JP4272576B2 - Method for producing non-oriented electrical steel sheet with high magnetic flux density - Google Patents
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- 229910000565 Non-oriented electrical steel Inorganic materials 0.000 title claims description 13
- 238000004519 manufacturing process Methods 0.000 title claims description 8
- 230000004907 flux Effects 0.000 title description 21
- 229910000831 Steel Inorganic materials 0.000 claims description 20
- 239000010959 steel Substances 0.000 claims description 20
- 238000002441 X-ray diffraction Methods 0.000 claims description 10
- 229910001208 Crucible steel Inorganic materials 0.000 claims description 9
- 239000013078 crystal Substances 0.000 claims description 9
- 238000000137 annealing Methods 0.000 claims description 5
- 238000001816 cooling Methods 0.000 claims description 4
- 239000012535 impurity Substances 0.000 claims description 2
- 238000005097 cold rolling Methods 0.000 description 37
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 12
- 238000005096 rolling process Methods 0.000 description 9
- 238000000034 method Methods 0.000 description 7
- 229910052742 iron Inorganic materials 0.000 description 5
- 238000005266 casting Methods 0.000 description 4
- 229910000859 α-Fe Inorganic materials 0.000 description 4
- 229910001566 austenite Inorganic materials 0.000 description 2
- 230000009931 harmful effect Effects 0.000 description 2
- 238000007712 rapid solidification Methods 0.000 description 2
- 229910052797 bismuth Inorganic materials 0.000 description 1
- JCXGWMGPZLAOME-UHFFFAOYSA-N bismuth atom Chemical compound [Bi] JCXGWMGPZLAOME-UHFFFAOYSA-N 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 150000003568 thioethers Chemical class 0.000 description 1
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Description
本発明は、全周方向の磁束密度が極めて高く、鉄損が低い無方向性電磁鋼板を得られる製造方法を提供するものである。 The present invention provides a manufacturing method capable of obtaining a non-oriented electrical steel sheet having extremely high magnetic flux density in the entire circumferential direction and low iron loss.
無方向性電磁鋼板は、大型発電機、モータ、音響機器用や安定器などの小型静止器に使用される。図1に鋼板の板取りを示すが、小、中型モータの一体コアでは磁路は全周方向となり、これらのような用途の場合、全周方向の磁束密度が高く鉄損が低い、磁気特性が優れた無方向性電磁鋼板が求められる。 Non-oriented electrical steel sheets are used for small stationary devices such as large generators, motors, acoustic equipment and ballasts. Fig. 1 shows the stripping of a steel plate, but the magnetic path of the small and medium-sized motor integrated core is in the entire circumferential direction. In such applications, the magnetic flux density in the circumferential direction is high and the iron loss is low. Is required.
全周方向の磁束密度の高い無方向性電磁鋼板の製造方法の一つに急冷凝固法がある。すなわち、移動更新する冷却体表面によって溶鋼を凝固せしめて鋳造鋼帯とし、次いで該当鋳造鋼帯を冷間圧延して所定の厚さとした後、仕上焼鈍して無方向性電磁鋼板を得る方法である。特許文献1、特許文献2には、急冷凝固鋳片の中心層の{100}面X線回折強度を対ランダム試料で2.3倍以上とし、冷間圧延の圧下率を5〜40%とすることを特徴とする磁束密度の高い無方向性電磁鋼板の製造方法が提案されている。
しかしながら近年、省エネルギー、省資源が求められるなか、小、中型モータの一体コアでは全周方向の磁束密度の更に高い鋼板が求められるようになり、上記特許文献1、2に記載の方法よりも更に磁束密度が高い無方向性電磁鋼板が求められていた。また急冷凝固鋳片は大変もろく、常温で圧延すると割れが発生する場合があった。
そこで本発明は、上記の課題を有利に解決して、全周方向の磁束密度の高い無方向性電磁鋼板を、冷間圧延時に割れなく製造する方法を提供することを目的とするものである。
However, in recent years, energy saving and resource saving are demanded, and a steel plate having a higher magnetic flux density in the entire circumferential direction has been demanded for an integrated core of small and medium-sized motors, which is more than the methods described in Patent Documents 1 and 2 above. A non-oriented electrical steel sheet having a high magnetic flux density has been demanded. Moreover, the rapidly solidified slab is very fragile and sometimes cracked when rolled at room temperature.
Then, this invention solves said subject advantageously, and it aims at providing the method of manufacturing a non-oriented electrical steel sheet with a high magnetic flux density of all the circumference directions without a crack at the time of cold rolling. .
本発明の要旨は下記のとおりである。
(1) 質量%で、
C :0.008%以下、 Mn:0.02〜1.0%、
S :0.005%以下、 N :0.01%以下
を含有し、かつ、SiとAlを1.8%≦(Si+2×Al)≦7%
の関係を満たす範囲で含有し、残部Fe及び不可避的不純物よりなる溶鋼を、移動更新する冷却体表面によって凝固せしめて鋳造鋼帯とし、その際の溶鋼の過熱度(鋳造時の溶鋼温度−溶鋼の液相線温度)を70℃以上とすることで、鋳片全厚を柱状晶とし、次いで、該鋳造鋼帯の鋳片厚中心層での鋳片の表面に平行な{100}面のX線回折強度が対ランダム試料で4倍以上の鋳造鋼帯を、180〜350℃の温度域で、かつ、圧下率15〜40%で冷間圧延して所定の厚さとし、さらに仕上焼鈍することを特徴とする、無方向性電磁鋼板の製造方法。
The gist of the present invention is as follows.
(1) In mass%,
C: 0.008% or less, Mn: 0.02-1.0%,
S: 0.005% or less, N: 0.01% or less, and Si and Al 1.8% ≦ (Si + 2 × Al) ≦ 7%
The molten steel consisting of the balance Fe and inevitable impurities is solidified by the surface of the moving cooling body to form a cast steel strip, and the superheat of the molten steel at that time (molten steel temperature at casting-molten steel) The liquidus temperature) is 70 ° C. or more, so that the total slab thickness becomes columnar crystals, and then the {100} plane parallel to the slab surface at the slab thickness center layer of the cast steel strip A cast steel strip whose X-ray diffraction intensity is 4 times or more of a random sample is cold-rolled to a predetermined thickness in a temperature range of 180 to 350 ° C. and at a reduction rate of 15 to 40%, and further subjected to finish annealing. The manufacturing method of the non-oriented electrical steel sheet characterized by the above-mentioned .
本発明によれば、小、中型モータの一体コアなど、全周方向を使用する鉄心に、冷間圧延で割れがなく、磁束密度が高く、鉄損の低い無方向性電磁鋼板を提供できる。 ADVANTAGE OF THE INVENTION According to this invention, the non-oriented electrical steel sheet which does not have a crack by cold rolling, has a high magnetic flux density, and a low iron loss can be provided in the iron core which uses the whole circumferential direction, such as the integral core of a small and a medium-sized motor.
以下、本発明の詳細について説明する。
本発明者らは冷間圧延で割れがなく、磁束密度の高い無方向性電磁鋼板用の製造方法を開発すべく鋭意研究を重ねた結果、急冷凝固法において、鋳造鋳片の組織、集合組織と冷延率、冷間圧延温度を狭い範囲に制御することが非常に有効であることを見出した。
Details of the present invention will be described below.
As a result of intensive research to develop a manufacturing method for a non-oriented electrical steel sheet having a high magnetic flux density without cracking by cold rolling, the present inventors have conducted a rapid solidification method in the structure of a cast slab and a texture. It was found that controlling the cold rolling rate and the cold rolling temperature within a narrow range is very effective.
図2は、本発明者が行なった実験結果の一例である。
C:0.0016〜0.0017%、Si:3.1%、Al:1.2%、Mn:0.24%、S:0.0022〜0.0023%、N:0.0013〜0.0014%を含む溶鋼を、2条件で双ロール法により急冷凝固させ、0.50mm厚の鋳片を作成した。
この時の鋳片1/2層の鋳片の表面に平行な{100}面X線回折強度の対ランダム試料比(以下、ある面のX線回折強度の対ランダム試料比を単に面強度ということもある。)は2.6と4.2であった。
これを0.35mm厚に30%の冷間圧延率で種々の温度で冷間圧延し、1075℃×30秒の仕上焼鈍を行い、磁気測定した。全周方向のB50は、X度方向のB50をB50−Xとすると、全周B50=[B50−0+B50−90+2×(B50−22.5+B50−45+B50−67.5)]/8により求めた。
FIG. 2 is an example of experimental results conducted by the present inventors.
C: 0.0016 to 0.0017%, Si: 3.1%, Al: 1.2%, Mn: 0.24%, S: 0.0022 to 0.0023%, N: 0.0013 to 0 Molten steel containing .0014% was rapidly solidified by a twin roll method under two conditions to produce a 0.50 mm thick slab.
The ratio of {100} plane X-ray diffraction intensity to random sample parallel to the surface of the slab of the slab 1/2 layer at this time (hereinafter, the ratio of X-ray diffraction intensity to random sample of a certain surface is simply referred to as surface strength) Was 2.6 and 4.2.
This was cold-rolled to a thickness of 0.35 mm at various temperatures at a cold rolling rate of 30%, subjected to finish annealing at 1075 ° C. for 30 seconds, and magnetically measured. The entire circumferential direction of B 50, when the X degree direction B 50 and B 50 -X, all around B 50 = [B 50 -0 + B 50 -90 + 2 × (B 50 -22.5 + B 50 -45 + B 50 -67. 5)] / 8.
この時の冷間圧延温度と全周方向の磁束密度B50、冷間圧延時の耳割れ深さを図2に示す。これより、冷間圧延温度を高めると耳割れ深さが小さくなり、180℃以上で耳割れがなくなる。そして180℃以上で冷間圧延すると、{100}面強度が4.2の鋳片では、20℃の常温で冷間圧延するよりも0.01T磁束密度が高くなることが分かる。 {100}面強度が2.6の鋳片では磁束密度の向上は小さい。 FIG. 2 shows the cold rolling temperature at this time, the magnetic flux density B 50 in the entire circumferential direction, and the ear crack depth during cold rolling. From this, when the cold rolling temperature is raised, the depth of the ear cracks becomes small, and the ear cracks disappear at 180 ° C. or higher. And when it cold-rolls above 180 degreeC, it turns out that a 0.01T magnetic flux density becomes high in the slab whose {100} plane intensity | strength is 4.2 compared with cold rolling at normal temperature of 20 degreeC. In the slab with {100} plane strength of 2.6, the improvement in magnetic flux density is small.
図3には、図2に実験の{100}面強度が4.2の0.50mm厚の鋳片を常温の20℃と220℃で種々冷間圧延率で冷間圧延し、1075℃×30秒の仕上焼鈍を行い、全周方向の磁束密度B50を評価した。そして、冷間圧延率とΔ全周B50(全周B50・220℃冷延−全周B50・20℃冷延)の関係を図3に示す。
これより、冷間圧延率が15〜40%の場合に冷間圧延を220℃とすると、常温の20℃の場合よりも磁束密度が高くなることが分かる。
鋳片の{100}面強度が4以上、冷間圧延温度が180〜350℃、冷間圧延率が15〜40%の場合に高い全周の磁束密度を得られる理由は、未解明の部分もあるが次のように考えている。
FIG. 3 shows a 0.50 mm-thick slab having an experimental {100} plane strength of 4.2 in FIG. 2 and is cold-rolled at various cold rolling rates at 20 ° C. and 220 ° C. at room temperature. Finish annealing was performed for 30 seconds, and the magnetic flux density B 50 in the entire circumferential direction was evaluated. FIG. 3 shows the relationship between the cold rolling rate and the Δ whole circumference B 50 (cold rolling of the entire circumference B 50 · 220 ° C.−cold rolling of the whole circumference B 50 · 20 ° C.).
From this, it can be seen that when the cold rolling rate is 15 to 40% and the cold rolling is set to 220 ° C., the magnetic flux density becomes higher than that at the normal temperature of 20 ° C.
The reason why high magnetic flux density can be obtained when the {100} surface strength of the slab is 4 or more, the cold rolling temperature is 180 to 350 ° C., and the cold rolling rate is 15 to 40% is an unexplained part However, I think as follows.
図4には、C:0.0011〜0.0013%、Si:3.1%、Al:1.1%、Mn:0.26%、S:0.0022〜0.0026%、N:0.0013〜0.0016%を含む溶鋼を双ロール法により急冷凝固し、1.6mm厚の鋳片を作成し、{100}面強度が6.4倍と1.3倍の試料の鋳片の凝固組織を示す。
6.4倍の試料は表面から中心層に伸びた柱状晶が非常によく発達しているのに対し、1.3倍の試料は柱状晶は殆ど認められず、球状の等軸晶が多数認められる。
In FIG. 4, C: 0.0011 to 0.0013%, Si: 3.1%, Al: 1.1%, Mn: 0.26%, S: 0.0022 to 0.0026%, N: A molten steel containing 0.0013 to 0.0016% is rapidly solidified by a twin roll method to produce a cast piece having a thickness of 1.6 mm, and casting of a specimen whose {100} surface strength is 6.4 times and 1.3 times. The solidified structure of a piece is shown.
In the 6.4-fold sample, columnar crystals extending from the surface to the central layer are very well developed, whereas in the 1.3-fold sample, almost no columnar crystals are observed, and many spherical equiaxed crystals are present. Is recognized.
これより、できるだけ柱状晶を発達させ、鋳片の集合組織を{100}<0vw>richとすることが非常に重要であると判断される。冷間圧延温度を180〜350℃とすると冷間圧延時の耳割れが少なくなることから、冷間圧延時の変形モードが変化し、鋳片の集合組織を{100}<0vw>richが冷間圧延で温存され、冷間圧延率を15〜40%については、冷間圧延率が15%未満では圧下率が低すぎ、冷間圧延を180〜350℃で行っても効果が小さすぎ、圧下率が40%超では、圧下率が大きすぎ鋳片の集合組織を{100}<0vw>richが温存されなくなってしまうと考えている。 From this, it is judged that it is very important to develop columnar crystals as much as possible and to set the texture of the slab to {100} <0vw> rich. When the cold rolling temperature is set to 180 to 350 ° C., ear cracks during cold rolling are reduced, so that the deformation mode during cold rolling changes, and the texture of the slab is cooled by {100} <0vw> rich. Preserved by cold rolling, and with a cold rolling rate of 15 to 40%, if the cold rolling rate is less than 15%, the reduction rate is too low, and even if cold rolling is performed at 180 to 350 ° C., the effect is too small, If the rolling reduction is over 40%, the rolling reduction is too large and {100} <0vw> rich is not preserved in the texture of the slab.
以下に本発明の成分限定理由を説明する。
Cは、オーステナイト、フェライト2相域とせず、フェライト1相とし、柱状晶をできるだけ発達させるため0.008%以下とした。
The reasons for limiting the components of the present invention will be described below.
C is not an austenite / ferrite two-phase region but a ferrite one phase, and is made 0.008% or less in order to develop columnar crystals as much as possible.
Si+2×Al:Si+2×Alが1.8%以上でかつCが0.008%以下であれば、オーステナイト、フェライト2相域とならずフェライト1相となるため、柱状晶が発達しやすい。更に、Si+2×Alが7%を超えると冷延性が劣化するため、上限は7%とした。 Si + 2 × Al: If Si + 2 × Al is 1.8% or more and C is 0.008% or less, austenite and ferrite do not become a two-phase region but a ferrite one phase, and columnar crystals are likely to develop. Furthermore, if Si + 2 × Al exceeds 7%, the cold rolling property deteriorates, so the upper limit was made 7%.
Mnは、脆性を改善するため0.02%以上とする。上限の1%はこれ以上添加すると磁束密度が劣化するためである。 Mn is made 0.02% or more in order to improve brittleness. The upper limit of 1% is because the magnetic flux density is deteriorated if added more than this.
Sは、微細な硫化物をつくり、鉄損に有害な作用を演ずるため、0.005%以下とする。 S is made 0.005% or less in order to produce fine sulfides and play a harmful effect on iron loss.
Nは、AlNなど微細な窒化物をつくり、鉄損に有害な作用を演ずるため、0.01%以下とする。 N forms a fine nitride such as AlN and exerts a harmful effect on iron loss, so is 0.01% or less.
溶鋼は、移動更新する冷却体表面によって凝固せしめて鋳造鋼帯とする。単ロール法、双ロール法などが用いられる。
鋳片厚中心層での鋳片の表面に平行な{100}面X線回折強度を対ランダム試料で4倍以上とする。図2及び図4に示すように、鋳造鋳片に柱状晶をできるだけ発達させ、 {100}面強度を対ランダムで4倍以上とすると高い磁束密度を得られる。
The molten steel is solidified by the surface of the cooling body to be renewed and moved into a cast steel strip. A single roll method, a twin roll method, or the like is used.
The {100} plane X-ray diffraction intensity parallel to the surface of the slab at the slab thickness center layer is set to 4 times or more for the random sample. As shown in FIGS. 2 and 4, a columnar crystal is developed as much as possible in the cast slab, and when the {100} plane strength is 4 times or more relative to random, a high magnetic flux density can be obtained.
{100}面強度を制御するには、溶鋼の過熱度を調整するのが有効である。溶鋼の過熱度は鋳造時の「溶鋼温度−溶鋼の液相線温度」を表し、実施例に示すように過熱度を70℃以上とすると{100}面強度を4倍以上にすることができる。 In order to control the {100} plane strength, it is effective to adjust the degree of superheat of the molten steel. The superheat degree of molten steel represents “molten steel temperature−liquidus temperature of molten steel” at the time of casting. As shown in the examples, when the superheat degree is 70 ° C. or higher, the {100} plane strength can be increased four times or more. .
冷間圧延の圧下率は15〜40%とする。図3に示すように15%未満や40%を超えると高い磁束密度を得られない。
冷間圧延は180〜350℃で行う。図2に示すように180℃より低いと冷間圧延で耳割れが発生し、磁束密度も高くできない。350℃を超えると磁束密度の向上が飽和する。
鋼板の温度を180℃以上にする方法としては、急冷凝固鋳片を180℃以上で鋳造し、それを冷間圧延に供する方法がある。また、電気炉、ガス炉などの外部加熱を利用する方法もある。
The rolling reduction of cold rolling is 15 to 40%. As shown in FIG. 3, a high magnetic flux density cannot be obtained if it is less than 15% or exceeds 40%.
Cold rolling is performed at 180 to 350 ° C. As shown in FIG. 2, when the temperature is lower than 180 ° C., ear cracks are generated by cold rolling, and the magnetic flux density cannot be increased. If it exceeds 350 ° C., the improvement of the magnetic flux density is saturated.
As a method of setting the temperature of the steel plate to 180 ° C. or higher, there is a method of casting a rapidly solidified cast slab at 180 ° C. or higher and subjecting it to cold rolling. There is also a method using external heating such as an electric furnace or a gas furnace.
C:0.0018%、Si:3.0%、Mn:0.21%、Al:1.2%、S:0.0005〜0.0011%、N:0.0012〜0.0020%、を含有する溶鋼を双ロール法により鋳造する際に、過熱度を変更して種々の板厚に鋳造した。この成分系における融点は1490℃である。続いて酸洗し、0.35mmに種々の温度で冷延し、1075℃×30秒の連続焼鈍し、絶縁皮膜を塗布して製品とした。 C: 0.0018%, Si: 3.0%, Mn: 0.21%, Al: 1.2%, S: 0.0005 to 0.0011%, N: 0.0012 to 0.0020%, When casting the molten steel containing bismuth by the twin roll method, the degree of superheat was changed and cast to various plate thicknesses. The melting point in this component system is 1490 ° C. Subsequently, it was pickled, cold-rolled to 0.35 mm at various temperatures, continuously annealed at 1075 ° C. for 30 seconds, and an insulating film was applied to obtain a product.
この時の、鋳片の表面に平行な{100}面X線回折強度の対ランダム試料比、冷間圧延温度、冷延率と冷延板の耳割れ深さ、磁気特性の関係を表1に示す。
これより、{100}面X線回折強度を4倍以上とし、冷間圧延温度を180〜350℃かつ冷延率を15〜40%とすることにより、冷間圧延で耳割れなく、高い磁束密度を得られることが分かる。
Table 1 shows the relationship between the {100} plane X-ray diffraction intensity parallel to the surface of the slab to the random sample ratio, the cold rolling temperature, the cold rolling rate, the depth of the ear cracks in the cold rolled sheet, and the magnetic properties. Shown in
From this, the {100} plane X-ray diffraction intensity is set to 4 times or more, the cold rolling temperature is 180 to 350 ° C., and the cold rolling rate is 15 to 40%. It can be seen that the density can be obtained.
Claims (1)
C :0.008%以下、 Mn:0.02〜1.0%、
S :0.005%以下、 N :0.01%以下
を含有し、かつ、SiとAlを1.8%≦(Si+2×Al)≦7%
の関係を満たす範囲で含有し、残部Fe及び不可避的不純物よりなる溶鋼を、移動更新する冷却体表面によって凝固せしめて鋳造鋼帯とし、その際の溶鋼の過熱度(鋳造時の溶鋼温度−溶鋼の液相線温度)を70℃以上とすることで、鋳片全厚を柱状晶とし、次いで、該鋳造鋼帯の鋳片厚中心層での鋳片の表面に平行な{100}面のX線回折強度が対ランダム試料で4倍以上の鋳造鋼帯を、180〜350℃の温度域で、かつ、圧下率15〜40%で冷間圧延して所定の厚さとし、さらに仕上焼鈍することを特徴とする、無方向性電磁鋼板の製造方法。 % By mass
C: 0.008% or less, Mn: 0.02-1.0%,
S: 0.005% or less, N: 0.01% or less, and Si and Al 1.8% ≦ (Si + 2 × Al) ≦ 7%
The molten steel consisting of the balance Fe and inevitable impurities is solidified by the surface of the moving cooling body to form a cast steel strip, and the superheat of the molten steel at that time (molten steel temperature at casting-molten steel) The liquidus temperature) is 70 ° C. or more, so that the total slab thickness becomes columnar crystals, and then the {100} plane parallel to the slab surface at the slab thickness center layer of the cast steel strip A cast steel strip whose X-ray diffraction intensity is 4 times or more of a random sample is cold-rolled to a predetermined thickness in a temperature range of 180 to 350 ° C. and at a reduction rate of 15 to 40%, and further subjected to finish annealing. The manufacturing method of the non-oriented electrical steel sheet characterized by the above-mentioned .
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US11469018B2 (en) | 2018-02-16 | 2022-10-11 | Nippon Steel Corporation | Non-oriented electrical steel sheet and method for manufacturing non-oriented electrical steel sheet |
KR102448800B1 (en) * | 2018-02-16 | 2022-09-29 | 닛폰세이테츠 가부시키가이샤 | Non-oriented electrical steel sheet, and manufacturing method of non-oriented electrical steel sheet |
US11459632B2 (en) | 2018-02-16 | 2022-10-04 | Nippon Steel Corporation | Non-oriented electrical steel sheet and method for manufacturing non-oriented electrical steel sheet |
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CN105543672B (en) * | 2016-02-23 | 2017-10-31 | 东北大学 | A kind of method for optimizing the high silicon steel cold-reduced sheet template of No yield point |
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