JPH079039B2 - Method for manufacturing good electromagnetic thick plate with uniform magnetic properties in the thickness direction - Google Patents
Method for manufacturing good electromagnetic thick plate with uniform magnetic properties in the thickness directionInfo
- Publication number
- JPH079039B2 JPH079039B2 JP1064734A JP6473489A JPH079039B2 JP H079039 B2 JPH079039 B2 JP H079039B2 JP 1064734 A JP1064734 A JP 1064734A JP 6473489 A JP6473489 A JP 6473489A JP H079039 B2 JPH079039 B2 JP H079039B2
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- rolling
- plate thickness
- thickness direction
- flux density
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Description
【発明の詳細な説明】 （産業上の利用分野） 本発明は板厚方向磁気特性が均一で、低磁場での磁束密
度が高く、かつ、低い保磁力を有する良電磁厚板の製造
方法を提供するものである。DETAILED DESCRIPTION OF THE INVENTION (Industrial field of application) The present invention provides a method for manufacturing a good electromagnetic thick plate having uniform magnetic properties in the plate thickness direction, high magnetic flux density in a low magnetic field, and low coercive force. It is provided.
（従来の技術） 近年最先端科学技術である素粒子研究や医療機器の進歩
に伴って、大型構造物に高い磁気特性を有する部材を使
用する装置が使われ、その磁気特性向上が求められてい
る。直流磁化条件で使用される磁石用、あるいは磁場を
遮蔽するのに必要な磁気シールド用の材料では、低磁場
での高い磁束密度が求められているが、さらに構造物が
巨大化するに従い、使用鋼材の磁気特性のバラツキの少
ない、特に板厚方向磁気特性の均一な鋼材が要求される
ようになった。(Prior art) With the progress of elementary particle research and medical equipment, which are the most advanced science and technology in recent years, a device using a member having high magnetic characteristics in a large structure is used, and its magnetic characteristics are required to be improved. There is. High magnetic flux densities in low magnetic fields are required for materials used for magnets used under DC magnetizing conditions or magnetic shields required to shield magnetic fields. There has been a demand for a steel material with less variation in the magnetic characteristics of the steel material, in particular, a steel material with uniform magnetic characteristics in the plate thickness direction.
磁束密度に優れた電磁鋼板としては、従来から薄板分野
で珪素鋼板、電磁軟鉄板をはじめとする数多くの材料が
提供されているのは公知である。しかし、構造部材とし
て使用するには組立加工及び強度上の問題があり、厚鋼
板を利用する必要が生じてくる。As magnetic steel sheets having excellent magnetic flux density, it has been known that many materials such as silicon steel sheets and electromagnetic soft iron sheets have been conventionally provided in the thin sheet field. However, there are problems in assembling and strength when used as a structural member, and it becomes necessary to use thick steel plates.
これまで電磁厚板としては鈍鉄系成分で製造されてい
る。たとえば、特開昭60-96749号公報が公知である。Up to now, electromagnetic thick plates have been manufactured with blunt iron-based components. For example, JP-A-60-96749 is known.
しかしながら、近年の装置の大型化、能力の向上等に伴
いさらに磁気特性の優れた、特に低磁場、たとえば80A/
mでの磁束密度の高い鋼材開発の要望が強い。従来開発
された鋼材では、80A/mでの低磁場の高い磁束密度が安
定して得られていない。これに加え実用上問題となる使
用鋼材の磁気特性のバラツキ、特に板厚方向磁気特性の
均一性に関する考慮はなされていない。However, with the recent increase in size of devices and improvement in capacity, magnetic properties are even better, especially in low magnetic fields, for example 80 A /
There is a strong demand for the development of steel materials with high magnetic flux density at m. With the steel materials developed so far, a high magnetic flux density with a low magnetic field at 80 A / m has not been stably obtained. In addition to this, no consideration is given to variations in the magnetic properties of the steel used, which is a problem in practical use, and particularly to the uniformity of the magnetic properties in the plate thickness direction.
（発明が解決しようとする課題） 本発明の目的は以上の点を鑑みなされたもので、板厚方
向磁気特性が均一で、低磁場での磁束密度が高く、か
つ、低い保磁力を有する良電磁厚板の製造方法を提供す
ることである。(Problems to be Solved by the Invention) The object of the present invention is made in view of the above points, and is good in that the magnetic properties in the plate thickness direction are uniform, the magnetic flux density in a low magnetic field is high, and the coercive force is low. An object of the present invention is to provide a method for manufacturing an electromagnetic thick plate.
（課題を解決するための手段） 本発明の要旨は次の通りである。(Means for Solving the Problems) The gist of the present invention is as follows.
（１）重量％で、C:0.01％以下、Si:0.02％以下、Mn:0.
20％以下、S:0.010％以下、Cr:0.05％以下、Mo:0.01％
以下、Cu:0.01％以下、Ni:0.1〜2.0％を含有し、Al:0.0
05〜0.040％、Ca:0.0005〜0.01％のうちいずれか一方で
脱酸し、N:0.004％以下、O:0.005％以下、H:0.0002％以
下、残部実質的に鉄からなる鋼組成の鋼片または、鋳片
を950〜1150℃に加熱し、800℃以上で圧延形状比Ａが0.
6以上の圧延パスを１回以上はとる圧延を行ない、引続
き800℃以下で圧下率を10〜35％とする圧延を行ない、
板厚50mm以上の厚板とし、該厚板を600〜750℃の温度で
脱水素熱処理を行なうことを特徴とする板厚方向の磁気
特性の均一な良電磁厚板の製造方法。(1) In% by weight, C: 0.01% or less, Si: 0.02% or less, Mn: 0.
20% or less, S: 0.010% or less, Cr: 0.05% or less, Mo: 0.01%
Below, Cu: 0.01% or less, Ni: containing 0.1 to 2.0%, Al: 0.0
Steel with a steel composition that is deoxidized with one of 05 to 0.040%, Ca: 0.0005 to 0.01%, N: 0.004% or less, O: 0.005% or less, H: 0.0002% or less, and the balance substantially iron. A piece or a cast piece is heated to 950 to 1150 ° C, and the rolling shape ratio A is 0.8 at 800 ° C or higher.
Rolling with 6 or more rolling passes at least once, and then rolling with a rolling reduction of 10 to 35% at 800 ° C or less,
A method for producing a good electromagnetic thick plate having uniform magnetic characteristics in the plate thickness direction, which is characterized in that a plate having a plate thickness of 50 mm or more is subjected to a dehydrogenation heat treatment at a temperature of 600 to 750 ° C.
ただし、 A :圧延形状比 hi：入側板厚（mm） hO：出側板厚（mm） R :圧延ロール半径（mm） （２）板厚50mm以上の厚板を脱水素熱処理後750〜950℃
の温度で焼鈍するかあるいは910〜1000℃の温度で焼準
することを特徴とする（１）記載の板厚方向の磁気特性
の均一な良電磁厚板の製造方法。However, A: Rolling shape ratio h i : Inlet plate thickness (mm) h O : Outlet plate thickness (mm) R: Rolling roll radius (mm) (2) After dehydrogenation heat treatment of plates with a thickness of 50 mm or more 750 to 950 ° C
The method for producing a good electromagnetic thick plate having uniform magnetic properties in the plate thickness direction according to (1), characterized in that the plate is annealed at a temperature of 10 to 1000 ° C.
（３）重量％で、C:0.01％以下、Si:0.02％以下、Mn:0.
20％以下、S:0.010％以下、Cr:0.05％以下、Mo:0.01％
以下、Cu:0.01％以下、Ni:0.1〜2.0％を含有し、Al:0.0
05〜0.040％、Ca:0.0005〜0.01％のうちいずれか一方で
脱酸し、N:0.004％以下、O:0.005％以下、H:0.0002％以
下、残部実質的に鉄からなる鋼組成の鋼片または、鋳片
を950〜1150℃に加熱し、800℃以上で圧延形状比Ａが0.
6以上の圧延パスを１回以上はとる圧延を行ない、引続
き800℃以下で圧下率を10〜35％とする圧延を行ない、
板厚20mm以上50mm未満の厚板とし、該厚板を750〜950℃
の温度で焼鈍するかあるいは910〜1000℃の温度で焼準
することを特徴とする板厚方向の磁気特性の均一な良電
磁厚板の製造方法。(3) C: 0.01% or less, Si: 0.02% or less, Mn: 0.
20% or less, S: 0.010% or less, Cr: 0.05% or less, Mo: 0.01%
Below, Cu: 0.01% or less, Ni: containing 0.1 to 2.0%, Al: 0.0
Steel with a steel composition that is deoxidized with one of 05 to 0.040%, Ca: 0.0005 to 0.01%, N: 0.004% or less, O: 0.005% or less, H: 0.0002% or less, and the balance substantially iron. A piece or a cast piece is heated to 950 to 1150 ° C, and the rolling shape ratio A is 0.8 at 800 ° C or higher.
Rolling with 6 or more rolling passes at least once, and then rolling with a rolling reduction of 10 to 35% at 800 ° C or less,
A plate with a plate thickness of 20 mm or more and less than 50 mm, and the plate is 750 to 950 ° C.
A method for manufacturing a good electromagnetic thick plate having uniform magnetic properties in the plate thickness direction, which is characterized by annealing at a temperature of 10 to 1000 or normalizing at a temperature of 910 to 1000 ° C.
ただし、 A :圧延形状比 hi：入側板厚（mm） hO：出側板厚（mm） R :圧延ロール半径（mm） まず、磁化のプロセスについて述べると、消磁状態の鋼
を磁界の中に入れ、磁界を強めていくと次第に磁区の向
きに変化が生じ、磁界の方向に近い磁区が優勢になり他
の磁区を蚕食併合していく。つまり、磁壁の移動が起こ
る。However, A: Rolling shape ratio h i : Inlet side plate thickness (mm) h O : Outlet side plate thickness (mm) R: Rolling roll radius (mm) First, the magnetization process is described below. , As the magnetic field is strengthened, the direction of the magnetic domain gradually changes, and the magnetic domain close to the direction of the magnetic field becomes dominant, and the other magnetic domains are annealed and eclipsed. That is, the domain wall moves.
さらに磁界が強くなり磁壁の移動が完了すると、次に磁
区全体の磁化方向に向きを変えていく。この磁化プロセ
スの中で低磁場での磁束密度を決めているのは、磁壁の
移動しやすさである。When the magnetic field is further strengthened and the movement of the domain wall is completed, the direction is changed to the magnetization direction of the entire magnetic domain. It is the ease of movement of the domain wall that determines the magnetic flux density in the low magnetic field in this magnetization process.
つまり低磁場で高磁束密度を得るためには、磁壁の移動
を障害するものを極力減らすことであると定性的に言う
ことができる。この観点から従来磁壁の移動の障害とな
る結晶粒の粗大化が重要な技術となっていた（特開昭60
-96749号公報）。That is, it can be qualitatively said that in order to obtain a high magnetic flux density in a low magnetic field, it is necessary to reduce as much as possible the obstacles to the movement of the domain wall. From this point of view, coarsening of crystal grains, which hinders the movement of the domain wall, has been an important technique in the past (Japanese Patent Laid-Open No. 60-58,058).
-96749).
発明者らは、ここにおいて単に結晶粒の粗大化をねらっ
たのでは圧延中の歪分布、温度分布の不均一性により不
可避的に混粒となるため、低磁場で高磁束密度を得なが
ら、特に板厚方向磁気特性を均一にすることが達成困難
であることを見出した。The inventors here simply aim at coarsening of the crystal grains, so that strain distribution during rolling, inevitably mixed grains due to nonuniformity of the temperature distribution, while obtaining a high magnetic flux density in a low magnetic field, In particular, it has been found that it is difficult to achieve uniform magnetic properties in the plate thickness direction.
そこで板厚方向の粒径が均一でやや粗い粒径（粒度No.
で１〜４番）とし、その粒径を板厚各位置でそろえる製
造法を完成したものである。Therefore, the grain size in the plate thickness direction is uniform and slightly coarse (grain size No.
No. 1 to No. 4), and the manufacturing method for adjusting the grain size at each position of the plate thickness is completed.
この方法は比較的低温の加熱を行ない加熱γ粒を板厚方
向にそろえ、さらに800℃以下で軽圧下を加えることで
適当な粒成長をはかるものである。その結果巨大粒を得
るのではなく、やや粗粒な板厚方向に均一な粒径を得る
ことができる。In this method, heating is performed at a relatively low temperature, the heated γ grains are aligned in the plate thickness direction, and a light reduction is applied at 800 ° C or less to achieve proper grain growth. As a result, rather than obtaining huge grains, it is possible to obtain a slightly coarse grain having a uniform grain size in the plate thickness direction.
そして、この800℃以下の軽圧下で導入された集合組織
により、磁区の方向をそろえ、低磁場での磁壁の移動を
容易とし、磁気特性を向上させる。The texture introduced under the light pressure of 800 ° C. or less aligns the directions of the magnetic domains, facilitates the movement of the domain wall in a low magnetic field, and improves the magnetic characteristics.
第１図に0.01C−0.06Mn−0.020Al鋼での800℃以下の圧
下率と80A/mでの磁束密度及び磁束密度のバラツキを示
す。Fig. 1 shows the rolling reduction of 0.01C-0.06Mn-0.020Al steel below 800 ° C and the magnetic flux density at 80A / m and the variation of the magnetic flux density.
10〜35％の軽圧下により、高磁束密度と板厚方向の磁束
密度の均一性が得られる。With a light reduction of 10 to 35%, high magnetic flux density and uniformity of magnetic flux density in the plate thickness direction can be obtained.
さらに低磁場での高磁束密度を得るための手段として、
内部応力の原因となる元素及び空隙性欠陥の作用につき
詳細な検討を行ない、所期の目的を達成した。As a means for obtaining a high magnetic flux density in a low magnetic field,
The elements that cause internal stress and the action of void defects were studied in detail, and the intended purpose was achieved.
まず、磁壁移動を妨げるAlNを減少するため、Al,Nを低
下すること、特にAl無添加（Al＜0.005％）にすること
が望ましい。内部応力減少のための元素の影響として
は、Ｃの低下が必要である。First, in order to reduce AlN that hinders domain wall movement, it is desirable to reduce Al, N, especially to add no Al (Al <0.005%). As an effect of the element for reducing the internal stress, it is necessary to reduce C.
第２図に示す0.01Si−0.1Mn−0.01Al鋼にあってＣ含有
量の増加につれ低磁場（80A/m）での磁束密度が低下し
ている。In the 0.01Si-0.1Mn-0.01Al steel shown in Fig. 2, the magnetic flux density at a low magnetic field (80A / m) decreases as the C content increases.
また、空隙性欠陥の影響についても種々検討した結果、
そのサイズが100μ以上のものが磁気特性を大幅に低下
することを知見したものである。そしてこの100μ以上
の有害な空隙性欠陥をなくすためには圧延形状比Ａが0.
6以上必要であることを見出した。In addition, as a result of various studies on the effect of void defects,
The inventors have found that a magnetic material having a size of 100 μ or more significantly deteriorates magnetic properties. And in order to eliminate this harmful void defect of 100μ or more, the rolling shape ratio A is set to 0.
It was found that 6 or more are necessary.
ただし、 A :圧延形状比 hi：入側板厚（mm） hO：出側板厚（mm） R :圧延ロール半径（mm） さらに、鋼中の水素の存在も第３図に示すように有害
で、脱水素熱処理を行なうことによって磁気特性が大幅
に向上することを知見した。However, A: Rolling shape ratio h i : Inlet side plate thickness (mm) h O : Outlet side plate thickness (mm) R: Rolling roll radius (mm) Furthermore, the presence of hydrogen in steel is harmful as shown in Fig. 3, It was found that the magnetic characteristics are significantly improved by performing the dehydrogenation heat treatment.
第３図に示すように0.007C−0.01Si−0.1Mn鋼にあって
高形状比圧延により空隙性欠陥のサイズを100μ以下に
し、かつ脱水素熱処理により鋼中水素を減少すること
で、低磁場での磁束密度が大幅に上昇することがわか
る。As shown in Fig. 3, in 0.007C-0.01Si-0.1Mn steel, by reducing the size of void defects to 100μ or less by high shape ratio rolling and reducing hydrogen in the steel by dehydrogenation heat treatment, low magnetic field It can be seen that the magnetic flux density at is significantly increased.
さらに、保磁力を低くし、かつ低磁場での磁束密度を低
下させない元素として種々検討した結果、第４図に示す
ように0.008C−0.15Mn−0.010Al鋼で、Niが最適である
ことを知見した。Furthermore, as a result of various studies as an element that lowers the coercive force and does not reduce the magnetic flux density in a low magnetic field, as shown in FIG. 4, 0.008C-0.15Mn-0.010Al steel was found to have the optimum Ni. I found out.
次に成分限定理由を述べる。Next, the reasons for limiting the components will be described.
Ｃは鋼中の内部応力を高め、磁気特性、特に低磁場での
磁束密度を最も低下させる元素であり、極力低減するこ
とが低磁場での磁束密度を低下させないことに寄与す
る。また、磁気時効の点からも低いほど経時低下が少な
く、磁気特性の良い状態で恒久的に使用できるものであ
り、このようなことから、0.01％以下に限定する。C is an element that increases the internal stress in steel and reduces the magnetic characteristics, particularly the magnetic flux density in a low magnetic field most, and reducing it as much as possible contributes to not decreasing the magnetic flux density in a low magnetic field. Further, the lower the magnetic aging is, the less the deterioration with time is, and the permanent magnet can be used in a state where the magnetic characteristics are good. Therefore, the content is limited to 0.01% or less.
第２図に示すようにさらに、0.005％以下にすることに
より一層高磁束密度が得られる。As shown in FIG. 2, a higher magnetic flux density can be obtained by further setting the content to 0.005% or less.
Si,Mnは低磁場での磁束密度の点から少ない方が好まし
く、MnはMnS系介在物を生成する点からも低い方がよ
い。この意味からSiは0.02％以下、Mnは0.20％以下に限
定する。Mnに関してはMnS系介在物を生成する点よりさ
らに望ましくは0.10％以下がよい。Si and Mn are preferably as small as possible from the viewpoint of magnetic flux density in a low magnetic field, and Mn is preferably as low as MnS-based inclusions are generated. From this meaning, Si is limited to 0.02% or less and Mn is limited to 0.20% or less. Mn is more preferably 0.10% or less from the viewpoint of forming MnS inclusions.
S,Oは鋼中において非金属介在物を形成し、磁壁の移動
を妨げる害を及ぼし含有量が多くなるに従って磁束密度
の低下が見られ、磁気特性を低下させるので少ないほど
よい。このため、Ｓは0.010％以下、Ｏは0.005％以下と
した。S and O form non-metallic inclusions in the steel, have a detrimental effect on the movement of the magnetic domain wall, and the magnetic flux density decreases as the content increases. Therefore, S is set to 0.010% or less and O is set to 0.005% or less.
Cr,Mo,Cuは低磁場での磁束密度を低下させるので少ない
ほど好ましく、また偏析度合を少なくすることから極力
低くすることが必要であり、この意味からCrは0.05％以
下、Moは0.01％以下、Cuは0.01％以下とする。Cr, Mo, Cu lower the magnetic flux density in a low magnetic field, so the smaller the better, and it is necessary to make it as low as possible in order to reduce the degree of segregation. From this meaning, Cr is 0.05% or less, Mo is 0.01%. Hereinafter, Cu is 0.01% or less.
Niは保磁力を低下させ、かつ低磁場での磁束密度を低下
させない元素として不可欠なもので、保磁力を低下させ
るためには0.1％以上添加させる必要がある。2.0％以上
添加すると保磁力の上昇と低磁場での磁束密度を低下さ
せるので、0.1〜2.0％に限定する。また、これによって
磁気特性を低下させずに強度をあげることが可能であ
り、望ましくは1.0〜2.0％である。Ni is indispensable as an element that lowers the coercive force and does not lower the magnetic flux density in a low magnetic field, and it is necessary to add 0.1% or more in order to lower the coercive force. Addition of 2.0% or more lowers the coercive force and the magnetic flux density in a low magnetic field, so the content is limited to 0.1 to 2.0%. Further, this makes it possible to increase the strength without deteriorating the magnetic characteristics, and is preferably 1.0 to 2.0%.
Al,Caは脱酸剤として用いるもので、Alは0.005％以上必
要であるが、多くなりすぎると介在物を生成し鋼の性質
を損なうので上限は0.040％とする。さらに磁壁の移動
を妨げる析出物であるAlNを減少させるためには低いほ
どよく、望ましくは0.020％以下がよい。Al and Ca are used as deoxidizers, and Al is required to be 0.005% or more. However, if too much, inclusions are generated and the properties of the steel are impaired, so the upper limit is made 0.040%. Further, in order to reduce AlN, which is a precipitate that hinders the movement of the domain wall, the lower the better, the better is 0.020%.
CaはAl＜0.005％の場合、Alに代わる脱酸元素として用
いられ、0.0005％以上添加されるが、0.01％超では低磁
場での磁束密度を低下させるので、上限は0.01％とす
る。When Al <0.005%, Ca is used as a deoxidizing element in place of Al and is added in an amount of 0.0005% or more. However, if it exceeds 0.01%, the magnetic flux density in a low magnetic field decreases, so the upper limit is made 0.01%.
Ｎは内部応力を高めかつAlNにより結晶粒微細化作用に
より低磁場での磁束密度を低下させるので上限は0.004
％とする。N increases the internal stress and reduces the magnetic flux density in a low magnetic field due to the grain refining effect of AlN, so the upper limit is 0.004.
%.
Ｈは磁気特性を低下させ、かつ、空隙性欠陥の減少を妨
げるので0.0002％以下とする。H reduces the magnetic properties and hinders the reduction of void defects, so it is made 0.0002% or less.
次に製造法について述べる。Next, the manufacturing method will be described.
圧延条件については、まず圧延前加熱温度を1150℃以下
にするのは、1150℃を超える加熱温度では加熱γ粒径の
板厚方向のバラツキが大きく、このバラツキが圧延後も
残り最終的な結晶粒が不均一となるため、上限を1150℃
とする。加熱温度が950℃未満となると圧延の変形抵抗
が大きくなり、以下に述べる空隙性欠陥をなくすための
形状比の高い圧延の圧延負荷が大きくなるため、950℃
を下限とする。Regarding the rolling conditions, first, the heating temperature before rolling is set to 1150 ° C or lower because the heating γ grain size has a large variation in the plate thickness direction at heating temperatures higher than 1150 ° C, and this variation remains even after rolling in the final crystal. The grain size is not uniform, so the upper limit is 1150 ° C.
And If the heating temperature is less than 950 ° C, the deformation resistance of rolling increases, and the rolling load of rolling with a high shape ratio to eliminate the void defects described below increases.
Is the lower limit.
熱間圧延にあたり前述の空隙性欠陥は鋼の凝固過程で大
小はあるが、必ず発生するものでありこれをなくす手段
は圧延によらなければならないので、熱間圧延の役目は
重要である。すなわち、熱間圧延１回当たりの変形量を
大きくし板厚中心部にまで変形が及ぶ熱間圧延が有効で
ある。In the hot rolling, the above-mentioned void defects are large and small in the solidification process of steel, but they are always generated and the means for eliminating them must be done by rolling, so the role of hot rolling is important. That is, it is effective to increase the amount of deformation per hot rolling so that the deformation reaches the center of the plate thickness.
具体的には圧延形状比Ａが0.6以上の圧延パスが１回以
上を含む高形状比圧延を行ない、空隙性欠陥のサイズを
100μ以下にすることが磁気特性によい。圧延中にこの
高形状比圧延により空隙性欠陥をなくすことで、後で行
なう脱水素熱処理における脱水素効率が飛躍的に上昇す
るのである。Specifically, high shape ratio rolling including one or more rolling passes with a rolling shape ratio A of 0.6 or more is performed to determine the size of void defects.
It is good for the magnetic properties to be 100 μm or less. By eliminating the void defects by the high shape ratio rolling during rolling, the dehydrogenation efficiency in the dehydrogenation heat treatment to be performed later is dramatically increased.
次に800℃以下の軽圧下により板厚方向に均一な粒成長
を図り、かつこの軽圧下で導入された集合組織により、
磁区の方向がそろい低磁場での磁壁の移動を容易とし、
板厚方向に均一な磁気特性の向上を図ることができる。Next, we plan uniform grain growth in the plate thickness direction by a light pressure of 800 ° C or less, and by the texture introduced under this light pressure,
Facilitates the movement of domain walls in low magnetic fields where the directions of the magnetic domains are uniform,
It is possible to improve the magnetic characteristics uniformly in the plate thickness direction.
この軽圧下の圧下率としては、第１図に示すように低磁
場での磁束密度を高くするためには、最低800℃以下で1
0％以上の圧下率が必要であるため、10％を下限とす
る。800℃以下で35％を超える圧下率の圧下を加える
と、板厚方向の磁気特性のバラツキが増大するため、35
％を上限とする。As the reduction ratio of this light reduction, in order to increase the magnetic flux density in a low magnetic field as shown in FIG.
Since a reduction rate of 0% or more is required, the lower limit is 10%. If a reduction rate of more than 35% is applied at 800 ° C or less, variations in magnetic properties in the plate thickness direction increase.
% Is the upper limit.
次に熱間圧延に引続き結晶粒粗大化、内部歪除去及び板
厚50mm以上の厚手材については脱水素熱処理を施す。板
厚50mm以上では水素の拡散がしにくく、これが空隙性欠
陥の原因となり、かつ水素自身の作用と合わさって低磁
場での磁束密度を低下させる。Next, following hot rolling, grain coarsening, internal strain removal, and dehydrogenation heat treatment are applied to thick materials with a plate thickness of 50 mm or more. When the plate thickness is 50 mm or more, it is difficult for hydrogen to diffuse, which causes void defects and, together with the action of hydrogen itself, reduces the magnetic flux density in a low magnetic field.
このため、脱水素熱処理を行なうが、その際600℃未満
では脱水素効率が悪く750℃超では変態が一部開始する
ので、600〜750℃の温度範囲で行なう。脱水素時間とし
ては種々検討の結果〔0.6（ｔ−50）＋６〕時間（t:板
厚）が適当である。For this reason, dehydrogenation heat treatment is performed, but at that time, dehydrogenation efficiency is poor at less than 600 ° C, and transformation partially starts at more than 750 ° C. Therefore, it is performed in the temperature range of 600 to 750 ° C. As a dehydrogenation time, as a result of various studies, [0.6 (t-50) +6] hours (t: plate thickness) is suitable.
焼鈍は結晶粒粗大化及び内部歪除去のために行なうが、
750℃未満では結晶粒粗大化が起こらず、また950℃超で
は結晶粒の板厚方向の均質性が保てないため、焼鈍温度
としては750〜950℃に限定する。Annealing is performed for grain coarsening and internal strain removal,
If the temperature is less than 750 ° C, grain coarsening does not occur, and if it exceeds 950 ° C, the uniformity of the crystal grains in the plate thickness direction cannot be maintained, so the annealing temperature is limited to 750 to 950 ° C.
焼準は板厚方向の結晶粒調整及び内部歪除去のために行
なうが、焼準温度は910〜1000℃に限定する。910℃未満
ではオーステナイト域とフェライト域の混在により結晶
粒が混粒となり、1000℃超では結晶粒の板厚方向の均質
性が保てない。Normalization is performed to adjust crystal grains in the plate thickness direction and remove internal strain, but the normalizing temperature is limited to 910 to 1000 ° C. Below 910 ° C, the crystal grains become mixed grains due to the mixture of austenite and ferrite regions, and above 1000 ° C, the homogeneity of the crystal grains in the plate thickness direction cannot be maintained.
なお、磁気特性向上のためには、結晶粒粗大化と内部歪
み除去とが考えられるが、特に内部歪み除去は必須条件
である。内部歪み除去は、板厚50mm以上の厚手材では脱
水素熱処理で行なうことができる。したがって、本発明
の厚手材では脱水素熱処理で、上記焼鈍あるいは焼準を
兼ねることができる。一方、板厚50mm未満のものは水素
の拡散が容易なため、脱水素熱処理は不要で前述の焼鈍
または焼準するのみでよい。In order to improve the magnetic properties, coarsening of crystal grains and removal of internal strain can be considered, but removal of internal strain is an essential condition. Internal strain can be removed by dehydrogenation heat treatment for thick materials with a plate thickness of 50 mm or more. Therefore, in the thick material of the present invention, the dehydrogenation heat treatment can also serve as the above-mentioned annealing or normalization. On the other hand, if the sheet thickness is less than 50 mm, hydrogen can be easily diffused, and therefore dehydrogenation heat treatment is not necessary and only the above-mentioned annealing or normalization is required.
（実施例） 次に本発明の実施例を比較例とともにあげる。(Examples) Next, examples of the present invention will be given together with comparative examples.
第１表に電磁厚板の製造条件とフェライト粒径、低磁場
での磁束密度、板厚方向の磁束密度のバラツキを示す。Table 1 shows the manufacturing conditions of the electromagnetic thick plate, the ferrite grain size, the magnetic flux density in a low magnetic field, and the variations in the magnetic flux density in the plate thickness direction.
例１〜11は本発明の実施例を示し、例12〜33は比較例を
示す。 Examples 1 to 11 show examples of the present invention, and Examples 12 to 33 show comparative examples.
例１〜６は板厚100mmに仕上げたもので、高磁束密度で
板厚方向のバラツキも少なく、保磁力は低い。例１に比
べ、例２はさらに低Ｃ、例3,4は低Mn、例５は低Al、例
６はAl無添加−Ca添加であり、より高い磁気特性を示
す。例７〜９は500mm、例10は40mm、例11は6mmに仕上げ
たもので、高磁束密度で板厚方向のバラツキも少なく、
保磁力は低い。Examples 1 to 6 are finished to a plate thickness of 100 mm, have high magnetic flux density, have little variation in the plate thickness direction, and have low coercive force. Compared with Example 1, Example 2 has lower C, Examples 3 and 4 have lower Mn, Example 5 has lower Al, and Example 6 has no Al added-Ca added, and shows higher magnetic properties. Examples 7 to 9 are finished with 500 mm, Example 10 with 40 mm, and Example 11 with 6 mm, and have high magnetic flux density and little variation in the plate thickness direction.
Coercive force is low.
例12はＣが高く、例13はSiが高く、例14はMnが高く、例
15はＳが高く、例16はCrが高く、例17はMoが高く、例18
はCuが高く、それぞれ上限を超えるため低磁束密度で、
保磁力は高い。例19はNiが低く、保磁力が高い。例20は
Niが高く、例21はAlが高く、例22はＮが高く、例23はＯ
が高く、例24はＨが高く、それぞれ上限を超えるため低
磁束密度で保磁力が高い。例25は加熱温度が上限を超え
板厚方向の磁束密度のバラツキが大きい。例26は加熱温
度が下限をはずれ最大形状比が小さいため、低磁束密度
で板厚方向のバラツキも大きい。例27は800℃以下の圧
下率が下限をはずれ低磁束密度となっている。例28は80
0℃以下の圧下率が上限を超えるため、板厚方向の磁束
密度のバラツキが大きい。例29は最大形状比が下限をは
ずれ、例30は脱水素熱処理温度が下限をはずれ、例31は
焼鈍温度が下限をはずれ、例32は焼準温度が上限を超
え、例33は脱水素熱処理がないため低磁束密度で、板厚
方向の磁束密度のバラツキが大きい。Example 12 has a high C, Example 13 has a high Si, and Example 14 has a high Mn.
15 has high S, Example 16 has high Cr, Example 17 has high Mo, Example 18
Is high in Cu and exceeds the upper limit of each, so it has a low magnetic flux density,
High coercive force. Example 19 has low Ni and high coercive force. Example 20
Ni is high, Example 21 is high Al, Example 22 is high N, Example 23 is O
Is high, and in Example 24, H is high and exceeds the respective upper limits, so that the magnetic flux density is low and the coercive force is high. In Example 25, the heating temperature exceeds the upper limit and the variation in the magnetic flux density in the plate thickness direction is large. In Example 26, the heating temperature is below the lower limit and the maximum shape ratio is small, so that the magnetic flux density is low and the variation in the plate thickness direction is large. In Example 27, the rolling reduction below 800 ° C falls below the lower limit and the magnetic flux density is low. Example 28 is 80
Since the rolling reduction at 0 ° C or lower exceeds the upper limit, the magnetic flux density varies greatly in the plate thickness direction. In Example 29, the maximum shape ratio is out of the lower limit, in Example 30, the dehydrogenation heat treatment temperature is out of the lower limit, in Example 31, the annealing temperature is out of the lower limit, in Example 32, the normalizing temperature exceeds the upper limit, and in Example 33, dehydrogenation heat treatment. Since it is not present, the magnetic flux density is low and the variation in the magnetic flux density in the plate thickness direction is large.
（発明の効果） 以上詳細に述べたごとく、本発明によれば適切な成分限
定により板厚の厚い厚鋼板に均質な高電磁特性を具備せ
しめることに成功し、直流磁化による磁気特性を利用す
る構造物に適用可能としたものであり、かつその製造法
も前述の成分限定と熱間圧延後結晶粒調整及び脱水素熱
処理を同時に行なう方式であり、極めて経済的に製造す
る方法を提供するもので産業上多大な効果を奏するもの
である。(Effects of the Invention) As described in detail above, according to the present invention, it has succeeded in providing a thick steel plate having a thick plate thickness with a uniform high electromagnetic characteristic by appropriately limiting the components, and utilizes the magnetic characteristic by direct-current magnetization. It is applicable to a structure, and its manufacturing method is a method of simultaneously performing the above-mentioned component limitation, grain adjustment and hot dehydrogenation heat treatment after hot rolling, and provides a very economical manufacturing method. It has a great industrial effect.
第１図は80A/mにおける磁束密度及び板厚方向の磁束密
度のバラツキに及ぼす800℃以下の圧下率の影響を示す
グラフである。第２図は80A/mにおける磁束密度に及ぼ
すＣ含有量の影響を示すグラフである。第３図は80A/m
における磁束密度に及ぼす空隙性欠陥のサイズ及び脱水
素熱処理の影響を示すグラフである。第４図は保磁力に
及ぼすNi含有量の影響を示すグラフである。FIG. 1 is a graph showing the influence of a rolling reduction of 800 ° C. or less on the variations in the magnetic flux density at 80 A / m and the magnetic flux density in the plate thickness direction. FIG. 2 is a graph showing the effect of C content on the magnetic flux density at 80 A / m. Figure 3 shows 80A / m
3 is a graph showing the influence of the size of void defects and dehydrogenation heat treatment on the magnetic flux density in FIG. FIG. 4 is a graph showing the effect of Ni content on the coercive force.
Claims (3)
一方で脱酸し、 N :0.004％以下、 O :0.005％以下、 H :0.0002％以下、 残部実質的に鉄からなる鋼組成の鋼片または、鋳片を95
0〜1150℃に加熱し、800℃以上で圧延形状比Ａが0.6以
上の圧延パスを１回以上はとる圧延を行ない、引続き80
0℃以下で圧下率を10〜35％とする圧延を行ない、板厚5
0mm以上の厚板とし、該厚板を600〜750℃の温度で脱水
素熱処理を行なうことを特徴とする板厚方向の磁気特性
の均一な良電磁厚板の製造方法。 ただし、 A :圧延形状比 hi：入側板厚（mm） hO：出側板厚（mm） R :圧延ロール半径（mm）1. By weight%, C: 0.01% or less, Si: 0.02% or less, Mn: 0.20% or less, S: 0.010% or less, Cr: 0.05% or less, Mo: 0.01% or less, Cu: 0.01% or less. , Ni: 0.1-2.0%, Al: 0.005-0.040%, Ca: 0.0005-0.01%, deoxidized by either, N: 0.004% or less, O: 0.005% or less, H: 0.0002% In the following, a slab or steel slab with a steel composition consisting essentially of iron is used.
After heating at 0 to 1150 ℃ and rolling at 800 ℃ or higher with a rolling shape ratio A of 0.6 or higher at least once, rolling is continued for 80 times.
Rolling at a rolling reduction of 10 to 35% at 0 ° C or less
A method for producing a good electromagnetic thick plate having uniform magnetic characteristics in the plate thickness direction, characterized in that the plate has a thickness of 0 mm or more and is subjected to dehydrogenation heat treatment at a temperature of 600 to 750 ° C. However, A: Rolling shape ratio h i : Inlet plate thickness (mm) h O : Outlet plate thickness (mm) R: Rolling roll radius (mm)
〜950℃の温度で焼鈍するかあるいは910〜1000℃の温度
で焼準することを特徴とする請求項１記載の板厚方向の
磁気特性の均一な良電磁厚板の製造方法。2. A 750-mm thick plate having a thickness of 50 mm or more after dehydrogenation heat treatment
The method for producing a good electromagnetic thick plate having uniform magnetic characteristics in the plate thickness direction according to claim 1, characterized in that annealing is carried out at a temperature of 950C to 950C or normalizing is carried out at a temperature of 910C to 1000C.
一方で脱酸し、 N :0.004％以下、 O :0.005％以下、 H :0.0002％以下、 残部実質的に鉄からなる鋼組成の鋼片または、鋳片を95
0〜1150℃に加熱し、800℃以上で圧延形状比Ａが0.6以
上の圧延パスを１回以上はとる圧延を行ない、引続き80
0℃以下で圧下率を10〜35％とする圧延を行ない、板厚2
0mm以上50mm未満の厚板とし、該厚板を750〜950℃の温
度で焼鈍するかあるいは910〜1000℃の温度で焼準する
ことを特徴とする板厚方向の磁気特性の均一な良電磁厚
板の製造方法。 ただし、 A :圧延形状比 hi：入側板厚（mm） hO：出側板厚（mm） R :圧延ロール半径（mm）3. In weight%, C: 0.01% or less, Si: 0.02% or less, Mn: 0.20% or less, S: 0.010% or less, Cr: 0.05% or less, Mo: 0.01% or less, Cu: 0.01% or less. , Ni: 0.1-2.0%, Al: 0.005-0.040%, Ca: 0.0005-0.01%, deoxidized by either, N: 0.004% or less, O: 0.005% or less, H: 0.0002% In the following, a slab or steel slab with a steel composition consisting essentially of iron is used.
After heating at 0 to 1150 ℃ and rolling at 800 ℃ or higher with a rolling shape ratio A of 0.6 or higher at least once, rolling is continued for 80 times.
Rolling at a rolling reduction of 10 to 35% at 0 ° C or less
A thick plate having a thickness of 0 mm or more and less than 50 mm, and the thick plate is annealed at a temperature of 750 to 950 ° C. or normalized at a temperature of 910 to 1000 ° C. Method for manufacturing planks. However, A: Rolling shape ratio h i : Inlet plate thickness (mm) h O : Outlet plate thickness (mm) R: Rolling roll radius (mm)
Priority Applications (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1064734A JPH079039B2 (en) | 1989-03-16 | 1989-03-16 | Method for manufacturing good electromagnetic thick plate with uniform magnetic properties in the thickness direction |
| US07/492,924 US5037493A (en) | 1989-03-16 | 1990-03-13 | Method of producing non-oriented magnetic steel plate having high magnetic flux density and uniform magnetic properties through the thickness direction |
| DE69020015T DE69020015T2 (en) | 1989-03-16 | 1990-03-14 | Process for producing non-oriented magnetic steel sheets with a high magnetic flux density and with uniform magnetic properties in the thickness direction. |
| EP90104818A EP0388776B1 (en) | 1989-03-16 | 1990-03-14 | Method of producing non-oriented magnetic steel plate having high magnetic flux density and uniform magnetic properties through the thickness direction |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1064734A JPH079039B2 (en) | 1989-03-16 | 1989-03-16 | Method for manufacturing good electromagnetic thick plate with uniform magnetic properties in the thickness direction |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH02243717A JPH02243717A (en) | 1990-09-27 |
| JPH079039B2 true JPH079039B2 (en) | 1995-02-01 |
Family
ID=13266674
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1064734A Expired - Lifetime JPH079039B2 (en) | 1989-03-16 | 1989-03-16 | Method for manufacturing good electromagnetic thick plate with uniform magnetic properties in the thickness direction |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH079039B2 (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113403537B (en) * | 2021-06-17 | 2023-01-31 | 江苏省沙钢钢铁研究院有限公司 | Non-oriented silicon steel and production method thereof |
-
1989
- 1989-03-16 JP JP1064734A patent/JPH079039B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPH02243717A (en) | 1990-09-27 |
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