JPS5884924A - Production of electrical steel plate utilizing warm rolling - Google Patents

Abstract

PURPOSE:To obtain an electrical steel plate of improved magnetic flux density with one time of treatment wherein rolling-annealing are combined by generating intensive dyamical strain aging with the steel of a sufficient solid soln. (C+N) in a specific temp. region then subjecting the same to recrystallization annealing. CONSTITUTION:Steel of >=10ppm solid soln. (C+N) is rolled at >=20% draft at 200-500 deg.C; thereafter the steel is subjected to recrystallization annealing. Then the degree of integration of the (110)[001]bearing components in the crystal structure is increased thoroughly and an electrical steel plate having high magnetic density is obtained. Here, if the solid soln. (C+N) is below 10ppm, the degree of dynamical strain aging is small and no effect is expected. If the rolling temp. is below the lower limit, the diffusion transfer of C, N atoms to dislocation is slow and no sufficient dynamical strain aging is generated. In excess of the upper limit, the C and N atoms can arrive easily at dislocation but the mutual effect between the dislocation and the C, N atoms is weak and the dynamical strain aging annihilates. If the draft is below 20%, the propagation rate of the dislocation during rolling is small and the intensive dynamical strain aging is not generated.

Description

【発明の詳細な説明】 本発明は、圧延−焼鈍を基本とする工程において（１１
０）（００１）方位を十分発達させ、磁束密度の向上と
鉄損低減を同時に満足する新しい電磁鋼板の製造法に関
するものである。DETAILED DESCRIPTION OF THE INVENTION The present invention provides a process based on rolling and annealing (11
The present invention relates to a new method for producing electrical steel sheets that fully develops the 0) (001) orientation and satisfies both the improvement of magnetic flux density and the reduction of iron loss.

電磁鋼板では、磁束密度を向上させるため、（１１０）
（００１）方位の集積度の高い鋼板が好ましいことは既
によく知られてはいるが、この種の鋼板の製造に当って
は、従来冷延−焼鈍の組合せを２回繰返し、その２回目
の焼鈍の段階での極端な粗大結晶粒成長の過程を通じて
、（１１０）（００１）方位の発達を図っている。In magnetic steel sheets, (110) is used to improve magnetic flux density.
It is already well known that steel sheets with a high concentration of (001) orientations are preferable, but in the production of this type of steel sheet, conventionally, the combination of cold rolling and annealing is repeated twice, and the second The (110) (001) orientation is developed through the process of extremely coarse grain growth at the annealing stage.

この従来法では、冷延−焼鈍の組合せ処理を２回おこな
うため製造工程でのエネルギー消費も大きい。一方、冷
延−焼鈍の１回の組合せでは、高い（１１０）（００１
）の集積は得られなかった。これに対して本発明を適用
すれば、正順焼鈍を組合せた１回の処理で（１１０）（
００１）得られる。In this conventional method, a combination of cold rolling and annealing is performed twice, which consumes a large amount of energy in the manufacturing process. On the other hand, in one combination of cold rolling and annealing, high (110) (001
) could not be obtained. On the other hand, if the present invention is applied, (110) (
001) obtained.

即ち本発明は、固溶（Ｃ十Ｎ）が１０　ｐｐｍ以上であ
る鋼を２００〜５００℃の温度域において、２０チ以上
の圧下率で圧延し、そのあと再結晶焼鈍をおこない、集
合組織の（１１０）（００１）方位成分の発達を図るこ
とを特徴とする電磁鋼板の製造法を骨子とする。That is, in the present invention, steel having a solid solution (C and N) of 10 ppm or more is rolled at a reduction rate of 20 inches or more in a temperature range of 200 to 500°C, and then recrystallized annealed to improve the texture. The gist of the method is to produce an electrical steel sheet characterized by developing the (110) (001) orientation component.

以下本発明の内容を詳細に説明する。The contents of the present invention will be explained in detail below.

本発明は、焼鈍に先立つ圧延の段階で激しい動的歪時効
を生ぜしめ、その結果得られる特殊な加工組織を利用し
て、焼鈍後の集合組織における（１１．０）（：００１
）方位成分の増大を図る点にある。動的歪時効とは、加
工時に運動する転位と鋼中の固溶Ｃ，Ｎとの相互作用に
よって生ずる加工中の歪時効である。本発明に関する詳
細な研究の結果によれば、圧延中に激しい動的歪時２効
が発生すると、結晶粒内に特に加工歪の大きい帯状の領
域（以下変形帯と称する）が形成され、焼鈍時にはその
変形帯に（１１０）〔００１〕再結晶核が優先的に形成
され、焼鈍後の集合組織における（１１０）（００１）
方位成分の増大に寄与する。The present invention produces severe dynamic strain aging in the rolling stage prior to annealing, and utilizes the resulting special processed structure to create (11.0) (:001) texture after annealing.
) The aim is to increase the azimuth component. Dynamic strain aging is strain aging during processing that is caused by the interaction between dislocations that move during processing and solid solution C and N in the steel. According to the results of detailed research related to the present invention, when severe dynamic strain effects occur during rolling, band-shaped regions with especially large working strains (hereinafter referred to as deformation bands) are formed within grains, and during annealing Sometimes (110)[001] recrystallization nuclei are preferentially formed in the deformation zone, and (110)(001) in the texture after annealing.
Contributes to an increase in the azimuth component.

このような動的歪時効を生ぜしむるに当っては、先ず鋼
が十分な量の固溶（Ｃ＋Ｎ　）を含有していなければな
らず、圧延前の段階で、内部摩擦法などで測定した固溶
（Ｃ’＋Ｎ）が１０　ｐｐｍ以上であることが必要であ
る。固溶（Ｃ＋Ｎ）が１０ｐｐｍ未満の場合には動的歪
時効の程度が小さく本発明の効果が期待できない。In order to produce such dynamic strain aging, the steel must first contain a sufficient amount of solid solution (C+N), and the steel must contain a sufficient amount of solid solution (C+N) before rolling. It is necessary that the amount of dissolved (C'+N) is 10 ppm or more. When the solid solution (C+N) is less than 10 ppm, the degree of dynamic strain aging is small and the effects of the present invention cannot be expected.

次に圧延温度であるが、２００℃未満の温度では鋼中に
おけるＣ、Ｎ原子の拡散が遅（、Ｃ１Ｎ原子が転位に向
って拡散移動する所要時間が長（かかり過ぎ、動的歪時
効が十分には生じない。また５００℃超の温度域ではＣ
，Ｈの拡散が十分早＜Ｃ，Ｎ原子は容易に転位に到達し
得るが、転位とＣ，Ｎ原子との相互作用が弱く、動的歪
時効が消衰する。したがって圧延温度は２００〜５００
℃の範囲、つまり温間−圧延（以下温延という）の範囲
になければならない。Next, regarding the rolling temperature, at temperatures below 200°C, the diffusion of C and N atoms in the steel is slow (and the time required for C1N atoms to diffuse and move toward dislocations is long (too much time is required, and dynamic strain aging occurs). In addition, in the temperature range exceeding 500℃, C
, H diffusion is sufficiently fast<C, N atoms can easily reach dislocations, but the interaction between dislocations and C, N atoms is weak, and dynamic strain aging disappears. Therefore, the rolling temperature is 200-500
℃ range, that is, the range of warm rolling (hereinafter referred to as hot rolling).

また圧延時の圧下率が２０％未満であっては、圧延中の
転位の増殖量が少なく、シたがって動的歪時効が激しく
は生ぜず有効でない。このため圧下率は２０％以上でな
ければならない。本発明は圧延後の再結晶によりその発
明効果が現われるのであるから、上記条件で圧延したの
ち、再結晶の生じる条件での再結晶焼鈍を必要とす□ る。Further, if the rolling reduction ratio during rolling is less than 20%, the amount of multiplication of dislocations during rolling is small, and therefore dynamic strain aging does not occur violently and is not effective. For this reason, the rolling reduction ratio must be 20% or more. Since the effects of the present invention are manifested by recrystallization after rolling, it is necessary to perform recrystallization annealing under conditions that cause recrystallization after rolling under the above conditions.

本発明を実施するに当っての素材鋼は、１０ｐｐｍ以上
の固溶（Ｃ＋Ｎ）を含有しているだけで十分であり、そ
の他の特殊な元素の添加を必要としない。しかしながら
、鉄損値などの電磁特性を向上、させる必要から、一般
的に添加されるＡ１、Ｓｉなどの合金元素が多量に添加
されていても、以下に述べる理由により、１０　ｐｐｍ
以上の固溶（Ｃ＋Ｎ）を有することは可能であり、本発
明の効果は現われる。即ち、Ａｌが添加された場合には
、固溶ＮはＮ原子がＡＩＮとして固定されるため減少あ
るいは存在しなくなるが、固溶Ｃを１０　ｐｐｍ以上に
することは容易である。It is sufficient for the steel material used to carry out the present invention to contain 10 ppm or more of solid solution (C+N), and there is no need to add other special elements. However, due to the need to improve electromagnetic properties such as iron loss value, even if a large amount of commonly added alloying elements such as A1 and Si are added, for the reasons described below, 10 ppm
It is possible to have the above solid solution (C+N), and the effects of the present invention will appear. That is, when Al is added, the solid solution N decreases or disappears because the N atoms are fixed as AIN, but it is easy to increase the solid solution C to 10 ppm or more.

また、Ｓｉの多量添加（数チ程度まで）に対しては、よ
く知られているように固溶（Ｃ＋Ｎ）量は大きく変化し
ない。Furthermore, as is well known, when a large amount of Si is added (up to several Si), the amount of solid solution (C+N) does not change significantly.

本発明に規定した条件での温延は、他の圧延との組合せ
、つまり熱延−温延、温延−冷延あるいは熱延−温延一
冷延の組合せで実施しても有効であるが、この場合冷延
の圧下率は温延の圧下率以下であることが望ましい。Hot rolling under the conditions specified in the present invention is effective even if it is performed in combination with other rolling, that is, a combination of hot rolling-hot rolling, hot rolling-cold rolling, or hot rolling-hot rolling and cold rolling. However, in this case, it is desirable that the rolling reduction in cold rolling is equal to or lower than that in hot rolling.

実施例１ 真空溶解、したＣＸＮの含有量の異なる鋼を１２００℃
に加熱し、仕上温度９５０℃で板厚２、０　Ｉｌｌに熱
延後空冷した。これらの試料の化学成分および内部摩擦
法で評価した固溶（Ｃ＋Ｎ）の量を第１表に示す。Example 1 Vacuum melted steels with different CXN contents were heated at 1200°C.
The sheet was hot rolled to a thickness of 2.0 Ill at a finishing temperature of 950°C, and then cooled in air. Table 1 shows the chemical composition of these samples and the amount of solid solution (C+N) evaluated by the internal friction method.

第１表 全試料とも他の元素は以下の通り。Table 1 Other elements in all samples are as follows.

Ｓｔ≦０．０１係、■＝ｏ、ｏｉ％、Ｐ＝０．００２チ
、Ｓ＝０．００４％、Ａ１−〇、００２％、残部Ｆｅ０
これらの試料を１０〜８０ｑｂの圧下率で、室温〜７０
０℃の温度で圧延し、７００℃×５分の再結晶焼鈍をお
こなってから、それぞれの試料についてＸ線極点図を作
成し、（１１０）（００１）の方位成分強度比（ランダ
ム集合組織をもつ標準試料の場合を基準としたＸ線の反
射強度比）を求めた。St≦0.01, ■=o, oi%, P=0.002chi, S=0.004%, A1-〇, 002%, remainder Fe0
These samples were heated at room temperature to 70 qb at a reduction rate of 10 to 80 qb.
After rolling at a temperature of 0°C and recrystallization annealing at 700°C for 5 minutes, an X-ray pole figure was created for each sample, and the (110) (001) orientation component intensity ratio (random texture) was The X-ray reflection intensity ratio (based on the case of a standard sample) was determined.

この（１１０）　’（００１）強度比と成分、工程条件
との関係を第１図、第２図に示す。The relationship between this (110) '(001) intensity ratio, components, and process conditions is shown in FIGS. 1 and 2.

第１図より明らかなどと＜、固溶（Ｃ＋Ｎ）が１０　Ｐ
Ｐｍ以上の試料を、２０チ以上の圧下率で温延（圧延温
度３７０℃）した場合、焼鈍後の（１１０）（００１）
強度比が著しく高くなる。（図中Ａ；圧下車７０％、Ｂ
；圧下率３０チ、Ｃ；圧下−１０チを示した。）また一
方第２図は、２００〜５００℃での温延（圧下率５０チ
）が、（１１０）（００１）強度比の著鴫い増大に寄与
していることを示した。（図中ａ；本発明材の試料ｘ６
、ｂ：比較材の試料屋１を示す。）実施例２ 第１表における試料Ａ２とＡｌを用い、室温〜７００℃
の各温度で、別々に各々７５％の圧延をおこない、板厚
０．５　ｍｇとしたのち、７００℃×５分の焼鈍で再結
晶を終了させ、各々の試料について圧延方向の電磁特性
を測定した結果を第３図及び第４図に示す。It is clear from Figure 1 that the solid solution (C+N) is 10 P.
When a sample with Pm or more is hot rolled (rolling temperature 370°C) at a rolling reduction of 20 inches or more, (110) (001) after annealing
The intensity ratio becomes significantly higher. (A in the figure; reduction car 70%, B
: The rolling reduction was 30 inches; C: The rolling reduction was -10 inches. ) On the other hand, FIG. 2 showed that hot rolling at 200 to 500°C (reduction ratio of 50 inches) contributed to a significant increase in the (110)(001) strength ratio. (a in the figure; sample x6 of the present invention material
, b: Shows sample shop 1 of comparative material. ) Example 2 Using sample A2 and Al in Table 1, at room temperature to 700°C
After rolling 75% of each sample separately at each temperature to obtain a plate thickness of 0.5 mg, recrystallization was completed by annealing at 700°C for 5 minutes, and the electromagnetic properties of each sample in the rolling direction were measured. The results are shown in FIGS. 3 and 4.

図から明らかなごとく、本発明材ａ（試料屋７）を本発
明条件（２００〜５００℃）で圧延した場合（圧下率７
５％、板厚０．５　ｍｇ　）には、比較材ｂ（試料Ａ２
）に比して圧延方向について高磁束密度と低鉄損値が同
時に得られており、電磁特性が著しく改善された。As is clear from the figure, when the present invention material a (sample shop 7) is rolled under the present invention conditions (200 to 500°C) (rolling reduction rate 7
5%, plate thickness 0.5 mg), comparative material b (sample A2
), high magnetic flux density and low core loss values were simultaneously obtained in the rolling direction, and the electromagnetic properties were significantly improved.

実施例３ Ｃ：　０．０５０％、Ｓｉ　：　２．９０％、Ｍｎ：０
．０８６チ、Ｓ：０．０２５％、Ｓｏｌ、Ａｌ　：　０
．０２７％、Ｎ：０．００７１％の化学組成を有する鋼
を溶解し、１３００℃に加熱後゛、仕上温度９７０℃で
板厚２、０　ｍに熱延し、その後の空冷中の４００℃お
よび室温で、別々に各々７５チの圧延をおこない、０．
５　ｍｍの板厚とした。Example 3 C: 0.050%, Si: 2.90%, Mn: 0
．． 086chi, S: 0.025%, Sol, Al: 0
．． Steel having a chemical composition of 0.027% and N: 0.0071% was melted and heated to 1300°C, then hot rolled to a thickness of 2.0 m at a finishing temperature of 970°C, and then heated at 400°C during air cooling. Rolling of 75 inches each was carried out separately at room temperature.
The plate thickness was 5 mm.

そののち、８００℃×５分の焼鈍で再結晶を終了させ、
圧延方向の電磁特性を測定した。After that, recrystallization is completed by annealing at 800°C for 5 minutes.
The electromagnetic characteristics in the rolling direction were measured.

その結果を第２表に示す。但し、７５％圧延の直前での
固溶（Ｃ＋Ｎ）は、内部摩擦法による測定の結果、４０
０℃での圧延直前で８３　ｐｐｍ。The results are shown in Table 2. However, the solid solution (C+N) just before 75% rolling is 40% as measured by the internal friction method.
83 ppm just before rolling at 0°C.

室温での圧延直前で７２　ｐｐｍであった。It was 72 ppm immediately before rolling at room temperature.

表から明らかなごとく、本発明材では、高磁束密度と低
鉄損値が同時に得られており、本発明を適用することに
より電磁特性の著しい改善が図られる。As is clear from the table, in the material of the present invention, high magnetic flux density and low core loss values are simultaneously obtained, and by applying the present invention, the electromagnetic properties can be significantly improved.

第２表Table 2

【図面の簡単な説明】[Brief explanation of the drawing]

第１図は、熱延板の固溶（Ｃ＋Ｎ）量と焼鈍後の（１１
０）（００１）方位成分のランダム強度比との関係図、
第２図は、圧延温度と焼鈍後の（１１０）（００１）方
位成分のランダム強度比との関係図、第３図は、圧延温
度と磁束密度との関係図、第４図は圧延温度と鉄損値と
の関係図である。 第７面 Ａ 圏ｚ３、（Ｃ十Ａ／）　（１）／）Ｍ）埠２図 圧χ温度　　（て２ θ　　　々θ　　４ｔｔ）　　　ｄ＜リ　　ｅの圧延、
＆崖　（でン 第４面 θ　　初　　＃Ｖ　　ω　６θ０ ）王し旬三う曙（）喫４（°ビノFigure 1 shows the amount of solid solution (C+N) in the hot rolled sheet and the amount of (11
0) (001) relationship diagram with the random intensity ratio of the azimuth component,
Figure 2 is a relationship between rolling temperature and random intensity ratio of (110) (001) orientation component after annealing, Figure 3 is a relationship between rolling temperature and magnetic flux density, and Figure 4 is a relationship between rolling temperature and random intensity ratio of (110) (001) orientation components after annealing. It is a relationship diagram with an iron loss value. 7th surface A sphere z3, (C0A/) (1)/) M) 2 θ pressure χ temperature (te2 θ 4tt) d<li e rolling,
& Cliff (Den 4th page θ first #V ω 6θ0) King Shunzo Ukebono () 4 (°Bino

Claims (1)

【特許請求の範囲】[Claims] 固溶（Ｃ十Ｎ）が１０　ｐｐｍ以上である鋼を、２００
〜５００℃の温度範囲において２０チ以上の圧下率で圧
延し、そのあと再結晶焼鈍をおこない、集合組織の（１
１０）（００１）方位成分を発達せしめることを特徴と
する温間圧延を利用した電磁鋼板の製造法。Steel with a solid solution (C0N) of 10 ppm or more is
Rolling is performed at a reduction rate of 20 inches or more in a temperature range of ~500℃, followed by recrystallization annealing to improve the texture (1
10) A method for producing an electrical steel sheet using warm rolling, which is characterized by developing a (001) orientation component.