | 2013-01-30 | Ｊｆｅスチール株式会社 | High strength non-oriented electrical steel sheet and manufacturing method thereof |
| PL3569726T3 (en) * | 2017-01-16 | 2022-08-01 | Nippon Steel Corporation | Non-oriented electrical steel sheet and method for manufacturing non-oriented electrical steel sheet |
-
1994
- 1994-02-01 JP JP6010589A patent/JP2853552B2/en not_active Expired - Fee Related
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2007069776A1 (en) * | 2005-12-15 | 2007-06-21 | Jfe Steel Corporation | Highly strong, non-oriented electrical steel sheet and method for manufacture thereof |
| JP2007186791A (en) * | 2005-12-15 | 2007-07-26 | Jfe Steel Kk | High strength non-oriented electrical steel sheet and method for manufacture the same |
| KR101011965B1 (en) * | 2005-12-15 | 2011-01-31 | 제이에프이 스틸 가부시키가이샤 | Highly strong, non-oriented electrical steel sheet and method for manufacture thereof |
| CN101310034B (en) * | 2005-12-15 | 2011-12-28 | 杰富意钢铁株式会社 | Highly strong, non-oriented electrical steel sheet and method for manufacture thereof |
| CN102226251B (en) * | 2005-12-15 | 2012-12-12 | 杰富意钢铁株式会社 | Highly strong, non-oriented electrical steel sheet and method for manufacture thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH07216516A (en) | 1995-08-15 |
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