JP4319889B2 - Non-oriented electrical steel sheet with excellent all-round magnetic properties and method for producing the same - Google Patents
Non-oriented electrical steel sheet with excellent all-round magnetic properties and method for producing the same Download PDFInfo
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- 229910000565 Non-oriented electrical steel Inorganic materials 0.000 title claims description 43
- 238000004519 manufacturing process Methods 0.000 title claims description 26
- 238000000137 annealing Methods 0.000 claims description 48
- 230000004907 flux Effects 0.000 claims description 48
- 238000005096 rolling process Methods 0.000 claims description 37
- 229910000831 Steel Inorganic materials 0.000 claims description 35
- 239000010959 steel Substances 0.000 claims description 35
- 238000005097 cold rolling Methods 0.000 claims description 27
- 230000009467 reduction Effects 0.000 claims description 18
- 238000005098 hot rolling Methods 0.000 claims description 12
- 239000012535 impurity Substances 0.000 claims description 11
- 229910052802 copper Inorganic materials 0.000 claims description 5
- 229910052758 niobium Inorganic materials 0.000 claims description 3
- 229910052720 vanadium Inorganic materials 0.000 claims description 3
- 229910052726 zirconium Inorganic materials 0.000 claims description 3
- 229910052785 arsenic Inorganic materials 0.000 claims description 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical group [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 55
- 229910052742 iron Inorganic materials 0.000 description 23
- 239000011162 core material Substances 0.000 description 18
- 239000013078 crystal Substances 0.000 description 14
- 230000000694 effects Effects 0.000 description 8
- 238000001953 recrystallisation Methods 0.000 description 8
- 230000007423 decrease Effects 0.000 description 6
- 238000005259 measurement Methods 0.000 description 6
- 239000000463 material Substances 0.000 description 5
- 238000001556 precipitation Methods 0.000 description 5
- -1 MnS Chemical class 0.000 description 4
- 230000009471 action Effects 0.000 description 4
- 238000000034 method Methods 0.000 description 4
- 239000000126 substance Substances 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 3
- 230000006872 improvement Effects 0.000 description 3
- 229910052718 tin Inorganic materials 0.000 description 3
- 238000011282 treatment Methods 0.000 description 3
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 2
- 150000004767 nitrides Chemical class 0.000 description 2
- 238000004080 punching Methods 0.000 description 2
- 229920006395 saturated elastomer Polymers 0.000 description 2
- 150000003568 thioethers Chemical class 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- 229910000976 Electrical steel Inorganic materials 0.000 description 1
- 229910001224 Grain-oriented electrical steel Inorganic materials 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 230000001276 controlling effect Effects 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000001934 delay Effects 0.000 description 1
- 238000001784 detoxification Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 230000007613 environmental effect Effects 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 230000002093 peripheral effect Effects 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000007712 rapid solidification Methods 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 230000002195 synergetic effect Effects 0.000 description 1
Classifications
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
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Description
本発明は、電気機器鉄心材料として使用される、磁気特性の優れた無方向性電磁鋼板に関するものであり、特に、回転機鉄心材料として望ましい、鋼板の板面内全周磁気特性に優れた無方向性電磁鋼板及びその製造方法を提供するものである。 The present invention relates to a non-oriented electrical steel sheet having excellent magnetic properties used as an electrical equipment iron core material. A grain-oriented electrical steel sheet and a method for producing the same are provided.
近年、電気機器、特に無方向性電磁鋼板がその鉄心材料として使用される回転機、中小型変圧器、電装品等の分野においては、世界的な電力・エネルギー節減、地球環境保全の動きの中で、高効率化、小型化の要請はますます強まりつつある。このような社会環境下において、当然無方向性電磁鋼板に対しても、その性能向上は喫緊の課題として強く要請されている。 In recent years, in the fields of electrical machinery, especially rotating machines, medium- and small-sized transformers, electrical components, etc. in which non-oriented electrical steel sheets are used as iron core materials, there is a trend of global power and energy saving and global environmental conservation. Therefore, the demand for higher efficiency and smaller size is increasing. Under such a social environment, of course, improvement of the performance of non-oriented electrical steel sheets is strongly demanded as an urgent issue.
周知のように、無方向性電磁鋼板においては、その性能向上に対して数多の手段がとられてきた。鉄損低減についてみると、一般には電気抵抗増大による渦電流損低減の観点から、ＳｉあるいはＡｌ等の含有量を高める方法が採られてきた。しかしこの方法では、反面、磁束密度の低下は避け得ないという問題点があった。 As is well known, many measures have been taken to improve the performance of non-oriented electrical steel sheets. In terms of iron loss reduction, in general, from the viewpoint of reducing eddy current loss due to an increase in electrical resistance, a method of increasing the content of Si or Al has been employed. However, this method has a problem that a decrease in magnetic flux density is inevitable.
また、単にＳｉ、あるいはＡｌ等の含有量を高めるのみではなく、Ｃ，Ｓ，Ｎ等の高純度鋼化や、特許文献１に記載されているようなＣａ添加等の化学的処置による不純物の無害化等による鉄損低減もなされてきた。さらに、特許文献２に記載されているような仕上焼鈍条件の工夫等の製造プロセス上の処置もなされてきた。一方、高磁束密度化についても、特許文献３に記載されているような熱延板焼鈍条件と冷延条件の工夫等の製造プロセス上の処置や、特許文献４に記載されているようなＳｎ，Ｃｕ等の合金元素添加による一次再結晶集合組織改善による処置等がなされてきた。 In addition to simply increasing the content of Si, Al, or the like, impurities such as C, S, N, etc. made of high purity steel, or chemical treatment such as Ca addition as described in Patent Document 1 are also introduced. Iron loss has been reduced by detoxification and the like. Furthermore, measures in the manufacturing process such as a device for finishing annealing as described in Patent Document 2 have been taken. On the other hand, with regard to increasing the magnetic flux density, treatments in the manufacturing process such as hot strip annealing conditions and cold rolling conditions as described in Patent Document 3 and Sn as described in Patent Document 4 Treatments have been made by improving the primary recrystallization texture by adding alloying elements such as Cu and Cu.
しかし上記のような処置により、無方向性電磁鋼板の磁気特性の向上はなされても、回転機等の鉄心として電気機器に使用される場合には、通常、ＪＩＳ等で規定されている鋼板圧延方向およびその鋼板面内直角方向の平均的磁気特性のみでなく、鋼板の板面内全周磁気特性、すなわち面内での等方的に優れた磁気特性が要請される。この目的のためには、無方向性電磁鋼板の｛１００｝集合組織を発達させることが望ましい。 However, even if the magnetic properties of the non-oriented electrical steel sheet are improved by the above-mentioned measures, when the steel core is used as an iron core of a rotating machine, etc. Not only the average magnetic property in the direction perpendicular to the direction of the steel sheet but also the whole-surface magnetic property in the sheet surface of the steel sheet, that is, the isotropically excellent magnetic characteristic in the surface is required. For this purpose, it is desirable to develop a {100} texture of the non-oriented electrical steel sheet.
無方向性電磁鋼板において｛１００｝集合組織を発達させる手段としては、特許文献５に記載されているように、冷間圧延の圧下率を８５％以上、望ましくは９０％以上の強圧下とし、かつ、仕上焼鈍を７００〜１２００℃で２分〜１時間の長時間とする方法があるが、このような強圧下冷間圧延および長時間仕上焼鈍を施すことは、生産性の低下や製造コストの上昇、さらには、設備制約上の問題が生じ、実用化には至っていない。
特許文献６や特許文献７に記載されているように、移動更新する冷却体表面によって溶鋼を凝固せしめて薄帯となす急冷凝固法等の特殊な製造方法も開発されているが、設備制約上の問題や安定生産性の問題等が生じ、実用化には至っていない。
As described in Patent Document 6 and Patent Document 7, special manufacturing methods such as a rapid solidification method in which molten steel is solidified by a moving and renewed cooling body surface to form a thin strip have been developed. Problems and stable productivity have occurred, and it has not been put into practical use.
上記に鑑み本発明は、無方向性電磁鋼板において｛１００｝集合組織を発達させ、回転機鉄心材料として望ましい、鋼板の板面内全周磁気特性に優れた無方向性電磁鋼板及びその製造方法を提供するものである。 In view of the above, the present invention develops a {100} texture in a non-oriented electrical steel sheet, and is desirable as a rotating machine core material. Is to provide.
本発明者らは、無方向性電磁鋼板の通常の製造工程において、冷間圧延前の結晶組織制御と冷間圧延圧下との組み合わせにより｛１００｝集合組織を発達させ、鋼板の板面内全周磁気特性に優れた無方向性電磁鋼板が得られないかとの観点から鋭意研究を積み重ねた。その結果、鋼板圧延方向磁束密度、およびその板面内垂直方向との磁束密度差、圧延方向から板面内２２．５度方向の磁束密度、および６７．５度方向，４５度方向との磁束密度Ｂ50差を一定範囲に制御すれば、回転機鉄心として用いた場合に優れた鉄損特性が得られること、また製造方法としては、冷間圧延前の結晶粒径をある値以上に粗大化させることにより、冷間圧延の圧下率を適切に選べは、短時間連続仕上焼鈍で、板面内全周磁気特性を顕著に向上させることが可能であることを究明した。 In the normal manufacturing process of a non-oriented electrical steel sheet, the inventors have developed a {100} texture by a combination of crystal structure control before cold rolling and cold rolling reduction, and the entire in-plane surface of the steel sheet is developed. From the viewpoint of obtaining non-oriented electrical steel sheets with excellent circumferential magnetic properties, we have conducted extensive research. As a result, the magnetic flux density in the steel sheet rolling direction, the magnetic flux density difference from the vertical direction in the plate surface, the magnetic flux density in the 22.5 degree direction in the plate surface from the rolling direction, and the magnetic flux in the 67.5 degree direction and 45 degree direction. If the difference in density B50 is controlled within a certain range, excellent iron loss characteristics can be obtained when used as a rotating machine core, and as a manufacturing method, the grain size before cold rolling is coarsened to a certain value or more. Thus, it has been found that the proper selection of the rolling reduction of cold rolling can be achieved by remarkably improving the in-plane circumferential magnetic properties by short-time continuous finish annealing.
本発明は上記知見に基づきなされたものであり、その要旨は次の通りである。
（１） 質量％で、
Ｃ ：０．００２％以下、 Ｓｉ：０．８％以上４．０％以下、
Ａｌ：０．１％以上２．０以下、 Ｍｎ：０．１％以上１．５％以下
を含有し、かつ、
Ｓｉ＋２Ａｌ−Ｍｎ：２％以上で、
残部Ｆｅおよび不可避不純物元素よりなる鋼であり、熱延板焼鈍後の平均結晶粒径を４３８μｍ以上とし、冷間圧延を圧下率８０％以上９０％以下で施すものであって、圧延方向の磁束密度Ｂ50が１．６９Ｔ以上でその板面内垂直方向の磁束密度Ｂ50との差が０．０３Ｔ未満であり、また圧延方向から板面内２２．５度方向の磁束密度Ｂ50が１．６５Ｔ以上で６７．５度方向の磁束密度Ｂ50との差が０．０４Ｔ未満であり、かつ、４５度方向の磁束密度Ｂ50との差が０．０６Ｔ未満であることを特徴とする無方向性電磁鋼板。
（２） 質量％でさらに、
Ｓｎ：０．０２〜０．４０％、 Ｃｕ：０．１〜１．０％
の１種または２種を含有することを特徴とする前記（１）に記載の無方向性電磁鋼板。
The present invention has been made based on the above findings, and the gist thereof is as follows.
(1) In mass%,
C: 0.002% or less, Si: 0.8% or more and 4.0% or less,
Al: 0.1% or more and 2.0 or less, Mn: 0.1% or more and 1.5% or less, and
Si + 2Al-Mn: 2% or more,
The steel is composed of the remaining Fe and inevitable impurity elements, the average grain size after hot-rolled sheet annealing is 438 μm or more, and cold rolling is performed at a rolling reduction of 80% or more and 90% or less, and the magnetic flux in the rolling direction The density B50 is 1.69T or more, the difference from the magnetic flux density B50 in the vertical direction in the plate surface is less than 0.03T, and the magnetic flux density B50 in the 22.5 degree direction in the plate surface from the rolling direction is 1.65T or more. The non-oriented electrical steel sheet is characterized in that the difference from the magnetic flux density B50 in the 67.5 degree direction is less than 0.04T and the difference from the magnetic flux density B50 in the 45 degree direction is less than 0.06T. .
(2) Further in mass%,
Sn: 0.02-0.40%, Cu: 0.1-1.0%
The non-oriented electrical steel sheet according to (1) above, which contains one or two of the above.
（３） 質量％で、
Ｃ ：０．００２％以下、 Ｓｉ：０．８％以上４．０％以下、
Ａｌ：０．１％以上２．０以下、 Ｍｎ：０．１％以上１．５％以下
を含有し、かつ、
Ｓｉ＋２Ａｌ−Ｍｎ：２％以上で、
残部Ｆｅおよび不可避不純物元素よりなる鋼を、熱間圧延後、熱延板焼鈍を施し、一回の冷間圧延により最終板厚とした後、仕上焼鈍を施す無方向性電磁鋼板の製造方法において、熱延板焼鈍後の平均結晶粒径を４３８μｍ以上とし、冷間圧延を圧下率：８０％以上９０％以下で施し、仕上焼鈍を８００℃以上９５０℃以下で１０秒以上１分以下施すことを特徴とする無方向性電磁鋼板の製造方法。
（４） 質量％でさらに、不可避不純物としてのＳ，Ｎ，Ｔｉをそれぞれ０．００２％以下とした鋼を用いることを特徴とする前記（３）に記載の無方向性電磁鋼板の製造方法。
（５） 質量％でさらに、不可避不純物としてのＶ，Ｚｒ，Ｎｂ，Ａｓをそれぞれ０．００３％以下とした鋼を用いることを特徴とする前記（３）または（４）に記載の無方向性電磁鋼板の製造方法。
(3) In mass%,
C: 0.002% or less, Si: 0.8% or more and 4.0% or less,
Al: 0.1% or more and 2.0 or less, Mn: 0.1% or more and 1.5% or less, and
Si + 2Al-Mn: 2% or more,
In the method for producing a non-oriented electrical steel sheet, the steel comprising the remaining Fe and inevitable impurity elements is subjected to hot rolling, followed by hot-rolled sheet annealing, the final sheet thickness is obtained by a single cold rolling, and then finish annealing. The average grain size after hot-rolled sheet annealing is set to 438 μm or more, cold rolling is performed at a reduction ratio of 80% to 90%, and finish annealing is performed at 800 ° C. to 950 ° C. for 10 seconds to 1 minute. The manufacturing method of the non-oriented electrical steel sheet characterized by the above-mentioned.
(4) The method for producing a non-oriented electrical steel sheet according to the above (3), wherein the steel further uses 0.002% or less of S, N, and Ti as inevitable impurities in mass%.
(5) Nondirectionality as described in (3) or (4) above, wherein the steel further uses less than 0.003% of V, Zr, Nb and As as inevitable impurities in mass%. A method for producing electrical steel sheets.
以上のように、本発明によれば、回転機鉄心材料として実用上好ましい特性を有する、鋼板の板面内全周磁気特性に優れた無方向性電磁鋼板を提供することができため、電気機器、特に無方向性電磁鋼板がその鉄心材料として使用される回転機等の分野における要請に十分に応えることができ、その工業的価値は極めて高いものである。 As described above, according to the present invention, it is possible to provide a non-oriented electrical steel sheet having practically preferable characteristics as a rotating machine iron core material and excellent in the in-plane magnetic properties of the steel sheet. In particular, the non-oriented electrical steel sheet can sufficiently meet the demands in the field of rotating machines and the like in which the core material is used, and its industrial value is extremely high.
以下、本発明を詳細に説明する。
まず、本発明の鋼成分の限定理由について述べる。
Ｃは、鉄損を高める有害な成分で、磁気時効の原因ともなるので、０．００２％以下とする。
Hereinafter, the present invention will be described in detail.
First, the reasons for limiting the steel components of the present invention will be described.
C is a harmful component that increases iron loss and causes magnetic aging, so it is 0.002% or less.
Ｓｉは、前記のように、電気抵抗を増大させて渦電流損を減少させることにより、鉄損を低減する作用のある成分であり、この作用を奏するためには、０．８％以上含有させる必要がある。一方、その含有量が増えると、前記のように、磁束密度が低下し、かつ、硬度の上昇を招いて、打ち抜き加工性を劣化させ、また、無方向性電磁鋼板の製造工程そのものにおいても、冷延等の作業性の低下、コスト高ともなるので、４．０％以下とする。 As described above, Si is a component having an action of reducing iron loss by increasing electric resistance and reducing eddy current loss. To achieve this action, Si is contained in an amount of 0.8% or more. There is a need. On the other hand, when the content is increased, as described above, the magnetic flux density is decreased, and the hardness is increased, the punching processability is deteriorated, and also in the manufacturing process itself of the non-oriented electrical steel sheet, Since workability such as cold rolling deteriorates and costs increase, the content is set to 4.0% or less.
Ａｌも、前記のように、Ｓｉと同様に電気抵抗を増大させて渦電流損を減少させることにより、鉄損を低減する作用のある成分であり、また、熱延板焼鈍時の結晶粒成長性を促進する作用を有する。これらの作用を奏するためには、０．１％以上含有させる必要がある。一方、その含有量が増えると磁束密度が低下し、かつ降伏比の減少を招いて打ち抜き加工性を劣化させるので、２．０％以下とする。 As described above, Al is also a component having an action of reducing iron loss by increasing electric resistance and reducing eddy current loss in the same manner as Si, and crystal grain growth during hot-rolled sheet annealing. Has the effect of promoting sex. In order to exhibit these effects, it is necessary to contain 0.1% or more. On the other hand, if the content is increased, the magnetic flux density is lowered and the yield ratio is reduced to deteriorate the punching workability.
Ｍｎも、電気抵抗を増大させて渦電流損を減少させることにより、鉄損を低減する作用を有する。この目的のためには０．１％以上含有させる必要がある。しかしその含有量が増えると、熱延板焼鈍時の結晶粒成長性そのものが低下するので、１．５％以下とする。 Mn also has an effect of reducing iron loss by increasing electric resistance and reducing eddy current loss. For this purpose, it is necessary to contain 0.1% or more. However, if the content is increased, the crystal grain growth itself during the hot-rolled sheet annealing is lowered, so the content is made 1.5% or less.
なお、上記の合金元素成分Ｓｉ，Ａｌ，Ｍｎ相互の間には、Ｓｉ＋２Ａｌ−Ｍｎ：２％以上の関係を満足する必要がある。これは、Ｓｉ＋２Ａｌ−Ｍｎが２％未満では、α−γ変態が存在する化学成分系となり、無方向性電磁鋼板の製造工程における焼鈍時、特に本発明の特徴とする熱延板焼鈍時に変態が生じ、熱延板焼鈍後の結晶粒径の粗大化を阻害し、続く冷間圧延の圧下率制御をもってしても、仕上焼鈍後の｛１００｝集合組織の発達が抑制され、板面内全周磁気特性の向上が阻まれるためである。 In addition, it is necessary to satisfy the relationship of Si + 2Al-Mn: 2% or more between the alloy element components Si, Al, and Mn. If Si + 2Al-Mn is less than 2%, it becomes a chemical component system in which an α-γ transformation exists, and the transformation occurs during annealing in the manufacturing process of a non-oriented electrical steel sheet, particularly during hot-rolled sheet annealing, which is a feature of the present invention. And the growth of {100} texture after finish annealing is suppressed even if the rolling reduction control of the subsequent cold rolling is inhibited. This is because improvement of the peripheral magnetic characteristics is hindered.
Ｓｎは、鋼板の一次再結晶集合組織を磁気特性に望ましい（１００）、もしくは（１１０）集合組織に発達させ、かつ、磁気特性に望ましくない（１１１）集合組織を抑制する効果を有するので、必要に応じて添加する。この目的のためには０．０２％以上含有させる必要がある。一方、その含有量が増えても作用は飽和し、むしろ焼鈍時の結晶粒成長性が抑制され、磁気特性が劣化する結果となるので、０．４０％以下とする。 Sn is necessary because it has the effect of developing the primary recrystallized texture of the steel sheet to a desirable (100) or (110) texture for magnetic properties and suppressing the undesirable (111) texture for magnetic properties. Add as appropriate. For this purpose, it is necessary to contain 0.02% or more. On the other hand, even if the content is increased, the action is saturated, rather the crystal grain growth property during annealing is suppressed and the magnetic properties are deteriorated, so the content is made 0.40% or less.
ＣｕもＳｎと同様に、鋼板の一次再結晶集合組織を磁気特性に望ましいものに発達させる効果を有するので、必要に応じて添加する。この効果を発揮させるためには０．１％以上含有させる必要がある。しかし、その含有量が増えると熱間脆化を招き、無方向性電磁鋼板の製造工程における熱延等での作業性を低下させるので、１．０％以下とする。 Similarly to Sn, Cu has the effect of developing the primary recrystallization texture of the steel sheet to a desirable one for magnetic properties, so it is added as necessary. In order to exhibit this effect, it is necessary to contain 0.1% or more. However, when the content increases, hot embrittlement is caused, and workability in hot rolling or the like in the manufacturing process of the non-oriented electrical steel sheet is lowered.
Ｓは、ＭｎＳ等の硫化物の微細析出により、熱間圧延後の再結晶および結晶粒成長を阻害し、熱延板焼鈍後の結晶粒径の粗大化、およびこれに伴う熱延板集合組織のランダム化を阻むので、０．００２％以下とする。 S inhibits recrystallization and grain growth after hot rolling due to fine precipitation of sulfides such as MnS, coarsening of crystal grain size after hot-rolled sheet annealing, and accompanying hot-rolled sheet texture Therefore, the content is made 0.002% or less.
Ｎは、ＡｌＮをはじめＴｉＮ等の窒化物の微細析出により、熱間圧延後の再結晶および結晶粒成長を阻害し、熱延板焼鈍後の結晶粒径の粗大化、およびこれに伴う熱延板集合組織のランダム化を阻むので、０．００２％以下とする。 N inhibits recrystallization and grain growth after hot rolling due to fine precipitation of nitrides such as TiN as well as AlN, coarsening of the crystal grain size after hot-rolled sheet annealing, and accompanying hot rolling. In order to prevent randomization of the plate texture, the content is made 0.002% or less.
Ｔｉは、再結晶温度を上昇させ、無方向性電磁鋼板の製造工程における焼鈍時に再結晶およびそれに続く結晶粒成長を遅らせる。また、無方向性電磁鋼板の磁気特性にとって好ましくない｛１１１｝集合組織を発達させる。さらに、ＴｉＮやＴｉＣ等の微細析出とも相俟って、熱延板焼鈍後の結晶粒径の粗大化、およびこれに伴う熱延板集合組織のランダム化を阻害するので、０．００２％以下とする。 Ti raises the recrystallization temperature and delays the recrystallization and the subsequent grain growth during annealing in the manufacturing process of the non-oriented electrical steel sheet. In addition, a {111} texture that is undesirable for the magnetic properties of the non-oriented electrical steel sheet is developed. Furthermore, in combination with fine precipitation of TiN, TiC, etc., it inhibits the coarsening of the crystal grain size after the hot-rolled sheet annealing and the randomization of the hot-rolled sheet texture accompanying this, so 0.002% or less And
Ｖ，Ｚｒ，Ｎｂは，ＶＮ，ＶＣ等の炭化物や窒化物の微細析出により、熱間圧延後の再結晶および結晶粒成長を阻害し、熱延板焼鈍後の結晶粒径の粗大化、およびこれに伴う熱延板集合組織のランダム化を阻むので、それぞれ、０．００３％以下とする。 V, Zr, and Nb, due to fine precipitation of carbides and nitrides such as VN and VC, inhibit recrystallization and grain growth after hot rolling, increase the grain size after hot-rolled sheet annealing, and Since randomization of the hot-rolled sheet texture accompanying this is hindered, each is made 0.003% or less.
Ａｓは、それ自身では、本発明の鋼成分範囲内では上述のような微細析出物を形成することはない。ただし、Ａｓが含有されるとＭｎＳ等の硫化物の微細析出を促進し、熱間圧延後の再結晶および結晶粒成長を阻害することとなり、熱延板焼鈍後の結晶粒径の粗大化、およびこれに伴う熱延板集合組織のランダム化を阻むので、０．００３％以下とする。 上述の成分以外は、Ｆｅおよび不可避不純物元素である。 As itself does not form fine precipitates as described above within the steel component range of the present invention. However, when As is contained, the fine precipitation of sulfides such as MnS is promoted, and recrystallization and crystal grain growth after hot rolling will be hindered. In order to prevent randomization of the hot rolled sheet texture accompanying this, the content is made 0.003% or less. Other than the above-described components, Fe and unavoidable impurity elements.
次に、本発明の特徴とする、鋼板の板面内での全周磁気特性変化と回転機鉄心として用いた場合の鉄損との関係について述べる。
表１に示した成分の鋼スラブを用い、熱間圧延条件、熱延板焼鈍条件、冷間圧延条件等を調整し、表２に示した全周磁気特性を有する０．３５ｍｍ厚の６種類の無方向性電磁鋼板を得た。これらの無方向性電磁鋼板を４極モータコアに加工，積層し、モータコア鉄損／素材鉄損の比、すなわちＢＦ（ビルディングファクタ）を測定した。その測定結果を表３に示す。
Next, the relationship between the change in the entire circumference magnetic properties within the plate surface of the steel sheet and the iron loss when used as a rotating machine iron core, which is a feature of the present invention, will be described.
Using steel slabs with the components shown in Table 1, hot rolling conditions, hot rolled sheet annealing conditions, cold rolling conditions, etc. are adjusted, and six types of 0.35 mm thickness having all-around magnetic properties shown in Table 2 A non-oriented electrical steel sheet was obtained. These non-oriented electrical steel sheets were processed and laminated into a 4-pole motor core, and the ratio of motor core iron loss / material iron loss, that is, BF (building factor) was measured. The measurement results are shown in Table 3.
鋼板の製造条件を操作して板面内での全周磁気特性を変化させることにより、｛１００｝＜Ｏｖｗ＞集合組織が発達した場合に得られるような鋼板の板面内すべての方向について均一な磁気特性が必ずしも実現されなくても、モータコア鉄損／素材鉄損の比、すなわちＢＦ（ビルディングファクタ）を低減することができ、回転機鉄心素材として実用上好ましい無方向性電磁鋼板となることがわかる。
特に、圧延方向の磁束密度Ｂ50が１．６９Ｔ以上でその板面内垂直方向との磁束密度Ｂ50差が０．０３Ｔ未満、圧延方向から板面内２２．５度方向の磁束密度Ｂ50が１．６５Ｔ以上で６７．５度方向との磁束密度Ｂ50差が０．０４Ｔ未満、４５度方向との磁束密度Ｂ50差が０．０６Ｔ未満であるＮｏ．６では、著しくＢＦが低く、モータコア素材として優れた無方向性電磁鋼板が実現されている。
Uniform in all directions in the plate surface of the steel plate as obtained when {100} <Ovw> texture develops by manipulating the manufacturing conditions of the steel plate and changing the magnetic properties around the plate surface Even if the magnetic characteristics are not necessarily realized, the ratio of motor core iron loss / material iron loss, that is, BF (building factor) can be reduced, and a non-oriented electrical steel sheet that is practically preferred as a rotating machine core material can be obtained. I understand.
In particular, the magnetic flux density B50 in the rolling direction is 1.69 T or more, the magnetic flux density B50 difference from the vertical direction in the plate surface is less than 0.03 T, and the magnetic flux density B50 in the 22.5 degree direction in the plate surface from the rolling direction is 1. The magnetic flux density B50 difference with the direction of 67.5 degrees is less than 0.04T at 65T or more, and the magnetic flux density B50 difference with the direction of 45 degrees is less than 0.06T. In No. 6, a non-oriented electrical steel sheet having an extremely low BF and excellent as a motor core material is realized.
このように、本発明の特徴は、鋼板圧延方向磁束密度、およびその板面内垂直方向との磁束密度差、圧延方向から板面内２２．５度方向の磁束密度、および６７．５度方向、４５度方向との磁束密度Ｂ50差を一定範囲に制御することにより、回転機鉄心として用いた場合に実用上優れた鉄損特性を有する無方向性電磁鋼板を提供することにある。 As described above, the present invention is characterized by the magnetic flux density in the rolling direction of the steel sheet, the magnetic flux density difference from the vertical direction in the plate surface, the magnetic flux density in the 22.5 degree direction in the plate surface from the rolling direction, and the 67.5 degree direction. It is intended to provide a non-oriented electrical steel sheet having practically excellent iron loss characteristics when used as a rotating machine iron core by controlling the magnetic flux density B50 difference with respect to the 45 degree direction within a certain range.
この場合、鋼板圧延方向磁束密度Ｂ50は１．６９Ｔ以上とする必要がある。１．６９Ｔ未満では、回転機の使用磁場を下げざるを得ず、またＢＦも増加し鉄損特性が劣化する。 鋼板圧延方向磁束密度Ｂ50とその板面内垂直方向磁束密度Ｂ50との差は０．０３Ｔ未満とする必要がある。０．０３Ｔ以上の差ではＢＦが増加する。
さらに、圧延方向から板面内２２．５度方向の磁束密度Ｂ50は１．６５Ｔ以上とする必要がある。１．６５Ｔ未満では、回転機の使用磁場を下げざるを得ず、またＢＦも増加し鉄損特性が劣化する。
圧延方向から板面内２２．５度方向の磁束密度Ｂ50と６７．５度方向との磁束密度Ｂ50との差は０．０４Ｔ未満、かつ、４５度方向との磁束密度Ｂ50との差は０．０６Ｔ未満とする必要がある。これらの差がそれぞれ０．０４Ｔ以上，０．０６Ｔ以上では、ＢＦが増加する。尚、本発明に規定した化学成分を有する鋼であれば、以下に述べるような製造条件によって、優れた全周磁気特性を得ることが出来る。
In this case, the steel plate rolling direction magnetic flux density B50 needs to be 1.69 T or more. If it is less than 1.69T, the magnetic field in use of the rotating machine must be lowered, and BF also increases and the iron loss characteristics deteriorate. The difference between the steel plate rolling direction magnetic flux density B50 and the in-plate vertical magnetic flux density B50 needs to be less than 0.03T. BF increases with a difference of 0.03T or more.
Furthermore, the magnetic flux density B50 in the 22.5 degree direction in the plate surface from the rolling direction needs to be 1.65 T or more. If it is less than 1.65T, the working magnetic field of a rotating machine must be lowered, and BF also increases and the iron loss characteristics deteriorate.
The difference between the magnetic flux density B50 in the 22.5 degree direction in the plate direction from the rolling direction and the magnetic flux density B50 in the 67.5 degree direction is less than 0.04T, and the difference between the magnetic flux density B50 in the 45 degree direction is 0. Must be less than 06T. When these differences are 0.04T or more and 0.06T or more, BF increases. In addition, if it is steel which has the chemical component prescribed | regulated to this invention, the outstanding all-around magnetic characteristic can be obtained on the manufacturing conditions as described below.
次に、本発明の特徴とする、熱延板焼鈍後の結晶粒径と冷間圧延の圧下率との組み合わせが磁気特性に及ぼす効果について述べる。表４に示した成分の鋼スラブを２．８ｍｍ厚に熱間圧延後、表５に示した焼鈍条件で熱延板焼鈍を施し、熱延板焼鈍後の結晶粒径を変化させ、また、冷間圧延圧下率も変化させ、９００℃で３０秒の仕上焼鈍を施した後、角度別（圧延方向，２２．５度方向，４５度方向，６７．５度方向，圧延方向に垂直方向）にエプスタイン試料を採取し、磁気特性（磁束密度：Ｂ50）を測定した。その測定結果も併せて表５に示す。 Next, the effect of the combination of the crystal grain size after hot-rolled sheet annealing and the cold rolling reduction ratio, which is a feature of the present invention, on the magnetic properties will be described. After hot-rolling a steel slab having the components shown in Table 4 to a thickness of 2.8 mm, it is subjected to hot-rolled sheet annealing under the annealing conditions shown in Table 5, and the crystal grain size after the hot-rolled sheet annealing is changed. After changing the cold rolling reduction ratio and finishing annealing at 900 ° C. for 30 seconds, by angle (rolling direction, 22.5 degree direction, 45 degree direction, 67.5 degree direction, perpendicular direction to the rolling direction) Epstein samples were taken and magnetic properties (magnetic flux density: B50) were measured. The measurement results are also shown in Table 5.
冷間圧延前、すなわち熱延板焼鈍後の平均結晶粒径と冷間圧延の圧下率との組み合わせにより、９００℃で３０秒の短時間連続仕上焼鈍で、板面内全周磁気特性を向上できることがわかる。特に、熱延板焼鈍後の平均結晶粒径を４３８μｍ以上に粗大化させ、かつ、冷間圧延の圧下率を８５％に制御したＮｏ．５では、著しくＢ50（全周平均値）が高く、全周磁気特性の優れた無方向性電磁鋼板が得られる。この場合、熱延板焼鈍後の平均結晶粒径を４３８μｍ以上に粗大化させることにより、熱延板集合組織のランダム化も促進されており、熱延板焼鈍後、すなわち冷間圧延前の平均結晶粒径の粗大化とランダム集合組織が、冷間圧延の圧下率制御との相乗効果により、仕上焼鈍後の｛１００｝集合組織の発達を促進し、板面内全周磁気特性の顕著な向上に寄与しているものと推察される。
このように本発明の特徴は、熱延板焼鈍後の結晶粒径と冷間圧延の圧下率との組み合わせにより、短時間連続仕上焼鈍で、板面内全周磁気特性の優れた無方向性電磁鋼板を製造することにある。
By combining the average grain size before cold rolling, that is, after hot-rolled sheet annealing, and the rolling reduction ratio of cold rolling, short-term continuous finish annealing at 900 ° C for 30 seconds improves the in-plane magnetic properties around the plate surface. I understand that I can do it. In particular, the average grain size after hot-rolled sheet annealing was coarsened to 438 μm or more, and the rolling reduction of cold rolling was controlled to 85%. No. 5, a non-oriented electrical steel sheet having a remarkably high B50 (circumference average value) and excellent all-round magnetic properties can be obtained. In this case, by making the average grain size after hot-rolled sheet annealing coarser to 438 μm or more, randomization of the hot-rolled sheet texture is also promoted, and after hot-rolled sheet annealing, that is, before cold rolling. The coarsening of the average grain size and the random texture promote the development of the {100} texture after finish annealing due to the synergistic effect of the cold rolling reduction ratio control, and the remarkable in-plane magnetic properties in the plate surface It is assumed that it contributes to the improvement.
As described above, the feature of the present invention is that the combination of the crystal grain size after hot-rolled sheet annealing and the reduction ratio of cold rolling is a short-time continuous finish annealing and excellent non-directionality in the in-plane circumferential magnetic properties. It is to manufacture an electromagnetic steel sheet.
熱延板焼鈍後の平均結晶粒径は４３８μｍ以上にする必要がある。熱延板平均結晶粒径が４３８ｍｍ未満では、冷間圧延の圧下率を制御しても板面内全周磁気特性を向上させることはできない。なお、本発明に規定した鋼の不純物元素含有量であれば、熱延板焼鈍条件、すなわち焼鈍温度と時間を、無方向性電磁鋼板の通常の製造工程範囲内で適宜選定することにより、熱延板焼鈍後の平均結晶粒径を４３８μｍ以上にすることができる。 The average crystal grain size after hot-rolled sheet annealing needs to be 438 μm or more. If the average grain size of hot-rolled sheet is less than 438 mm, the in-plane circumferential magnetic properties cannot be improved even if the rolling reduction of cold rolling is controlled. In addition, if the impurity element content of the steel specified in the present invention, the hot-rolled sheet annealing conditions, that is, the annealing temperature and time are appropriately selected within the normal manufacturing process range of the non-oriented electrical steel sheet. The average crystal grain size after the sheet annealing can be set to 438 μm or more.
冷間圧延の圧下率は、８０％以上９０％以下とする。８０％未満では、磁気特性の異方性が大きくなり、板面内全周磁気特性が向上しない。一方９０％超では、磁気特性の異方性は減少するものの、無方向性電磁鋼板の磁気特性にとって好ましくない｛１１１｝集合組織が発達し、磁束密度が低下する。 The rolling reduction of cold rolling is 80% or more and 90% or less. If it is less than 80%, the magnetic property anisotropy becomes large, and the in-plane circumferential magnetic property is not improved. On the other hand, if it exceeds 90%, the magnetic property anisotropy decreases, but a {111} texture unfavorable for the magnetic property of the non-oriented electrical steel sheet develops, and the magnetic flux density decreases.
仕上焼鈍は８００℃以上９５０℃以下で１０秒以上１分以下とする。８００℃未満では、磁気特性の異方性が大きくなり、板面内全周磁気特性が向上しない。一方、９５０℃超では、磁気特性の異方性は減少するものの、無方向性電磁鋼板の磁気特性にとって好ましくない｛１１１｝集合組織が発達し、磁束密度が低下する。また１０秒未満では、結晶粒の整粒性が悪く、磁束密度の低下や鉄損の増加を招く。一方１分超では、その効果は飽和し、かつ生産性の低下や製造コストの上昇をも招く。 Finish annealing is performed at 800 ° C. or more and 950 ° C. or less for 10 seconds or more and 1 minute or less. If it is less than 800 ° C., the anisotropy of the magnetic characteristics increases, and the in-plane circumferential magnetic characteristics do not improve. On the other hand, if it exceeds 950 ° C., the magnetic property anisotropy decreases, but a {111} texture unfavorable for the magnetic properties of the non-oriented electrical steel sheet develops, and the magnetic flux density decreases. If the time is less than 10 seconds, the crystal grain size is poor, leading to a decrease in magnetic flux density and an increase in iron loss. On the other hand, if it exceeds 1 minute, the effect is saturated, and the productivity is lowered and the manufacturing cost is increased.
なお、本発明の特徴とする化学成分を有する鋼は、転炉あるいは電気炉等で溶製され、連続鋳造あるいは造塊後の分塊圧延によりスラブとされた後、上記の熱間圧延以降の処理が施される。 In addition, the steel having the chemical component characterized by the present invention is melted in a converter or an electric furnace, and is made into a slab by continuous rolling or ingot rolling after ingot forming, and then after the above hot rolling. Processing is performed.
次に本発明の実施例を示す。
（実施例１）
表６に示した成分を含有し、表７に示した全周磁気特性を有する０．５０ｍｍ厚の無方向性電磁鋼板を８極モータコアに加工，積層し、モータコア鉄損／素材鉄損の比、すなわちＢＦ（ビルディングファクタ）を測定した。その測定結果も併せて表７に示す。
Next, examples of the present invention will be described.
Example 1
A non-oriented electrical steel sheet of 0.50 mm thickness containing the components shown in Table 6 and having the entire circumference magnetic properties shown in Table 7 is processed and laminated into an 8-pole motor core, and the ratio of motor core iron loss / material iron loss That is, BF (building factor) was measured. The measurement results are also shown in Table 7.
表７において、比較例のＮｏ．１１および１２は、所定の全周磁気特性、すなわち、圧延方向の磁束密度Ｂ50が１．６９Ｔ以上でその板面内垂直方向との磁束密度Ｂ50差が０．０３Ｔ未満、圧延方向から板面内２２．５度方向の磁束密度Ｂ50が１．６５Ｔ以上で６７．５度方向との磁束密度Ｂ50差が０．０４Ｔ未満、４５度方向との磁束密度Ｂ50差が０．０６Ｔ未満の条件のいずれかを満たさないため、ＢＦが大きい。
また、比較例のＮｏ．１４，１５および１６は、所定の全周磁気特性を満たさないためＢＦが大きい。特に、Ｓｉ＋２Ａｌ−Ｍｎが２％未満であるため、｛１００｝＜Ｏｖｗ＞集合組織の発達が難しくなっており、ＢＦの増加を助長している。
それに対して本発明例のＮｏ．１３は、所定の全周磁気特性を満足しているため素材鉄損が低いとともに、ＢＦも著しく低い。
このように、本発明により、回転機鉄心として用いた場合に優れた鉄損特性が得られる全周磁気特性に優れた無方向性電磁鋼板を提供できることがわかる。
In Table 7, No. of the comparative example. Nos. 11 and 12 are predetermined circumferential magnetic characteristics, that is, the magnetic flux density B50 in the rolling direction is 1.69 T or more and the difference in magnetic flux density B50 from the vertical direction in the plate surface is less than 0.03 T. Any of the conditions where the magnetic flux density B50 in the 22.5 degree direction is 1.65T or more and the magnetic flux density B50 difference with the 67.5 degree direction is less than 0.04T and the magnetic flux density B50 difference with the 45 degree direction is less than 0.06T. Since BF is not satisfied, BF is large.
Moreover, No. of the comparative example. 14, 15 and 16 have a large BF because they do not satisfy the predetermined circumferential magnetic characteristics. In particular, since Si + 2Al—Mn is less than 2%, it is difficult to develop a {100} <Ovw> texture, which promotes an increase in BF.
On the other hand, No. of the present invention example. No. 13 satisfies the predetermined all-round magnetic characteristics, so that the material iron loss is low and the BF is remarkably low.
Thus, according to the present invention, it can be seen that a non-oriented electrical steel sheet excellent in all-around magnetic characteristics that can provide excellent iron loss characteristics when used as a rotating machine core can be provided.
（実施例２）
表８に示した成分を含有し、表９に示した全周磁気特性を有する０．３５ｍｍ厚の無方向性電磁鋼板を４極モータコアに加工，積層し、モータコア鉄損／素材鉄損の比、すなわちＢＦ（ビルディングファクタ）を測定した。その測定結果も併せて表９に示す。
(Example 2)
A non-oriented electrical steel sheet having a thickness of 0.35 mm containing the components shown in Table 8 and having the entire magnetic properties shown in Table 9 is processed and laminated on a 4-pole motor core, and the ratio of motor core iron loss / material iron loss That is, BF (building factor) was measured. The measurement results are also shown in Table 9.
表９において、比較例のＮｏ．２１〜２４は、所定の全周磁気特性、すなわち、圧延方向の磁束密度Ｂ50が１．６９Ｔ以上でその板面内垂直方向との磁束密度Ｂ50差が０．０３Ｔ未満、圧延方向から板面内２２．５度方向の磁束密度Ｂ50が１．６５Ｔ以上で６７．５度方向との磁束密度Ｂ50差が０．０４Ｔ未満、４５度方向との磁束密度Ｂ50差が０．０６Ｔ未満の条件のいずれかを満たさないため、ＢＦが大きい。
それに対して本発明例のＮｏ．２５は、所定の全周磁気特性を満足しているため、ＢＦが著しく低い。
本発明により、回転機鉄心として用いた場合に優れた鉄損特性が得られる全周磁気特性に優れた無方向性電磁鋼板を提供できることがわかる。
In Table 9, No. of the comparative example. Nos. 21 to 24 have predetermined circumferential magnetic characteristics, that is, the magnetic flux density B50 in the rolling direction is 1.69 T or more and the magnetic flux density B50 difference from the vertical direction in the plate surface is less than 0.03 T. Any of the conditions where the magnetic flux density B50 in the 22.5 degree direction is 1.65T or more and the magnetic flux density B50 difference with the 67.5 degree direction is less than 0.04T and the magnetic flux density B50 difference with the 45 degree direction is less than 0.06T. Since BF is not satisfied, BF is large.
On the other hand, No. of the present invention example. No. 25 satisfies a predetermined all-round magnetic characteristic, so BF is remarkably low.
By this invention, it turns out that the non-oriented electrical steel sheet excellent in the perimeter magnetic characteristic from which the excellent iron loss characteristic is obtained when it uses as a rotary machine core can be provided.
（実施例３）
表１０に示した成分の鋼を、１．５ｍｍ厚、２．７ｍｍ厚、４．２ｍｍ厚にそれぞれ熱間圧延後、１０００℃で２分間の熱延板焼鈍を施し、０．３５ｍｍ厚に冷間圧延した後、８５０℃で３０秒の仕上焼鈍を施した。その後、角度別（圧延方向，２２．５度方向，４５度方向，６７．５度方向，圧延方向に垂直方向）にエプスタイン試料を採取し、磁気特性を測定した。その測定結果を表１１に示す。なお、磁気特性の全周平均値は、（圧延方向＋２・２２．５度方向＋２・４５度方向＋２・６７．５度方向＋圧延方向に垂直方向）／８により求めた。
本発明により、板面内全周磁気特性の優れた無方向性電磁鋼板の製造が可能であることがわかる。
(Example 3)
Steels having the components shown in Table 10 were hot-rolled to 1.5 mm thickness, 2.7 mm thickness, and 4.2 mm thickness, respectively, and then subjected to hot-rolled sheet annealing at 1000 ° C. for 2 minutes, and then cooled to 0.35 mm thickness. After hot rolling, finish annealing was performed at 850 ° C. for 30 seconds. Thereafter, Epstein samples were taken for each angle (rolling direction, 22.5 degree direction, 45 degree direction, 67.5 degree direction, perpendicular to the rolling direction), and the magnetic properties were measured. The measurement results are shown in Table 11. The average value of the entire circumference of the magnetic properties was obtained by (rolling direction + 2-22.5 degree direction + 2.45 degree direction + 2.67.5 degree direction + direction perpendicular to the rolling direction) / 8.
By this invention, it turns out that manufacture of the non-oriented electrical steel sheet excellent in the in-plate all-around magnetic characteristic is possible.
（実施例４）
表１２に示した成分の鋼を、３．３ｍｍ厚に熱間圧延後、１０２０℃で２分間の熱延板焼鈍を施し、０．５０ｍｍ厚に冷間圧延（冷間圧延の圧下率：８４．８％）した後、９３０℃で４０秒の仕上焼鈍を施し、その後、角度別（圧延方向，２２．５度方向，４５度方向，６７．５度方向，圧延方向に垂直方向）にエプスタイン試料を採取し、磁気特性を測定した。その測定結果を表１３に示す。なお、磁気特性の全周平均値は、（圧延方向＋２・２２．５度方向＋２・４５度方向＋２・６７．５度方向＋圧延方向に垂直方向）／８により求めた。
本発明により、板面内全周磁気特性の優れた無方向性電磁鋼板が得られることがわかる。
(Example 4)
The steel having the components shown in Table 12 was hot-rolled to a thickness of 3.3 mm, subjected to hot-rolled sheet annealing at 1020 ° C. for 2 minutes, and then cold-rolled to a thickness of 0.50 mm (cold rolling reduction ratio: 84 8%), and then annealed at 930 ° C. for 40 seconds, and then Epstein by angle (rolling direction, 22.5 degrees direction, 45 degrees direction, 67.5 degrees direction, perpendicular to the rolling direction). A sample was taken and the magnetic properties were measured. The measurement results are shown in Table 13. The average value of the entire circumference of the magnetic properties was obtained by (rolling direction + 2-22.5 degree direction + 2.45 degree direction + 2.67.5 degree direction + direction perpendicular to the rolling direction) / 8.
According to the present invention, it can be seen that a non-oriented electrical steel sheet having excellent in-plane magnetic properties can be obtained.
Claims (5)
Ｃ ：０．００２％以下、 Ｓｉ：０．８％以上４．０％以下、
Ａｌ：０．１％以上２．０以下、 Ｍｎ：０．１％以上１．５％以下
を含有し、かつ、
Ｓｉ＋２Ａｌ−Ｍｎ：２％以上で、
残部Ｆｅおよび不可避不純物元素よりなる鋼であり、熱延板焼鈍後の平均結晶粒径を４３８μｍ以上とし、冷間圧延を圧下率８０％以上９０％以下で施すものであって、圧延方向の磁束密度Ｂ50が１．６９Ｔ以上でその板面内垂直方向の磁束密度Ｂ50との差が０．０３Ｔ未満であり、また圧延方向から板面内２２．５度方向の磁束密度Ｂ50が１．６５Ｔ以上で６７．５度方向の磁束密度Ｂ50との差が０．０４Ｔ未満であり、かつ、４５度方向の磁束密度Ｂ50との差が０．０６Ｔ未満であることを特徴とする無方向性電磁鋼板。 % By mass
C: 0.002% or less, Si: 0.8% or more and 4.0% or less,
Al: 0.1% or more and 2.0 or less, Mn: 0.1% or more and 1.5% or less, and
Si + 2Al-Mn: 2% or more,
It is a steel composed of the remaining Fe and inevitable impurity elements, the average grain size after hot-rolled sheet annealing is set to 438 μm or more, and cold rolling is performed at a rolling reduction of 80% or more and 90% or less. The magnetic flux density B50 is 1.69T or more, the difference from the magnetic flux density B50 in the vertical direction in the plate surface is less than 0.03T, and the magnetic flux density B50 in the 22.5 degree direction in the plate surface from the rolling direction is 1.65T. The non-directional electromagnetic wave characterized in that the difference from the magnetic flux density B50 in the 67.5 degree direction is less than 0.04T and the difference from the magnetic flux density B50 in the 45 degree direction is less than 0.06T. steel sheet.
Ｓｎ：０．０２〜０．４０％、 Ｃｕ：０．１〜１．０％
の１種または２種を含有することを特徴とする請求項１に記載の無方向性電磁鋼板。 In addition by mass%
Sn: 0.02-0.40%, Cu: 0.1-1.0%
The non-oriented electrical steel sheet according to claim 1, comprising one or two of the following.
Ｃ ：０．００２％以下、 Ｓｉ：０．８％以上４．０％以下、
Ａｌ：０．１％以上２．０以下、 Ｍｎ：０．１％以上１．５％以下
を含有し、かつ、
Ｓｉ＋２Ａｌ−Ｍｎ：２％以上で、
残部Ｆｅおよび不可避不純物元素よりなる鋼を、熱間圧延後、熱延板焼鈍を施し、一回の冷間圧延により最終板厚とした後、仕上焼鈍を施す無方向性電磁鋼板の製造方法において、熱延板焼鈍後の平均結晶粒径を４３８μｍ以上とし、冷間圧延を圧下率：８０％以上９０％以下で施し、仕上焼鈍を８００℃以上９５０℃以下で１０秒以上１分以下施すことを特徴とする無方向性電磁鋼板の製造方法。 % By mass
C: 0.002% or less, Si: 0.8% or more and 4.0% or less,
Al: 0.1% or more and 2.0 or less, Mn: 0.1% or more and 1.5% or less, and
Si + 2Al-Mn: 2% or more,
In the method for producing a non-oriented electrical steel sheet, the steel comprising the remaining Fe and inevitable impurity elements is subjected to hot rolling, followed by hot-rolled sheet annealing, the final sheet thickness is obtained by a single cold rolling, and then finish annealing. The average grain size after hot-rolled sheet annealing is set to 438 μm or more, cold rolling is performed at a reduction ratio of 80% to 90%, and finish annealing is performed at 800 ° C. to 950 ° C. for 10 seconds to 1 minute. The manufacturing method of the non-oriented electrical steel sheet characterized by the above-mentioned.
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| JP5025942B2 (en) * | 2005-03-14 | 2012-09-12 | 新日本製鐵株式会社 | Method for producing non-oriented electrical steel sheet |
| JP4790537B2 (en) * | 2006-08-10 | 2011-10-12 | 新日本製鐵株式会社 | Method for producing non-oriented electrical steel sheet with all-around characteristics and good workability |
| BR112013002583B1 (en) | 2010-08-04 | 2018-07-10 | Nippon Steel & Sumitomo Metal Corporation | METHOD OF MANUFACTURING STEEL PLATE FOR NON-ORIENTED GRAIN ELECTRICAL PURPOSES |
| JP5533958B2 (en) * | 2012-08-21 | 2014-06-25 | Ｊｆｅスチール株式会社 | Non-oriented electrical steel sheet with low iron loss degradation by punching |
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| CN110573640B (en) | 2017-06-02 | 2021-08-13 | 日本制铁株式会社 | Non-oriented electromagnetic steel sheet |
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