200948985 六、發明說明： 【發明所屬之技術領咸】 本發明係關於適合祚為在熔接等之三片加工和DI等之二 片加工後進行直徑形狀之縮小和放大加工之罐用素材的古 強度罐用鋼板及其製造方法。 ‘ 【先前技術】 近年來’以減低費用為目的，又’以削減顧資材和減輕 ° 環境負荷為目的，已進行用以減薄素材鋼材(鋼板)之製品板 厚的製品開發。 又’因為製品板厚減薄則剛性降低，故為了彌補此剛性的 降低，亦必須圖謀鋼材的高強度化。但是，於圖謀鋼材之高 強度化時，因為硬質化，以凸緣加工和頸縮加工時有發生= 痕的問題。 對於上述’現在’已提案有各種製造方法。 例如，於專利文獻丨中，提案有將鋼中成分管理於一定範 圍上’於⑽變態點-3(rc)以上施行熱軋’且於冷軋後，進 行連續退火的方法。 但是，專利文獻！之方法中，因為令P為〇〇2wt%以下， 使凸緣加工性、頸縮加工性及_性不會惡化，更且令二_欠 冷㈣軋縮率為15〜3G%，因此難以有效率處理薄 有容易發生外觀;^的問題。又，難以安定製造必須改盖。 又，於專利文獻2中，提案有將鋼中成分及固熔 098111149 3 200948985 於一定範圍上，於(Ar3變態點-30°C)以上施行熱軋，進行既 定之冷卻、捲取、水冷，進行冷軋後，進行既定之加熱圖案 的連續退火，製造具有塗敷燒結處理後之屈服應力：550MPa 以上之罐用鋼板的方法。 但是，專利文獻2之方法中，為半極低碳材，且為了確保 既定的固熔N而提高連續退火的溫度，更且難以嚴格管理 加熱圖案，具有難以生產的問題。又，僅單單確保鋼中N 之80%以上的固熔N，由於鋼中N含量的偏差，故難以安 定製造既定強度的鋼板，必須加以改善。又，專利文獻2 之方法中係全部伸度變小，加工性惡化。 更且，作為高強度之罐用鋼板的代表性製造方法，已提案 有下述方法。根據退火種類適當選擇使用（例如，非專利文 獻1)。 熱軋-> 酸洗-> 冷軋—箱型退火（BAF)—第2回冷軋（軋縮 率：20〜50%) 熱軋—酸洗—冷軋—連續退火（CAL)—第2回冷軋（軋縮 率：20〜50°/〇) 但是，上述之方法中，第2回之冷軋的軋縮率高達 20〜50%，因軋製荷重高，使得操作能率變低。又，在提高 軋製時之潤滑性的目的下，使用高黏度的各種軋製油，故具 有因軋製油之濃度不勻和部分油附著所造成之軋製後之外 觀不良的問題。更且，在軋製軋縮率高之情況，全部伸度變 098111149 4 200948985 小’加性惡化’又’因為鋼板經幸L製而被延伸，故根據素 材之製造方向和加工方向之寬度方向與長度方向的耐力差 變大。 對於此情況’考慮壓低第2回冷軋之軋縮率的方法。但 是’於減低軋縮率的情況，難以取得必要的耐力。 專利文獻1:日本專利第3108615號公報 專利文獻2 :日本專利特開2〇〇ι_ι〇7187號公報 Ο 非專利文獻1 :「我國之罐用表面處理鋼板之技術史」曰 本鐵鋼協會平成10年10月3〇日發行p i88 如此’於欲取得製品板厚薄之罐用鋼板的情況，在目前狀 況為未有令強度與生產性兩相成立的製造方法，期望此種製 造方法。 本發明為鑑於此類情事而完成，以提供塗敷•燒結處理後 之屈服應力YP為具有5〇〇MPa以上之強度之罐用鋼板及其製 ® 造方法為其目的。 【發明内容】 本發明為如下述。 [1] 一種高強度罐用鋼板，其特徵為，以質量％計含有c : 超過〇. 02%且為0. 10%以下、Si : 〇. 1〇%以下、Mn: L 5%以下、 P . 0.20%以下、S : 〇. 20%以下、A1 : 〇 1〇%以下、N : 〇. 0120〜〇. 0250%，且該N中含有〇. 〇1〇〇%以上固熔N，殘餘 部分為Fe及不可避免的雜質所構成。 098111149 200948985 [2] 如[1]中記載之高強度罐用鋼板，其中表面具有鍍敷 層。 [3] 一種高強度罐用鋼板之製造方法，其特徵為，將以質 量％計含有C :超過0. 02%且為0. 10%以下、Si : 0. 10%以下、 Mn : 1. 5%以下、P : 0. 20%以下、S : 0. 20%以下、A1 : 0. 10% 以下、Ν : 0. 0120〜0. 0250%，殘餘部分為Fe及不可避免的雜 質所構成之鋼胚，實施胚萃取溫度設為1200°C以上、精軋 溫度設為（Ar3變態點溫度-30)°C以上之熱軋，並以650°C以 下捲取，施行酸洗後，施行冷軋，其次，施行連續退火。 [4] 如[3]中記載之高強度罐用鋼板之製造方法，其中，於 上述連續退火後，施行將軋縮率設為10%以上未滿20%之第 2回冷軋。 [5] 如[3]或[4]中記載之高強度罐用鋼板之製造方法，其 中，上述連續退火之均熱溫度設為Arl變態點溫度以上。 [6] 如[3]〜[5]中任一項記載之高強度罐用鋼板之製造方 法，其中，於上述連續退火或上述第2回冷軋後，施行鑛敷 處理。 另外，於本說明書中，表示鋼成分的％，全部為質量％。又， 於本發明中，所謂「高強度罐用鋼板」，係指塗敷·燒結處 理後具有屈服應力YP為500MPa以上之強度的罐用鋼板。 又，本發明之高強度罐用鋼板係以罐用素材作為對象。更 且，不論有無表面處理，施行鍍錫、鍍鎳錫、鍍鉻（所謂無 098111149 6 200948985 锡鍛敷）、或者進—步被覆有機物等，可於極廣範圍之用途 中應用。 更且’關於鋼板的厚度並無特別限定，由可最大限度活用 本發明效果之方面而言’板厚0. 3丽以下、更且以〇. 2mm 以下為佳。特佳者為0. 170mm以下。 【實施方式] 本發明者等人為了解決上述課題而進行致力研究。其結 ❹果，得到以下之發現。 發現成分組成中’作成低碳材’且將固熔N量之絕對量確 保於定以上，且於製罐加工前施行之印刷步驟或薄膜層合 步驟、乾燥•燒結步驟等，以淬火時效及應變時效進行硬化， 則可確保高強度之材質。 如上述，本發明係管理根據上述發現的成分，而達到完成 高強度罐用鋼板。 φ 以下，詳細說明本發明。 本發月之间強度罐用鋼板，係於塗敷•燒結處理後具有屈 服應力YP為5〇〇Mpa以上之強度的罐用鋼板。 其-人’本發明中，係作成低碳材，將固溶N量之絕對 保一定以上，承0 更且，經由塗敷燒結處理後之時效硬化，未進 行人冷軋、或者進行低軋縮率之二次冷軋，則可提高生產 T且提高罐用鋼板之生產性並且變成可高強度化。未進行二 -人冷軋、即在連續退火後施行左右之調質軋製所得的冷 098111149 7 200948985 乳鋼板，係於塗敷•燒結處理後具有全部伸度ei為挪以 上。 說明關於本發明之容器用鋼板之成分組成。 C :超過0. 02%且為〇. 10%以下 C為經由固熔強化令鋼強度增加的有效元素，另一方面， 形成碳化物，且令鋼板的延性、進而令加卫性降低。c成分 若較多，齡二次冷軋後_板硬質化，且製罐性和頸縮加 工性惡化。又，成為因熔接部的顯著硬質化，使得凸緣加工 時產生HAZ裂開的元素。c若超過〇1〇%，則此等影響變得 』著故將C疋為〇 1〇%以下。另一方面，若c成分極端變 低’則有若不將二次冷軋軌縮率設為⑽以上的強壓下， 則無法確保強度的_，故將C定為超過〇. 〇2%。C以〇. 03% 以上、0. 05%以下為佳。200948985 VI. Description of the Invention: [Technical Fields of the Invention] The present invention relates to a material for cans which is suitable for the reduction and enlargement of the diameter shape after the three-piece processing such as welding and the two-piece processing of DI and the like. Steel sheet for strength cans and a method for producing the same. 『 [Prior Art] In recent years, in order to reduce costs, the company has developed products for thinner material steel (steel sheet) for the purpose of reducing the amount of materials and reducing the environmental load. Further, since the rigidity of the product is reduced, the rigidity is lowered. Therefore, in order to compensate for the decrease in rigidity, it is necessary to increase the strength of the steel material. However, when the strength of the steel is increased, the problem of the occurrence of the mark is caused by the flange processing and the necking process due to the hardening. Various manufacturing methods have been proposed for the above-mentioned 'now'. For example, in the patent document, a method of subjecting a steel component to a certain range to perform hot rolling at (10) metamorphosis point -3 (rc) or more and performing continuous annealing after cold rolling is proposed. However, the patent literature! In the method, since P is 〇〇 2 wt% or less, the flange workability, the necking workability, and the _ property are not deteriorated, and the second undercooling (four) rolling reduction ratio is 15 to 3 G%, which is difficult. Efficient handling of thin ones is prone to appearance; ^ problems. Moreover, it is difficult to stabilize the manufacturing and must be replaced. Further, in Patent Document 2, it is proposed to carry out hot rolling by subjecting steel components and solid-melting 098111149 3 200948985 to a certain range, and performing predetermined cooling, coiling, and water cooling at (Ar3 transformation point - 30 ° C). After the cold rolling, continuous annealing of a predetermined heating pattern is performed to produce a steel sheet for a can having a yield stress of 550 MPa or more after the sintering treatment. However, in the method of Patent Document 2, it is a semi-polar low-carbon material, and in order to secure a predetermined solid solution N, the temperature of continuous annealing is increased, and it is difficult to strictly manage the heating pattern, which is difficult to produce. Further, only the solid solution N of 80% or more of N in the steel is ensured, and since the N content in the steel varies, it is difficult to stably manufacture a steel sheet having a predetermined strength, and it is necessary to improve it. Further, in the method of Patent Document 2, the total elongation is small, and the workability is deteriorated. Further, as a representative production method of a high-strength steel sheet for cans, the following method has been proposed. It is appropriately selected depending on the type of annealing (for example, Non-Patent Document 1). Hot Rolling->Pickling-> Cold Rolling-Box Annealing (BAF) - 2nd Cold Rolling (Rolling Rate: 20~50%) Hot Rolling - Pickling - Cold Rolling - Continuous Annealing (CAL) - The second cold rolling (rolling reduction ratio: 20 to 50 ° / 〇) However, in the above method, the second rolling cold rolling has a rolling reduction of 20 to 50%, and the operating load rate is changed due to the high rolling load. low. Further, in order to improve the lubricity during rolling, various high-viscosity rolling oils are used, which causes a problem of poor appearance after rolling due to uneven concentration of the rolling oil and partial oil adhesion. Moreover, in the case of high rolling reduction, all the elongations become 098111149 4 200948985 small 'additive deterioration' and 'because the steel plate is extended by the L system, so according to the manufacturing direction of the material and the width direction of the processing direction The difference in endurance with the length direction becomes large. In this case, a method of lowering the rolling reduction ratio of the second cold rolling is considered. However, it is difficult to obtain the necessary endurance in the case of reducing the rolling reduction rate. Patent Document 1: Japanese Patent No. 3108615 Patent Document 2: Japanese Patent Laid-Open No. 2〇〇ι_ι〇7187 Ο Non-Patent Document 1: "Technical History of Surface Treated Steel Sheets for Cans in China", Sakamoto Iron and Steel Association, Heisei In the case of the steel sheet for the cans of the product sheet thickness, the manufacturing method for the strength and the production phase is established in the current situation. The present invention has been made in view of such circumstances, and it is an object of the present invention to provide a steel sheet for cans having a strength of 5 MPa or more after application and sintering treatment, and a method for producing the same. SUMMARY OF THE INVENTION The present invention is as follows. [1] A high-strength steel sheet for a can, characterized in that it contains, by mass%, c: more than 〇. 02% and is 0. 10% or less, Si: 〇. 1〇% or less, and Mn: L 5% or less. P. 0.20% or less, S: 〇. 20% or less, A1: 〇1〇% or less, N: 〇. 0120~〇. 0250%, and the N contains 〇. 〇1〇〇% or more of solid-melting N, The remainder is composed of Fe and unavoidable impurities. 098111149 200948985 [2] The steel sheet for high-strength cans according to [1], wherein the surface has a plating layer. [ 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 5% or less, P: 0. 20% or less, S: 0. 20% or less, A1: 0. 10% or less, Ν: 0. 0120~0. 0250%, the remainder is Fe and inevitable impurities For the steel embryo, the embryo extraction temperature is set to 1200 ° C or higher, and the finish rolling temperature is set to (Ar3 transformation point temperature -30) ° C or higher hot rolling, and the coil is taken at 650 ° C or lower, and after pickling, it is carried out. Cold rolling, and second, continuous annealing is performed. [4] The method for producing a steel sheet for high-strength cans according to the above [3], wherein after the continuous annealing, the second cold rolling is performed at a rolling reduction ratio of 10% or more and less than 20%. [5] The method for producing a steel sheet for high-strength cans according to [3] or [4], wherein the soaking temperature of the continuous annealing is equal to or higher than the Arl transformation temperature. [6] The method for producing a steel sheet for high-strength cans according to any one of [3] to [5] wherein, after the continuous annealing or the second cold rolling, the mineralizing treatment is performed. In addition, in this specification, the % of steel components is all the mass %. In the present invention, the "high-strength steel sheet for a can" refers to a steel sheet for a can having a strength of a yield stress YP of 500 MPa or more after coating and sintering. Moreover, the steel sheet for high-strength cans of the present invention is intended for the material for cans. In addition, tin plating, nickel-plated tin plating, chrome plating (so-called 098111149 6 200948985 tin forging), or further coating of organic materials can be applied to a wide range of applications, with or without surface treatment. Further, the thickness of the steel sheet is not particularly limited, and it is preferably 0. 3 Å or less, more preferably 〇 2 mm or less, from the viewpoint of maximizing the effect of the present invention. The best is 0. 170mm or less. [Embodiment] The inventors of the present invention have made efforts to solve the above problems. As a result, the following findings were obtained. It is found that the composition of the composition is 'made into a low carbon material' and the absolute amount of the solid solution N is ensured to be more than or equal to the above, and the printing step or the film lamination step, the drying and sintering step, etc., which are performed before the canning process, are quenched and aged. Hardening by strain aging ensures high strength materials. As described above, the present invention manages the completion of the high-strength steel sheet for cans based on the components found above. Hereinafter, the present invention will be described in detail. The steel sheet for strength cans between the month of the month is a steel sheet for cans having a strength of a yield stress YP of 5 〇〇Mpa or more after coating and sintering treatment. In the present invention, it is made into a low-carbon material, and the amount of solid solution N is kept to a certain level or more, and the age is further suppressed by the coating and sintering treatment, and no cold rolling or low rolling is performed. In the second cold rolling of the shrinkage ratio, the production T can be improved and the productivity of the steel sheet for cans can be improved and the strength can be increased. The cold-transformed 098111149 7 200948985 steel plate obtained by cold-rolling, that is, after continuous annealing, is subjected to continuous annealing, and has a full elongation ei of more than or equal to the coating and sintering treatment. The composition of the steel sheet for containers of the present invention will be described. C: more than 0.02% and 〇. 10% or less C is an effective element for increasing the strength of steel by solid solution strengthening, and on the other hand, carbide is formed, and the ductility of the steel sheet and the refractory property are lowered. If there are many c-components, the plate is hardened after the second cold rolling, and the potability and necking workability are deteriorated. Further, since the welded portion is remarkably hardened, an element in which the HAZ is cracked during the flange processing is caused. If c exceeds 〇1〇%, then these effects become "caused" and C疋 is 〇1〇% or less. On the other hand, if the c-component is extremely low, if the secondary cold-rolling rail shrinkage ratio is not higher than (10), the strength cannot be ensured, so C is set to exceed 〇. 〇 2%. C% 03. 03% or more, preferably 0. 05% or less.
Si : 0. 10%以下 為、星由固溶強化令鋼強度增加的元素’但大量添加則發 生表面處理性惡化、_性惡化等問題，故將Si限定於 0· 10%以下。另休 、 卜’尤其在要求優良耐姓性的情況，Si定為 0.02%以下為佳。 ‘Si: 0. 10% or less is an element in which the strength of the steel is increased by solid solution strengthening. However, when a large amount is added, problems such as deterioration of surface treatment property and deterioration of _ properties occur, so Si is limited to 0. 10% or less. In addition, in the case of requiring excellent resistance to surnames, Si is preferably 0.02% or less. ‘
Mn : 1. 5% 以下 曰Μη為有效防止因s造成之熱裂開的元素。因此，根據s 置予以適當添加，則可取得防止裂開的效果。於料此等效 乂添加〇. 2〇%以上為佳。又，亦具有令結晶粒微細 098111149 200948985 化的作用。另一方面，若 日,,郎-山 w右大1添加，則顯不出耐蝕性亞 ::二化至所需以上，且凸緣—縮 加性』，故上限定為1. 5%。Μη以0· 20%以上、〇. 3〇%以 下為佳。 ° Ρ : 0· 20%以下 Ρ雖""_著硬質化’但令凸緣加卫性和頸縮加工性惡 化，同時令耐飾性顯著惡化。因此，本發明中，將ρ限定為 © 0.20%以下。Ρ以〇._以上、〇.顯以下為佳。’，、、 S : 0. 20%以下 S於鋼中依中介物型式存在’係令鋼板的延性減少且令耐 • 射生惡化的凡素。因此’定為0.20%以下。S以0.001%以上、 0. 018%以下為佳。 Α1 : 0. 10%以下 A1係與固炫Ν結合’形成Α1Ν，具有減低固熔Ν量的效果。 曰 又’ A1含量的増加造成再結晶溫度的上升，且退火溫度必 須為高溫。高溫退火時，因為形成A1N，故固熔N量減低， 時效硬化量減低，因此造成鋼板強度降低。低碳材之情況 下，於A1含量為超過〇. 1〇%之時此類現象變得顯著。由此’ 將A1限定為〇. 1〇%以下。另外，就鋼熔製步驟中安定操作 的觀點而言’期望A1為0.020%以上。A1以0.020%以上、 0. 060%以下為佳。 N ： 0.0120-0.0250% 098111149 9 200948985 N為增加時效硬化性的元素，於本發明中，令其積極地含 有。時效硬化性的顯著增加，係於低碳材之情況下以含有 0. 0120%以上時可觀察見。另—方面，若含有超過 0.0250% ， 則於軋製素材⑻發生㈣缺陷的危險性顯著增^因此， 將N限定為0.0120%以上〇 〇25〇%以下。 罐用鋼板（冷軋鋼板）之固熔N : 〇· 〇1〇〇%以上 為了確保本發_徵之較大的時效硬純，必齡罐用鋼 板（冷軋鋼板）中_熔N量為㈣Q_上。其在本發明中 係最重要的要件。 本發明之冷軋鋼板，較佳係在將熱軋板酸洗後，予以冷 軋’進行連軌火，視需要騎第2回冷軋即可製造，作在 此連續退火步驟中有析出A1N的傾向，故管理令罐用鋼板 v L鋼板）中之固熔“未滿請〇_步驟實為重要。另 ^本發日种’根據料實施之細之熔解處理後的萃取分 析’求出變成A1N的N量f W -Γ ηMn : 1. 5% or less 曰Μη is an element effective to prevent thermal cracking due to s. Therefore, if it is appropriately added according to the s, the effect of preventing cracking can be obtained. It is expected that this equivalent 乂 is added 〇. 2% or more is better. In addition, it also has the effect of making the crystal grains fine 098111149 200948985. On the other hand, if the day, the lang-mountain w is added to the right, the corrosion resistance is not shown: the second is more than necessary, and the flange-shrinkage is limited, so the upper limit is 1.5%. . Μη is preferably 0. 20% or more, 〇. 3〇% or less. ° Ρ : 0·20% or less Ρ Although the ""_hardened, but the flange reinforcement and necking process deteriorate, and the durability is significantly deteriorated. Therefore, in the present invention, ρ is limited to © 0.20% or less. Ρ 〇. _ above, 〇. The following is better. ',,, S: 0. 20% or less S is present in the steel according to the type of the medium. The ductility of the steel sheet is reduced and the resistance to deterioration is caused. Therefore, it is set to be 0.20% or less. S is preferably 0.001% or more and 0.018% or less. Α1 : 0. 10% or less The A1 system is combined with the solid ’ ’ to form Α1Ν, which has the effect of reducing the amount of solid solution.曰 And the addition of the A1 content causes an increase in the recrystallization temperature, and the annealing temperature must be a high temperature. At the time of high-temperature annealing, since A1N is formed, the amount of solid-melting N is reduced, and the amount of age-hardening is reduced, so that the strength of the steel sheet is lowered. In the case of a low carbon material, such a phenomenon becomes remarkable when the A1 content is more than 0.1%. Thus, A1 is limited to 〇. 1〇% or less. Further, from the viewpoint of the stability operation in the steel melting step, it is desirable that A1 is 0.020% or more. A1 is preferably 0.020% or more and 0.060% or less. N: 0.0120-0.0250% 098111149 9 200948985 N is an element which increases age hardenability, and is actively contained in the present invention. A significant increase in the age hardenability is observed in the case of a low carbon material containing 0. 0120% or more. On the other hand, if the content exceeds 0.0250%, the risk of occurrence of defects in the rolled material (8) is remarkably increased. Therefore, N is limited to 0.0120% or more and 〇25% or less. Solid-state melting of steel sheet for cans (cold-rolled steel sheet): 〇·〇1〇〇% or more In order to ensure a large aging hardening of the hair _ _ _ _ _ _ _ _ _ _ _ For (four) Q_. It is the most important requirement in the present invention. The cold-rolled steel sheet of the present invention is preferably subjected to cold rolling after the pickling of the hot-rolled sheet, and is subjected to continuous rail fire, and can be manufactured by riding the second cold rolling as needed, for which A1N is precipitated in the continuous annealing step. The tendency to be solidified in the management of the can steel plate v L steel plate "The step is not important. The step is important. The other is the same as the extraction analysis after the melting treatment of the material." The amount of N that becomes A1N is f W -Γ η
量減去w ㈣下，稱為NasA1N)，將由全N 里減去Nas A1N之值定為固炼 二量與_c量合計以。._以上為佳。 的C*由全C量或者將鋼板所萃取之析嶋 殘餘部分為Fe及不可避免雜質。 作為=刀从外之殘餘部分為以及不可避免雜質。另外， °避免雜f，例如可容許Sn : G.G1%以下。 09811H49 200948985 其次，說明本發明之高強度罐用鋼板的製造方法。 本發明之高強度罐用鋼板係由下迷方法所獲得。首先，將 上述組成所構成的熔鋼使用轉爐等通常公知的熔製方法予 以溶製，並以連續鑄造法等之通常公知的铸造方法作成札製 素材（胚）。其:欠，使㈣料製素材，轉軋作成熱軋板。 此時，胚萃取溫度設為120〇。(：以上，精軋溫度設為（Ar3變 態點溫度-30)°C以上（適當為Ar3變態點溫度以上）。其次， ❸於650 C以下捲取，施行酸洗後，施行冷軋，並施行連續退 火。更且視需要，施行軋縮率10%以上、未滿2〇%之第2回 冷軋。又，亦可施行鍍敷處理。 以下’詳細說明。 胚萃取溫度：1201TC以上 罐用鋼板之固熔N量設為〇. 0100%以上，於加熱爐中插入 馨胚並加熱，由加熱爐萃取的溫度設為12〇〇°C以上。此係為 了促進A1N的分解，並且確保既定量的固熔N量。較佳係插 入於保持在此溫度的加熱爐中並加熱。 精軋溫度：（Ar3變態點-3〇。〇)以上 本發明中，為了有效抑制A1N的析出，進一步不產生異向 性與加工性的惡化，乃將熱軋中的精軋溫度定為（Ar3變態 點-30。〇以上。精軋溫度未滿（Ar3變態點_3〇。〇，則a1n 顯著析出，固熔N減低，產生異向性與加工性的惡化。另外， 較佳為Ar3變態點以上。 098111149 11 200948985 另外，精軋後， A1N的析出。 以水冷進行㈣料卩騎。如此，可抑制 捲取溫度：650°C以下 捲取溫度係為了抑制A1造成N之固定，而6以 下’捲取溫度若超過65(rc，則A1N析出量顯著增加且固溶 N減^ ’結果無法取得目標之時效硬化性。另外，為了穩定 取得高時效硬化性，更佳係將捲取溫度定為刪。c以下。另 ❹ 卜本發月中，較佳係於捲取後以卷圈之狀態予以空氣冷卻 或水冷為佳。水冷之情形，生產性雖可提高，但就鋼板之板 寬方向及長度方向之材質均勻性而言’以空氣冷卻為佳。 酸洗、冷札 對於如上處理製造的熱軋板，施行酸洗、冷軋，作成冷軋 板。酸洗為根據常法，以鹽酸、硫酸等酸除去表面銹皮即可。 冷札軋縮率亦根據常法，板厚愈薄則愈高。 〇 連續退火之均熱溫度：60(TC以上（較佳條件） 連續退火步驟中，以依6〇(Tc以上之溫度範圍予以均熱為 佳。均熱溫度若為600°c以上，則再結晶快速進行，經冷軋 所導入的加工應變無法殘留，延性高’適於壓製加工。更且， 若以Arl變態點以上進行均熱，則可更加提高強度故為佳。 若以Arl變態點以上進行均熱，則部分變成波來鐵組織推 察有助於強度。 又，若為此溫度範圍内，則不需特別保持於一定溫度。由 098111149 12 200948985 作業之安定性而言’若為相當於1仏以上之均熱時間則為充 分。 連續退火後’較佳係施行1%左右的調質札製，進行表面 粗度與硬度的調整。 經過上述步驟所得的冷軋鋼板，於塗敷•燒結處理後之全 申度E1為2G%以上，成為加工性極優的罐用鋼板。 ❹ 參 連續退火後，亦可進一步施行軋縮率：灌以上、未滿20% 之第2回冷軋4第2回冷軋係以進—步高強度化為主要目 的。經由作成1G%以上，可達成進一步高強度化，經由未滿 20% ’則可碟保延伸度且不會令加工性惡化並且取得上述高 強度化的效果。施行軋縮率：1〇%以上、未滿2〇%之第2 : ^軋的冷軋鋼板，係於塗敷•燒結處理後之全部伸度E1為 8%以上〜15%以下，具有優良之加讀且為極高強度的罐用鋼 板。軋縮率以10%以上、未滿15%為佳，取得塗敷·燒結處 理後之全部伸度E1為10%以上的冷軋鋼板。 經過上述步驟取得冷軋鋼板。其次，經由製罐加工前（壓 製加工前）的塗敷•燒結處理成為硬質材，應用於板厚為 〇. 3mm以下之極薄鋼板時，可更加有效發揮其優異性。又 根據上述步驟所製造的冷軋鋼板，係具有固熔N量為 0.0100%以上，成為具有塗敷•燒結處理後之屈服應力卯： 500MPa以上的高強度罐用鋼板。更且，本發明之 可取得較大延伸度，故加工性優良。 鋼板 098111149 13 200948985 本發明之罐用鋼板為經由固炼N跑”“ %侍較大的時致 性。因此，具有塗敷•燒結處理後之屈服應力γρ : $化 以上且使鋼板的薄化優異進展。又，本發 〇〇M?a +狄π之冷軋鋼极传 由有效利用固Μ的作用，錢敷後之迴流處理後的強度^ 增加，又，於壓製成形後之塗敷燒結步驟時亦引起顯著的時 效硬化現象，亦可造成罐體強度大幅地增加。 本毛月中係於上述所得之冷乳鋼板表面（至少單面）形成 鑛敷層，可作成鍍軸板。表面所形成的鍍敷層可應用罐用 鋼板所❹的任何物f。作為魏層，可例雜錫、鍛絡、 鑛鎳、鑛雜。又，此等鍍敷處理後，亦可塗敷、貼上有機 樹脂薄膜等無妨。 [實施例1] 將表1所不成分所構成之鋼以轉爐熔製，並以連續鑄造法The amount minus w (four), called NasA1N), is determined by subtracting the value of Nas A1N from all N into the total amount of solidification and _c. ._ above is better. The C* is determined by the total amount of C or the residual portion of the steel extracted by the steel sheet as Fe and inevitable impurities. As the residual part of the = knife from the outside and inevitable impurities. Further, ° avoids the impurity f, and for example, Sn: G.G1% or less can be tolerated. 09811H49 200948985 Next, a method of producing the steel sheet for high-strength cans of the present invention will be described. The steel sheet for high-strength cans of the present invention is obtained by the following method. First, the molten steel having the above-described composition is dissolved by a generally known melting method such as a converter, and a material (embryo) is prepared by a generally known casting method such as a continuous casting method. It: owe, make (4) material materials, turn into cold-rolled sheets. At this time, the embryo extraction temperature was set to 120 Torr. (The above, the finishing rolling temperature is set to (Ar3 transformation point temperature -30) °C or more (appropriately above the Ar3 transformation point temperature). Secondly, the crucible is taken up at 650 C or less, and after pickling, cold rolling is performed, and Continuous annealing is performed, and if necessary, the second cold rolling is performed at a rolling reduction ratio of 10% or more and less than 2% by weight. Further, plating treatment may be performed. The following is a detailed description. The embryo extraction temperature: 1201 TC or more The solid solution N amount of the steel sheet is set to 〇. 0100% or more, and the scented embryo is inserted into the heating furnace and heated, and the temperature extracted by the heating furnace is set to 12 〇〇 ° C or higher. This is to promote the decomposition of A1N and ensure The amount of solid-solid N is preferably inserted into a heating furnace maintained at this temperature and heated. Finishing temperature: (Ar3 metamorphic point - 3 〇. 〇) In the present invention, in order to effectively suppress precipitation of A1N, Further, the deterioration of the anisotropy and the workability is not caused, and the finish rolling temperature in hot rolling is determined to be (Ar3 metamorphic point -30. 〇 or more. The finishing rolling temperature is not full (Ar3 metamorphic point _3 〇. 〇, then a1n Significant precipitation, solid solution N reduction, resulting in deterioration of anisotropy and processability. It is preferably Ar3 metamorphic point or more. 098111149 11 200948985 In addition, after finish rolling, precipitation of A1N is carried out by water cooling (four) material riding. Thus, the coiling temperature can be suppressed: the coiling temperature is below 650 ° C to suppress A1. If it is more than 65 (rc, the amount of precipitation of A1N is significantly increased and the solid solution is reduced by N), the target age hardenability cannot be obtained. In addition, it is better to obtain high age hardenability for stability. The coiling temperature is set to be less than c. In addition, in this month, it is better to use air-cooling or water-cooling in the state of coiling after coiling. In the case of water cooling, the productivity can be improved, but In terms of material uniformity in the width direction and the longitudinal direction of the steel sheet, it is preferable to use air cooling. Pickling and cold rolling are performed on the hot-rolled sheet produced as described above by pickling and cold rolling to form a cold-rolled sheet. According to the conventional method, the surface scale can be removed by acid such as hydrochloric acid or sulfuric acid. The cold rolling reduction rate is also according to the conventional method, and the thinner the plate thickness is, the higher the homogenization temperature of continuous annealing is: 60 (TC or more (preferably) Condition) continuous annealing step According to the temperature range above Tc, it is better to use soaking. If the soaking temperature is above 600 °c, the recrystallization will proceed rapidly. The processing strain introduced by cold rolling cannot be left, and the ductility is high. In addition, if the soaking is performed at the Arl metamorphic point or higher, the strength can be further improved. If the soaking is performed at the Arl metamorphic point or more, the portion of the ferromagnetic structure is inferred to contribute strength. For this temperature range, it is not necessary to maintain a certain temperature. 098111149 12 200948985 The stability of the operation is 'sufficient if it is equivalent to 1 仏 or more. After continuous annealing' About 5% of the quenching and tempering, the surface roughness and hardness are adjusted. The cold-rolled steel sheet obtained by the above-described steps has a full-scale E1 of 2 G% or more after the coating and sintering treatment, and is a steel sheet for cans which is excellent in workability. After the continuous annealing of the ginseng, the rolling reduction ratio can be further applied: the second cold rolling of the second cold rolling and the second cold rolling of less than 20% is mainly for the purpose of increasing the strength of the step. When the content is 1 G% or more, the strength can be further increased, and if the thickness is less than 20%, the elongation can be maintained without deteriorating the workability, and the above-mentioned high strength can be obtained. The cold rolling steel sheet having a rolling reduction ratio of 1% or more and less than 2% by weight is excellent in the elongation E1 of 8% or more to 15% or less after coating and sintering treatment. It is a steel plate for cans that is read and is extremely high strength. The rolling reduction ratio is preferably 10% or more and less than 15%, and a cold-rolled steel sheet having a total elongation E1 of 10% or more after the coating and sintering treatment is obtained. Through the above steps, a cold rolled steel sheet is obtained. Then, it is made into a hard material by coating and sintering treatment before the can processing (before press processing), and when it is applied to an extremely thin steel sheet having a thickness of 〇. 3 mm or less, the superiority can be more effectively exhibited. Further, the cold-rolled steel sheet produced by the above-mentioned steps has a solid-solid N content of 0.0100% or more, and has a yield stress 卯 of 500 MPa or more after coating/sintering treatment. Further, the present invention can achieve a large elongation and is excellent in workability. Steel plate 098111149 13 200948985 The steel sheet for cans of the present invention is a time-dependent process by which the % of the steel plate is operated by the solidification. Therefore, the yield stress γρ after the coating and sintering treatment is not more than the above, and the thickness of the steel sheet is excellent. Moreover, the cold-rolled steel of the hairpin M?a + Di π is effectively utilized by the effect of solidification, and the strength after the reflow treatment after the application of the money is increased, and also during the coating and sintering step after the press forming. It causes significant age hardening and can also cause a significant increase in tank strength. In the present month, the surface of the cold-milk steel sheet obtained above (at least one side) is formed into a mineral coating layer, which can be used as a plated plate. The plating layer formed on the surface can be applied to any material f which is adhered to the steel plate for can. As the Wei layer, tin, forged, ore, and minerals can be used. Further, after the plating treatment, an organic resin film or the like may be applied or attached. [Example 1] The steel composed of the components not shown in Table 1 was melted in a converter and was continuously cast.
作為胚。其次，將此等胚，以表2所示之條件熱軋，作成扳 厚.2· 0賴的熱軋板。其次，對於上述所得之熱軋板以酸洗 施行脫錄處理，再施行冷軋，並以表2所示之條件進行速續 退火且一部分進行二次軋製，作成最終精軋板厚：〇17_ 的冷軋鋼板。 [表1]As an embryo. Next, these embryos were hot rolled under the conditions shown in Table 2 to prepare a hot rolled sheet having a thickness of 2,000 Å. Next, the hot-rolled sheet obtained above was subjected to pickling treatment by pickling, and then cold-rolled, and subjected to rapid annealing under the conditions shown in Table 2, and partially subjected to secondary rolling to prepare a final finish rolled sheet thickness: 17_ cold rolled steel plate. [Table 1]
化學成分（質量％) Μη )725 )730- 098111149 ).017 ).012 S "ο. 010 Τ 017 Α1 0. 035 0. 009 ΤΓ0Τ48^ 〇. 〇16〇_ 14 200948985 [表2] 鋼板 鋼 Ar3 熱軋 冷軋 Arl 連續退火 二次冷軋 No No 變態點 胚萃 精軋 揍取 軋縮率 變態點 退火 均熱 軋縮率 取溫度 溫度 溫度 溫度 時間 c °C °C °C % °C V S % 1* A 860 1210 890 590 91.4 723 680 14 2氺 A 860 Γ1150 890 590 91.4 723 680 14 _ 3* B 870 1210 890 590 91.4 卜723 760 14 _ 4 A 860 1200 900 600 90.0 723 690 15 15 5* A 860 1230 890 590 91.4 723 740 14 6 A 860 1250 900 590 90.5 723 690 15 10 * :連續退火後進行軋縮率1. 1%之調質軋製。 對於如此處理所得之冷軋鋼板，測定固熔N量以及於燒結 硬化試驗前後實施拉伸試驗。 (i) 固熔N量之分析 根據化學分析，分析冷軋鋼板中的N量，又，根據溴酯之 熔解處理後的萃取分析，以A1N型式求出存在的N量。冷軋 鋼板中的固熔N量為使用 {(冷軋鋼板中之N量）-(以A1N型式存在之1^量）丨之值。 (ii) 拉伸試驗 自此等冷軋鋼板之寬度方向的中央部朝向軋製方向，採取 JIS13號-B拉伸試驗片，並以應變速度交叉頭速度：1(hnm/s 實施拉伸試驗，測定屈服應力YP與全部伸度El。另外，拉 伸試驗為於製品化後i日以内實施。將拉伸試驗片作成jis 13號-B試驗片，係為了極力減低標點外之斷裂之現象。 (ui)燒結硬化性試驗 自此等冷軋鋼板之寬度方向的中央部朝向軋製方向 ，採取 098111149 15 200948985 JIS 13號-B拉伸試驗片，加以2%之拉伸預應變後暫時移除 負重，施行21(TCx2G分鐘之相當於塗敷燒結處理的熱^ 理。於此試驗前後，進行（ii)所示之拉伸試驗。、 其結果示於表3。 [表3] 鋼板No 冷軋鋼板 生燒結處理後Chemical composition (% by mass) Μη )725 )730- 098111149 ).017 ).012 S "ο. 010 Τ 017 Α1 0. 035 0. 009 ΤΓ0Τ48^ 〇. 〇16〇_ 14 200948985 [Table 2] Steel plate Ar3 hot rolling cold rolling Arl continuous annealing secondary cold rolling No No metamorphic point embryo extraction finishing rolling rolling reduction rate point annealing hot rolling rate taking temperature temperature temperature temperature time c °C °C °C % °CVS % 1* A 860 1210 890 590 91.4 723 680 14 2氺A 860 Γ1150 890 590 91.4 723 680 14 _ 3* B 870 1210 890 590 91.4 723 760 14 _ 4 A 860 1200 900 600 90.0 723 690 15 15 5* A 860 1230 890 590 91.4 723 740 14 6 A 860 1250 900 590 90.5 723 690 15 10 * : After continuous annealing, the rolling reduction rate of 1. 1% temper rolling. For the cold-rolled steel sheet thus obtained, the amount of solid-melting N was measured and a tensile test was carried out before and after the sintering hardening test. (i) Analysis of the amount of solid-melting N According to the chemical analysis, the amount of N in the cold-rolled steel sheet was analyzed, and the amount of N present was determined by the A1N type according to the extraction analysis after the melting treatment of the bromo ester. The amount of solid-melting N in the cold-rolled steel sheet is a value obtained by using {(the amount of N in the cold-rolled steel sheet)-(the amount of the A1N type). (ii) Tensile test JIS No. 13-B tensile test piece was taken from the center portion in the width direction of the cold-rolled steel sheet toward the rolling direction, and the head speed was measured at a strain rate: 1 (hnm/s tensile test) The yield stress YP and the total elongation El were measured. In addition, the tensile test was carried out within 1 day after the product was produced. The tensile test piece was made into the jis 13-B test piece in order to minimize the phenomenon of fracture outside the punctuation. (ui) Sintering hardenability test From the central portion of the cold-rolled steel sheet in the width direction toward the rolling direction, a tensile test piece of 098111149 15 200948985 JIS No. 13-B was taken, and a 2% tensile pre-strain was temporarily moved. Except for the load, 21 (TCx2G minutes corresponds to the heat treatment of the coating sintering treatment. Before and after this test, the tensile test shown in (ii) was carried out. The results are shown in Table 3. [Table 3] Steel plate No After cold-rolled steel sheet is sintered
由表 本發明例之No. 1、4、5及6於塗敷· 燒結處理 可充分達 後具有充分的屈服應力YP及全部伸度E1，例如 成3片加工所必要的強度和加工性。 另一方面，比較例之No. 2及3分別為屈服應力γρ和全部 伸度Ε1不足，不具有3片加工所必要的強度和加工性，故 無法施行既定的加工。 如上述若根據本發明，則可取得於塗敷•燒結處理後具有 屈服應力ΥΡ為500MPa以上強度的高強度罐用鋼板。 更且，本發明中，係作成低碳材，且經由（1)含有特定之 N量作為成分， (2)胚萃取溫度設為i2〇〇°c以上，使在胚鑄造時所生成的 A1N分解， 098111149 16 200948985 ⑶將熱軋盤以65(rc以下進行捲取以抑制續的析出’ 使冷軋鋼板之_ N量的絕對量雜於—定以上，更且，經 由塗敷燒域錢之雜魏，切行二切軋、或者進行 低札縮率之二次冷軋，則可提高生產性且可令_鋼板 度化。 D通 (產業上之可利用性） ❷ 岸力大^罐用鋼板為經由成形後的塗敷燒姑處理，令屈服 應力大為上升，且 板的薄化。 a者罐體強度大幅上升，故極有助於鋼Tables No. 1, 4, 5 and 6 of the present invention have sufficient yield stress YP and full elongation E1 after the coating and sintering treatment, for example, the strength and workability necessary for three-piece processing. On the other hand, in No. 2 and 3 of the comparative example, the yield stress γρ and the total elongation Ε1 were insufficient, and the strength and workability necessary for the three-piece processing were not obtained, so that the predetermined processing could not be performed. According to the present invention, it is possible to obtain a steel sheet for high-strength cans having a yield stress ΥΡ of 500 MPa or more after coating/sintering treatment. Furthermore, in the present invention, it is made into a low-carbon material, and (1) contains a specific amount of N as a component, and (2) an embryo extraction temperature is set to i2〇〇°c or more, and A1N generated at the time of embryo casting is obtained. Decomposition, 098111149 16 200948985 (3) The hot-rolled coil is wound up at 65 (c or less to suppress continuous precipitation), so that the absolute amount of the amount of the cold-rolled steel sheet is more than or equal to the above, and further, the coating is burned. The Wei Wei, the cutting and cutting, or the secondary cold rolling with low shrinkage rate can improve the productivity and can make the steel plate more. D-pass (industrial availability) ❷ shore force ^ The steel sheet for cans is subjected to coating and baking treatment after molding, so that the yield stress is greatly increased and the thickness of the sheet is reduced.
098111149 17098111149 17