JP3410873B2 - Manufacturing method of shadow mask master by continuous annealing - Google Patents
Manufacturing method of shadow mask master by continuous annealingInfo
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- JP3410873B2 JP3410873B2 JP20963595A JP20963595A JP3410873B2 JP 3410873 B2 JP3410873 B2 JP 3410873B2 JP 20963595 A JP20963595 A JP 20963595A JP 20963595 A JP20963595 A JP 20963595A JP 3410873 B2 JP3410873 B2 JP 3410873B2
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- Prior art keywords
- shadow mask
- annealing
- continuous annealing
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- range
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Description
【０００１】[0001]
【発明の属する技術分野】本発明は、カラーＴＶのブラ
ウン管内に装着される色選別電極に使用されるシャドウ
マスク原板の製造方法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method of manufacturing a shadow mask original plate used for a color selection electrode mounted in a cathode ray tube of a color TV.
【０００２】[0002]
【従来の技術】シャドウマスクは、素材メーカーにおけ
る１次冷延−焼鈍−２次冷延の後、エッチング−焼鈍−
レベラー掛け−プレス成形−黒化処理の各工程を経て製
造される。2. Description of the Related Art A shadow mask is a primary cold rolling-annealing-secondary cold rolling after etching-annealing-
It is manufactured through the steps of leveler application-press molding-blackening treatment.
【０００３】シャドウマスクの品質に対しては、エッチ
ング性、プレス成形性、黒化特性等が要求されるが、最
も重要となるのは、プレス成形時に均一な変形特性を有
している点であり、不均一変形が生じるとエッチング穴
の変形あるいは穴間隔のずれが生じ、ＴＶ画面の色ずれ
等品質に著しい悪影響を及ぼす。このため、成形時に降
伏点伸びに起因した不均一変形が生じないことが必須条
件となる。The quality of the shadow mask is required to have etching properties, press formability, blackening properties, etc., but the most important point is that it has uniform deformation properties during press forming. However, if non-uniform deformation occurs, the etching holes may be deformed or the hole intervals may be displaced, which has a significant adverse effect on the quality such as color shift of the TV screen. Therefore, it is an essential condition that uneven deformation due to elongation at yield does not occur during molding.
【０００４】このような観点から、シャドウマスク原板
の製造方法として、低炭素鋼を冷間圧延後に焼鈍する際
に強脱炭を施すことが数多く提案されている（例えば特
公昭６０−３０７２７号公報、特公昭６３−４０８４８
号公報）。ところが、このような脱炭焼鈍プロセスを経
ることは、コストあるいは納期的にも不利になる上、材
質のバラツキが大きくなる原因にもなるため、低コス
ト、短納期かつコイル内の材質均質性を満足するシャド
ウマスク原板の製造法のニーズは高まっている。From this point of view, as a method for producing a shadow mask original plate, it has been proposed in many cases to perform strong decarburization when annealing low carbon steel after cold rolling (for example, Japanese Patent Publication No. 30727/1985). , JP-B-63-40848
Issue). However, passing such a decarburization annealing process is disadvantageous in terms of cost and delivery time, and also causes a large variation in material, so low cost, short delivery time and material homogeneity in the coil are not provided. There is an increasing need for a method for producing a satisfactory shadow mask master plate.
【０００５】[0005]
【発明が解決しようとする課題】上述したような脱炭焼
鈍プロセスを省略するには、製鋼段階でＣ：５０ppm 以
下といった極低炭素レベルに成分調整した鋼を素材とし
て用いることで可能となる。しかし、このようなＣレベ
ルではＦｅ3 Ｃの析出駆動力が小さいため、焼鈍後にか
えって残留固溶Ｃが多くなり、これが降伏点伸び増加の
原因となってしまう。また、短納期という観点からは、
冷圧後の焼鈍を連続焼鈍設備で行なうことが効果的であ
るが、やはり、箱焼鈍に比べると一般に残留固溶Ｃが多
くなり易いという問題点が有る。In order to omit the decarburization annealing process as described above, it is possible to use, as a raw material, steel whose composition is adjusted to an extremely low carbon level such as C: 50 ppm or less at the steelmaking stage. However, at such a C level, the precipitation driving force of Fe 3 C is small, so the amount of residual solid solution C increases after annealing, which causes an increase in the yield point elongation. Also, from the perspective of quick delivery,
It is effective to carry out the annealing after cold pressing in a continuous annealing equipment, but again, there is a problem that the residual solid solution C is generally liable to increase as compared with the case of box annealing.
【０００６】本発明はかかる事情に鑑みてなされたもの
であって、脱炭焼鈍を省略することができ、なおかつ短
時間の連続焼鈍でもシャドウマスク原板を製造できる方
法を提供することを目的とする。The present invention has been made in view of the above circumstances, and an object of the present invention is to provide a method capable of omitting decarburization annealing and manufacturing a shadow mask blank even with continuous annealing for a short time. .
【０００７】[0007]
【課題を解決するための手段】本発明者らは、製鋼段階
でＣ：５０ppm 以下といった極低炭素レベルに成分調整
した鋼について、いかにして１次冷延−連続焼鈍−２次
冷延−焼鈍した場合にも多量の固溶Ｃが残留することな
く、成形時に降伏点伸びに起因した不均一変形が生じな
いシャドウマスク原板に適した鋼板を製造できるかにつ
いて鋭意検討した。[Means for Solving the Problems] The inventors of the present invention how to perform primary cold rolling-continuous annealing-secondary cold rolling-for steel whose composition is adjusted to an extremely low carbon level such as C: 50 ppm or less at the steelmaking stage. Even after annealing, a large amount of solute C did not remain, and it was earnestly studied whether or not a steel plate suitable for a shadow mask original plate that does not cause nonuniform deformation due to elongation at yield at the time of forming can be manufactured.
【０００８】その結果、このようなＦｅ3 Ｃの析出駆動
力が小さい極低炭素鋼においても、酸化物、硫化物、窒
化物をエッチング特性に悪影響を及ぼさない範囲でＣ量
に応じて鋼中に分散させることにより、Ｆｅ3 Ｃの析出
駆動力を十分高めることができ、最終焼鈍後においても
良好な成形性を得ることが可能であることを見出した。As a result, even in such an ultra-low carbon steel having a small Fe 3 C precipitation driving force, oxides, sulfides, and nitrides are contained in the steel according to the amount of C within a range that does not adversely affect the etching characteristics. It has been found that the Fe 3 C precipitation driving force can be sufficiently increased by dispersing the Fe 2 C in the alloy, and good formability can be obtained even after the final annealing.
【０００９】本発明は、本発明者のこのような知見に基
づいてなされたものであって、第１に、重量％で、Ｃ：
０．００１〜０．００３５％、Ｓｉ：０．１％以下、Ｍ
ｎ：０．１〜０．３％、Ｐ：０．０１５％以下、Ｓ：
０．００５〜０．０１５％、ｓｏｌ．Ａｌ：０．０１〜
０．０８％、Ｎ：０．００２〜０．００７％、Ｏ：０．
００１５〜０．００４％を含有し、かつＣ、Ｏ、Ｓ、Ｎ
がｐｐｍで４×（Ｃ／１２）−０．５≦（Ｏ／１６）＋
０．５×（Ｓ／３２）＋０．２×（Ｎ／１４）≦５を満
たす鋼を、熱間圧延および酸洗後、冷間圧延し、次い
で、連続焼鈍を、再結晶温度以上８５０℃以下の範囲で
均熱した後、６００〜４００℃の温度域を１０℃／sec
以上、４００℃未満を５℃／sec以下で冷却する条件で
行い、その後冷間圧延により製品厚さとすることを特徴
とするシャドウマスク原板の製造方法を提供するもので
あり、第２に、上記方法において、連続焼鈍が、さらに
３００〜４００℃の範囲で３０〜３００秒保持する工程
を有することを特徴とするシャドウマスク原板の製造方
法を提供するものである。The present invention has been made on the basis of such knowledge of the present inventor. First, in% by weight, C:
0.001-0.0035%, Si: 0.1% or less, M
n: 0.1 to 0.3%, P: 0.015% or less, S:
0.005-0.015%, sol. Al: 0.01-
0.08%, N: 0.002-0.007%, O: 0.
0015-0.004% and C, O, S, N
Is 4 × (C / 12) −0.5 ≦ (O / 16) + in ppm
Steel satisfying 0.5 × (S / 32) + 0.2 × (N / 14) ≦ 5 is hot-rolled, pickled, cold-rolled, and then continuously annealed at a recrystallization temperature of 850 ° C. or higher. After soaking in the following range, the temperature range of 600-400 ℃ is 10 ℃ / sec
As described above, the present invention provides a method for producing a shadow mask original plate, which is performed under the condition that the temperature is less than 400 ° C. is cooled at 5 ° C./sec or less, and then cold rolled to obtain a product thickness. In the method, the continuous annealing further includes a step of holding the material in the range of 300 to 400 ° C. for 30 to 300 seconds, to provide a method for producing a shadow mask original plate.
【００１０】[0010]
【発明の実施の形態】以下、本発明について具体的に説
明する。まず、成分の限定理由について説明する。
（１）Ｃ：０．００１〜０．００３５％
Ｃは、その含有量が多いとＦｅ3 Ｃが多くなり、エッチ
ング特性に悪影響を及ぼす、また、極端に少なくなれ
ば、Ｆｅ3 Ｃの析出駆動力が低下し、残留固溶Ｃの増加
を招く。このため、Ｃの範囲をこのような恐れがない
０．００１〜０．００３５％の範囲に規定する。BEST MODE FOR CARRYING OUT THE INVENTION The present invention will be specifically described below. First, the reasons for limiting the components will be described. (1) C: 0.001 to 0.0035% When the content of C is large, Fe 3 C is large, which adversely affects the etching characteristics, and when it is extremely small, Fe 3 C is driven to precipitate. The force decreases, and the residual solid solution C increases. For this reason, the range of C is defined as 0.001 to 0.0035% in which there is no such fear.
【００１１】（２）Ｓｉ：０．１％以下
Ｓｉは含有量が多くなると鋼板が硬質化して好ましくな
いため、このような恐れのない０．１％以下とする。(2) Si: 0.1% or less Since the steel plate becomes hard when the content of Si is large, it is not preferable. Therefore, the content of Si is set to 0.1% or less.
【００１２】（３）Ｍｎ：０．１〜０．３％
Ｍｎも含有量が多くなると鋼板が硬質化して好ましくな
いが、含有量が少なすぎると本発明において重要となる
介在物が減少して所望の効果が得られなくなる。したが
って、このようなことを回避するために、Ｍｎ量を０．
１〜０．３％の範囲に規定する。(3) Mn: 0.1 to 0.3% If Mn content is too high, the steel sheet becomes hard, which is not preferable, but if the Mn content is too small, inclusions that are important in the present invention decrease. The desired effect cannot be obtained. Therefore, in order to avoid such a case, the Mn content is set to 0.
It is specified in the range of 1 to 0.3%.
【００１３】（４）Ｐ：０．０１５％以下
Ｐは含有量が多くなると鋼板が硬質化するばかりか、偏
析しやすい元素でもあるため、エッチング特性にも悪影
響を及ぼす。このため、０．０１５％以下に規定する。(4) P: 0.015% or less If the content of P is large, not only the steel plate becomes hard, but also it is an element that tends to segregate, which adversely affects the etching characteristics. Therefore, it is specified to be 0.015% or less.
【００１４】（５）ｓｏｌ．Ａｌ：０．０１〜０．０８
％
Ａｌは鋼の脱酸のために添加されるが、本発明において
は窒化物を形成させる意味においても必須添加元素とな
る。しかし、０．０１％未満では窒化物が十分析出せ
ず、０．０８％を超えると窒化物が粗大化してエッチン
グ特性に悪影響を及ぼす。したがって、Ａｌ量をｓｏ
ｌ．Ａｌで０．０１〜０．０８％の範囲に規定する。(5) Sol. Al: 0.01 to 0.08
% Al is added for deoxidizing steel, but in the present invention, it is an essential addition element also in the sense of forming a nitride. However, if it is less than 0.01%, the nitride is not sufficiently precipitated, and if it exceeds 0.08%, the nitride is coarsened and the etching characteristics are adversely affected. Therefore, the Al amount is
l. Al is specified in the range of 0.01 to 0.08%.
【００１５】（６）Ｓ：０．００５〜０．０１５％
Ｏ：０．００１５〜０．００４％
Ｎ：０．００２〜０．００７％
これらの元素は本発明においては、Ｆｅ3 Ｃの析出核を
形成させる上で、適量添加することが非常に重要であ
る。それぞれの含有量の下限値未満では析出核として十
分な密度が得られなくなり、上限値を超えると介在物が
粗大化してエッチング特性に悪影響を及ぼす。このた
め、Ｓ、Ｏ、Ｎをこれらの範囲に規定する。(6) S: 0.005 to 0.015% O: 0.0015 to 0.004% N: 0.002 to 0.007% In the present invention, these elements precipitate Fe 3 C. It is very important to add an appropriate amount in order to form nuclei. If the content is less than the lower limit, sufficient density as precipitation nuclei cannot be obtained, and if it exceeds the upper limit, inclusions are coarsened and the etching characteristics are adversely affected. Therefore, S, O, and N are defined in these ranges.
【００１６】また、本発明では、Ｆｅ３Ｃの析出核の密
度に影響を及ぼすＯ、Ｓ、Ｎ量とＣ量とが、ｐｐｍで４
×（Ｃ／１２）−０．５≦（Ｏ／１６）＋０．５×（Ｓ
／３２）＋０．２×（Ｎ／１４）≦５で示される式を満
たす必要がある。この式は、Ｃ量が少なくなっていく
と、Ｏ、Ｓ、Ｎ含有量の下限値を増加させていかなけれ
ばならないことを示す。これは、Ｃ量が少なくなるほど
Ｆｅ３Ｃの析出駆動力が低下していくため、析出核を増
加させて析出を促進する必要があるためである。また
（Ｏ／１６）＋０．５×（Ｓ／３２）＋０．２×（Ｎ／
１４）≦５に規定したのは、この値を超えると介在物が
粗大化してエッチング特性に悪影響を及ぼすためであ
る。Further, in the present invention, the amounts of O, S, N and C, which affect the density of Fe 3 C precipitation nuclei, are 4 ppm in ppm.
× (C / 12) −0.5 ≦ (O / 16) + 0.5 × (S
/32)+0.2×(N/14)≦5 must be satisfied. This formula shows that the lower limits of the O, S, and N contents must be increased as the C content decreases. This is because the Fe 3 C precipitation driving force decreases as the amount of C decreases, and it is necessary to increase precipitation nuclei to promote precipitation. Also, (O / 16) + 0.5 × (S / 32) + 0.2 × (N /
14) ≦ 5 is defined because if it exceeds this value, inclusions become coarse and adversely affect etching characteristics.
【００１７】Ｃ量と（Ｏ／１６）＋０．５×（Ｓ／３
２）＋０．２×（Ｎ／１４）の値（以下Ｘと表す）の適
正範囲を図１に示す。この図は、後述する表２のデータ
のうち、以下に示す焼鈍熱サイクル条件を満たすものを
プロットしたものである。この図において白丸はエッチ
ング特性およびプレス成形性とも良好なもの、黒丸はエ
ッチング特性およびプレス成形性のうちいずれかが不良
のものを示す。この図から、Ｃ量が少なくなるほど、エ
ッチング特性およびプレス成形性とも良好になるための
Ｘの値の下限値が高くなっていることがわかる。この下
限値の曲線は、Ｘ＝４×（Ｃ／１２）-0.5で近似され
る。C amount and (O / 16) + 0.5 × (S / 3
2) The appropriate range of the value of + 0.2 × (N / 14) (hereinafter referred to as X) is shown in FIG. This figure is a plot of data of Table 2 described later that satisfies the following annealing thermal cycle conditions. In this figure, white circles indicate good etching characteristics and press moldability, and black circles indicate defective etching characteristics and press moldability. From this figure, it is understood that the lower the amount of C, the higher the lower limit of the value of X for improving the etching characteristics and the press formability. This lower limit curve is approximated by X = 4 × (C / 12) −0.5 .
【００１８】なお、上記式において、Ｏ、Ｓ、Ｎ量につ
いては等価となっていない。これは、介在物の中で酸化
物−硫化物−窒化物の順に析出していき、後工程で析出
していく硫化物、窒化物については、酸化物を核として
析出するものが多くなるためである。In the above equation, the amounts of O, S and N are not equivalent. This is because oxides-sulfides-nitrides are sequentially deposited in the inclusions, and many of the sulfides and nitrides that are deposited in the later step are deposited with the oxide as a nucleus. Is.
【００１９】その他の元素については特に限定されない
が、７０ppm 以下のＳｎ、Ｓｂ、０．１％以下のＣｕ、
Ｃｒ、または、０．０１％以下のＶ、Ｚｒなどは許容さ
れ、これらを含有しても、本発明の効果は損なわれな
い。Other elements are not particularly limited, but 70 ppm or less of Sn and Sb, 0.1% or less of Cu,
Cr, or 0.01% or less of V, Zr and the like are acceptable, and the inclusion of these does not impair the effects of the present invention.
【００２０】次に、本発明のシャドウマスク原板の製造
工程について説明する。本発明では、上記組成を満たす
鋼を、熱間圧延および酸洗後、冷間圧延し、次いで、連
続焼鈍し、その後２次冷間圧延を行い、シャドウマスク
原板を製造する。Next, the manufacturing process of the shadow mask original plate of the present invention will be described. In the present invention, steel satisfying the above composition is hot-rolled, pickled, cold-rolled, continuously annealed, and then secondary cold-rolled to produce a shadow mask original plate.
【００２１】連続焼鈍は、再結晶温度以上８５０℃以下
の範囲で均熱した後、６００〜４００℃の温度域を１０
℃/sec以上、４００℃未満を５℃/sec以下で冷却する条
件で行う。In the continuous annealing, after soaking in the range of recrystallization temperature to 850 ° C., the temperature range of 600 to 400 ° C. is 10 times.
It is performed under the condition of cooling at 5 ° C / sec or more and less than 400 ° C at 5 ° C / sec or less.
【００２２】均熱温度を再結晶温度以上８５０℃以下と
するのは、再結晶温度未満では、続く冷延−焼鈍後の組
織が不均一となって、成形時に不均一変形が生じシャド
ウマスクの品質が著しく劣化し、また、８５０℃を超え
ると組織が著しく粗大化して、やはりシャドウマスクの
品質に悪影響を及ぼすためである。The soaking temperature is set to be not lower than the recrystallization temperature and not higher than 850 ° C. When the recrystallization temperature is lower than the recrystallization temperature , the structure after the subsequent cold rolling-annealing becomes non-uniform, resulting in non-uniform deformation during molding. This is because the quality is remarkably deteriorated, and when the temperature exceeds 850 ° C. , the structure is remarkably coarsened and the quality of the shadow mask is also adversely affected.
【００２３】このように均熱した後の冷却パターンは本
発明において固溶ＣをＦｅ3 Ｃとして析出させる上で重
要である。まず、６００〜４００℃の温度域を10℃/sec
以上で冷却するが、これはこの温度域を急冷することに
よりＣの過飽和度を高めるためである。続いて、４００
℃未満を５℃/sec以下で冷却するが、これは、冷却速度
が５℃/secを超えると、過飽和となったＣが酸化物、硫
化物、窒化物あるいはこれらの複合化物を核として析出
できなくなるためである。The cooling pattern after soaking is important in the present invention in order to precipitate solid solution C as Fe 3 C. First, the temperature range of 600-400 ℃ is 10 ℃ / sec
The cooling is performed as described above, in order to increase the supersaturation degree of C by rapidly cooling in this temperature range. Then 400
It is cooled below 5 ° C / sec at 5 ° C / sec or less, but when the cooling rate exceeds 5 ° C / sec, supersaturated C precipitates with oxides, sulfides, nitrides or their composites as nuclei. This is because it will not be possible.
【００２４】なお、この連続焼鈍において、Ｆｅ3 Ｃの
析出が進行しやすい３００〜４００℃で30〜300 秒保持
する熱サイクルを加えれば、固溶Ｃの減少が促進される
ので好ましい。In this continuous annealing, it is preferable to add a heat cycle in which the precipitation of Fe 3 C is maintained at 300 to 400 ° C. for 30 to 300 seconds, because the reduction of solid solution C is promoted.
【００２５】このように、本発明で規定する鋼成分を1
次冷延後、所定の熱サイクルで連続焼鈍して固溶Ｃから
介在物を核に析出したＦｅ3 Ｃは、続く２次冷延−エッ
チング後のユーザー焼鈍での均熱においても再溶解しに
くく、その後の冷却においても再析出しやすくなるの
で、最終製品段階での降伏点伸びを極めて小さくするこ
とができる。Thus, the steel composition specified in the present invention is 1
After the subsequent cold rolling, the Fe 3 C continuously annealed in a predetermined heat cycle to precipitate inclusions from the solid solution C in the nucleus is re-melted even in the soaking during the user annealing after the subsequent secondary cold rolling-etching. Since it is difficult to reprecipitate in the subsequent cooling, the yield point elongation in the final product stage can be made extremely small.
【００２６】[0026]
【実施例】次に、本発明の実施例について説明する。ま
ず、表１に示す本発明の組成を満たす鋼Ａ〜Ｏおよびそ
の範囲から外れる比較鋼ａ〜ｔを転炉で出鋼し鋳造した
後、熱間圧延により板厚２．８ｍｍの鋼帯とした。これ
ら鋼帯を酸洗した後、０．６５ｍｍに冷間圧延して表２
に示す連続焼鈍熱サイクルで焼鈍を施した。EXAMPLES Next, examples of the present invention will be described. First, steels A to O satisfying the composition of the present invention shown in Table 1 and comparative steels a to t out of the range are tapped in a converter and cast, and then hot rolled to form a steel strip having a plate thickness of 2.8 mm. did. After pickling these steel strips, cold rolling them to 0.65 mm
Annealing was performed by the continuous annealing heat cycle shown in.
【００２７】この焼鈍板に再度冷間圧延を施して０．２
５ｍｍに仕上げ、シャドウマスク原板とした。その後、
エッチング−焼鈍（６２０℃×２０分）−レベラー掛け
−プレス成形を施した。表３に、２次冷圧−焼鈍後のサ
ンプルの降伏点伸び、エッチング特性およびプレス成形
性の結果を示す。なお、エッチング特性を評価したの
は、エッチング特性が悪いと、エッチング孔の形状がく
ずれて画面品質に悪影響を及ぼし、結果として色ずれが
生じるからである。また、成形性を評価したのは、原板
の降伏点伸び（ＹＰＥｌ）が高い場合には、レベラー掛
け後でもＹＰＥｌが残り、プレス成形時にストレッチャ
ーストレイン（ＳＳ）が生じ、エッチング孔がずれて画
面品質に悪影響を及ぼすからである。これらの評価は、
エッチング後に光線を照射し、検査員が光線の透過むら
があるか否かを検査し、むらがないものを良好、むらが
あるものをエッチングに起因するものか成形性に起因す
るものかによりいずれかまたは両方を不良とし、表２に
○、×で示した。The annealed sheet was cold-rolled again to 0.2
It was finished to 5 mm and used as a shadow mask original plate. afterwards,
Etching-annealing (620 ° C. × 20 minutes) -leveler application-press molding was performed. Table 3 shows the results of yield point elongation, etching characteristics and press formability of the samples after the secondary cold pressure-annealing. The etching characteristic was evaluated because if the etching characteristic is poor, the shape of the etching hole is deformed and the screen quality is adversely affected, resulting in color shift. In addition, the moldability was evaluated when the yield elongation (YPEl) of the original plate was high, YPEl remained even after leveling, stretcher strain (SS) occurred during press molding, and the etching hole was displaced, resulting in a screen error. This is because it adversely affects the quality. These ratings are
After etching, irradiate a light beam, the inspector inspects whether there is unevenness of transmission of the light ray, if there is no unevenness is good, depending on whether unevenness is due to etching or moldability Either or both were judged to be defective, and shown in Table 2 as ◯ and ×.
【００２８】[0028]
【表１】 [Table 1]
【００２９】[0029]
【表２】 [Table 2]
【００３０】[0030]
【表３】 [Table 3]
【００３１】表３から明らかなように、Ｎｏ．２５〜４
４のサンプルのように成分が適正でないものは、エッチ
ング特性が劣っていたり、成形性が劣っていることが確
認された。また、Ｎｏ．１，８，１０，１５，１９，２
２のように成分が本発明範囲内にある鋼でも、連続焼鈍
の熱サイクルが適切でなものでは、成形性が劣っている
ことが確認された。As is apparent from Table 3, No. 25-4
It was confirmed that, in the case where the components were not proper such as the sample of No. 4, the etching characteristics were inferior or the moldability was inferior. In addition, No. 1,8,10,15,19,2
It was confirmed that even in the steel having the components within the range of the present invention as in Example 2, the formability was inferior when the thermal cycle of continuous annealing was appropriate.
【００３２】これに対して、本発明の組成および連続焼
鈍熱サイクル条件を満たすＮｏ．２〜７，９，１１〜１
４，１６〜１８，２０，２１，２３はエッチング性およ
び成形性のいずれもが優れた結果であることが確認され
た。On the other hand, No. 3 which satisfies the composition and continuous annealing thermal cycle conditions of the present invention. 2-7, 9, 11-11
It was confirmed that 4,16 to 18,20,21,23 had excellent etching properties and moldability.
【００３３】特に、６００〜４００℃での冷却速度が３
０℃/sec以上になると降伏点伸びが０．１％以下とな
り、これらのサンプルでは、２次冷圧−焼鈍後のレベラ
ー掛けを省略しても良好な成形性を示した。Particularly, the cooling rate at 600 to 400 ° C. is 3
At 0 ° C./sec or more, the yield point elongation became 0.1% or less, and these samples showed good formability even if the leveling after secondary cold pressure-annealing was omitted.
【００３４】また、これらの中で３００〜４００℃の範
囲で３０〜３００秒保持する工程を付加したＮｏ．５，
７，９，１２，１４，１８，２３についても降伏点伸び
が０．１％以下と低い値となった。Further, among these, No. 3 added with a step of holding in the range of 300 to 400 ° C. for 30 to 300 seconds. 5,
The yield point elongations of 7, 9, 12, 14, 18, and 23 were as low as 0.1% or less.
【００３５】なお、図２に２次冷圧−焼鈍後のサンプル
の降伏点伸びに及ぼす連続焼鈍熱サイクルでの６００〜
４００℃の冷却速度の影響を示す。この図は、表２の中
で，Ｘ≦５のものをプロットしたものである。この図か
ら明らかなように、連続焼鈍における６００〜４００℃
の冷却速度が１０℃/secを満たす場合に、２次冷圧−焼
鈍後の降伏点伸びが０．２％以下と非常に良好な成形性
を有するシャドウマスク原板が得られる。なお、図中、
白丸、黒丸は本発明例であり、白丸が３００〜４００℃
での保持なしのもの、黒丸が３００〜４００℃での保持
ありのものである。また三角、白四角、黒四角はいずれ
も比較例であり、三角は４×（Ｃ／１２）-0.5≦Ｘ≦５
を満たすが、連続焼鈍の熱サイクルが本発明の範囲から
外れるもの、白四角は連続焼鈍の熱サイクルは本発明の
範囲内であるが適当であるが、４×（Ｃ／１２）-0.5＞
Ｘであるもの、黒四角は連続焼鈍の熱サイクルが本発明
の範囲から外れ、４×（Ｃ／１２）-0.5＞Ｘであるもの
を示す。It should be noted that, in FIG. 2, the value of 600-in the continuous annealing thermal cycle exerted on the yield point elongation of the sample after the secondary cold pressure-annealing.
The effect of a cooling rate of 400 ° C. is shown. This figure is a plot of X ≦ 5 in Table 2. As is clear from this figure, 600 to 400 ° C. in continuous annealing
When the cooling rate of 10 ° C./sec is satisfied, a shadow mask original plate having a very good formability such that the yield point elongation after secondary cold pressure-annealing is 0.2% or less is obtained. In the figure,
White circles and black circles are examples of the present invention, and white circles are 300 to 400 ° C.
In the black circle, and those with a black circle at 300 to 400 ° C. Triangles, white squares and black squares are all comparative examples, and the triangle is 4 × (C / 12) −0.5 ≦ X ≦ 5.
Although the thermal cycle of continuous annealing is out of the range of the present invention, the white squares are suitable although the thermal cycle of continuous annealing is within the range of the present invention, but 4 × (C / 12) −0.5 >
X is a black square, and the thermal cycle of continuous annealing is out of the scope of the present invention and 4 × (C / 12) −0.5 > X.
【００３６】[0036]
【発明の効果】以上説明したように、本発明によれば、
脱炭焼鈍を省略し、なおかつ連続焼鈍が短時間であって
も、エッチング性等が良好なシャドウマスク原板を得る
ことができる。As described above, according to the present invention,
Even if decarburization annealing is omitted and continuous annealing is performed for a short time, it is possible to obtain a shadow mask original plate having good etching properties and the like.
【図１】Ｃ量と（Ｏ／１６）＋０．５×（Ｓ／３２）＋
０．２×（Ｎ／１４）の値の適正範囲を示す図。FIG. 1 C amount and (O / 16) + 0.5 × (S / 32) +
The figure which shows the appropriate range of the value of 0.2x (N / 14).
【図２】２次冷圧−焼鈍後のサンプルの降伏点伸びに及
ぼす連続焼鈍での600 〜400 ℃の冷却速度の影響を示す
図。FIG. 2 is a diagram showing the influence of a cooling rate of 600 to 400 ° C. in continuous annealing on the yield point elongation of a sample after secondary cold pressure-annealing.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 細谷 佳弘 東京都千代田区丸の内一丁目１番２号 日本鋼管株式会社内 (56)参考文献 特開 昭56−139625（ＪＰ，Ａ) 特開 昭59−110731（ＪＰ，Ａ) 特開 平９−227998（ＪＰ，Ａ) 特開 平８−27541（ＪＰ，Ａ) 特開 平６−330167（ＪＰ，Ａ) 特公 昭60−30727（ＪＰ，Ｂ１) 特公 昭63−40848（ＪＰ，Ｂ１) (58)調査した分野(Int.Cl.7，ＤＢ名) C21D 9/46 C22C 38/00 301 C22C 38/06 ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Yoshihiro Hosoya 1-1-2 Marunouchi, Chiyoda-ku, Tokyo Inside Nippon Kokan Co., Ltd. (56) References JP-A-56-139625 (JP, A) JP-A-59 -110731 (JP, A) JP-A-9-227998 (JP, A) JP-A-8-27541 (JP, A) JP-A-6-330167 (JP, A) JP-B-60-30727 (JP, B1) ) JP-B-63-40848 (JP, B1) (58) Fields investigated (Int.Cl. 7 , DB name) C21D 9/46 C22C 38/00 301 C22C 38/06
Claims (2)
５％、Ｓｉ：０．１％以下、Ｍｎ：０．１〜０．３％、
Ｐ：０．０１５％以下、Ｓ：０．００５〜０．０１５
％、ｓｏｌ．Ａｌ：０．０１〜０．０８％、Ｎ：０．０
０２〜０．００７％、Ｏ：０．００１５〜０．００４％
を含有し、かつＣ、Ｏ、Ｓ、Ｎがｐｐｍで４×（Ｃ／１
２）−０．５≦（Ｏ／１６）＋０．５×（Ｓ／３２）＋
０．２×（Ｎ／１４）≦５を満たす鋼を、熱間圧延およ
び酸洗後、冷間圧延し、次いで、連続焼鈍を、再結晶温
度以上８５０℃以下の範囲で均熱した後、６００〜４０
０℃の温度域を１０℃／sec以上、４００℃未満を５℃
／sec以下で冷却する条件で行い、その後冷間圧延によ
り製品厚さとすることを特徴とするシャドウマスク原板
の製造方法。1. C: 0.001-0.003 by weight%.
5%, Si: 0.1% or less, Mn: 0.1 to 0.3%,
P: 0.015% or less, S: 0.005 to 0.015
%, Sol. Al: 0.01 to 0.08%, N: 0.0
02-0.007%, O: 0.0015-0.004%
And C, O, S, N in ppm are 4 × (C / 1
2) −0.5 ≦ (O / 16) + 0.5 × (S / 32) +
Steel satisfying 0.2 × (N / 14) ≦ 5 is hot-rolled, pickled, cold-rolled, and then subjected to continuous annealing in a range of recrystallization temperature or higher and 850 ° C. or lower, 600-40
10 ° C / sec or more in the temperature range of 0 ° C, 5 ° C below 400 ° C
The method for producing a shadow mask original plate is characterized in that cooling is performed at a cooling rate of not more than 1 sec / sec and then the product thickness is obtained by cold rolling.
℃の範囲で３０〜３００秒保持する工程を有することを
特徴とする請求項１に記載のシャドウマスク原板の製造
方法。2. The continuous annealing further comprises 300 to 400.
The method for manufacturing a shadow mask original plate according to claim 1, further comprising a step of maintaining the temperature in the range of 30 to 300 seconds.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP20963595A JP3410873B2 (en) | 1995-08-17 | 1995-08-17 | Manufacturing method of shadow mask master by continuous annealing |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP20963595A JP3410873B2 (en) | 1995-08-17 | 1995-08-17 | Manufacturing method of shadow mask master by continuous annealing |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0953122A JPH0953122A (en) | 1997-02-25 |
| JP3410873B2 true JP3410873B2 (en) | 2003-05-26 |
Family
ID=16576061
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP20963595A Expired - Fee Related JP3410873B2 (en) | 1995-08-17 | 1995-08-17 | Manufacturing method of shadow mask master by continuous annealing |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3410873B2 (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100328077B1 (en) * | 1997-12-20 | 2002-05-10 | 이구택 | Cold rolled steel sheet for shadow mask and a method of manufacturing thereof |
| AU2571700A (en) * | 1999-02-19 | 2000-09-04 | Toyo Kohan Co. Ltd. | Shadow mask material for color picture tube, shadow mask and color picture tube |
-
1995
- 1995-08-17 JP JP20963595A patent/JP3410873B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0953122A (en) | 1997-02-25 |
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