TW200948984A - Manufacturing method of steel sheet for cans - Google Patents
Manufacturing method of steel sheet for cans Download PDFInfo
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- TW200948984A TW200948984A TW98110593A TW98110593A TW200948984A TW 200948984 A TW200948984 A TW 200948984A TW 98110593 A TW98110593 A TW 98110593A TW 98110593 A TW98110593 A TW 98110593A TW 200948984 A TW200948984 A TW 200948984A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
200948984 六、發明說明: 【發明所屬之技術領域】 本發明係關於一種板厚精度優異之製罐用鋼板之製造方 法,尤其係關於一種適合於將罐高擠壓加工成與罐體直徑相同 程度之用途、或者彎曲成圓筒狀或角筒狀並接合端部彼此而形 成罐體後進行凸緣加工之用途之製罐用鋼板之製造方法。 【先前技術】 ❹ 飲料罐、食品罐、18公升罐、桶罐(pail can)等之罐可根據 其製k方法(步驟)而大致分成兩片罐(tw〇_piece can)與三片罐 (three-piece can)。 兩片罐係指對實施有鍍錫、鍍鉻、金屬氧化物包覆處理、化 學合成處理、無機皮膜包覆處理、有機樹脂皮膜包覆處理、塗 油等之處理的表面處理鋼板,實施淺擠壓加工、DWI(drawand wall iron ’變薄拉伸)加工、DR〇(draw_redraw,深拉伸)加工等 ⑩之加工而使罐底與罐體成形為一體,並對其安裝蓋子之由兩個 零件構成之罐。 二片罐係指將表面處理鋼板彎曲成圓筒狀或角筒狀並接合 端部彼此而形成罐體後,對其安裒頂蓋與底蓋之由三個零件構 成之罐。 該等罐中’素材成本於職本巾所占之比例較I因此,於 降低罐成本時對降低鋼板成本之要求強烈。此處,毋庸置言, 於製造鋼板時,處理步驟越多則成本越高。其中尤其是使鋼板 098110593 3 200948984 於高溫下再結晶之退火步驟,由於因加熱而消耗大量能量成 本’故為提高製造成本之步驟。因此,業界考慮藉由省略該步 驟來試圖降低成本之方法。然而,於冷軋後不進行再結晶之鋼 板因加工硬化而處於強度過高之狀態,故不適於製罐加工。因 此,先前一直在探討藉由適當地控制鋼成分、熱軋條件來獲得 具備適度強度之鋼板的方法。 例如,於專利文獻1中揭示有一種罐用鋼板之製造方法,其 特徵在於,於極低碳鋼中添加作為碳氮化物形成元素之Nb, 於A1·3點以下之所謂α區域進行熱軋,且經冷軋後不進行退 火。然而,由專利文獻1之技術所獲得之鋼板由於一直處於冷 軋之狀態,因此延展性欠佳,在有的用途中並不具備充分之加 工性。 作為改善上述方面之技術,於專利文獻2中揭示有如下技 術.於極低奴鋼中添加作為碳氮化物形成元素之Nb、Ti,於 A1·3點以下進行熱軋,且經冷軋後進行低溫退火,藉此來改善 延展性。此處所謂之低溫退火,係指於不產生再結晶之溫度下 進行之處理,因此用以加熱之能量成本得到降低。 另外,於專利文獻3中揭示有如下技術:於極低碳鋼中添加 屬於碳氣化物形成元素之Nb、Ti、Zr、V、Β,於如點以下 進行熱軋’且經冷軋後,以再結晶溫度以下之溫度進行退火。 專利文獻1 :曰本專利特開平4·280926號公報 專利文獻2:日本專利特開平8_41549號公報 098110593 4 200948984 6-248339號公報 專利文獻3:曰本專利特開平 【發明内容】 4 μ 1至3之背景技術中所共通之特徵,係使用極低碳 鋼:為鋼’更進一步添加碳氮化物形成元素,且於紙點以下 之皿度下知純。朗,於該條件下_造之触存在鋼板 卷材長度方向上之板厚均勻性欠佳之_。糾,於專利文獻200948984 VI. Description of the Invention: [Technical Field] The present invention relates to a method for producing a steel sheet for can making which has excellent plate thickness precision, and more particularly to a method suitable for crushing a can into a diameter equal to that of a can. A method for producing a steel sheet for cans which is used for the purpose of flange processing after being bent into a cylindrical shape or a rectangular tube shape and joining the end portions to form a can body. [Prior Art] 罐 A can, a food can, an 18 liter can, a pail can, etc. can be roughly divided into two cans (tw〇_piece can) and three cans according to the method (step) thereof. (three-piece can). The two-piece can is a surface-treated steel plate which is subjected to treatments such as tin plating, chrome plating, metal oxide coating treatment, chemical synthesis treatment, inorganic film coating treatment, organic resin coating treatment, oil coating, etc. Press processing, DWI (drawand wall iron), DR〇 (draw_redraw) processing, etc., so that the bottom of the can is formed integrally with the can body, and the cover is mounted by two A can of parts. The two-piece can refers to a can composed of three parts of the top cover and the bottom cover after the surface-treated steel plate is bent into a cylindrical shape or a rectangular tube shape and joined to the ends to form a can body. In these tanks, the proportion of material cost to the cost of the towel is higher than that of I. Therefore, the cost of reducing the cost of the steel plate is strong when the cost of the tank is lowered. Here, it goes without saying that the more the number of processing steps in manufacturing the steel sheet, the higher the cost. Among them, in particular, the annealing step of recrystallizing the steel sheet 098110593 3 200948984 at a high temperature is a step of increasing the manufacturing cost because it consumes a large amount of energy due to heating. Therefore, the industry is considering ways to reduce costs by omitting this step. However, since the steel sheet which is not subjected to recrystallization after cold rolling is in an excessively high strength due to work hardening, it is not suitable for can making. Therefore, a method of obtaining a steel sheet having moderate strength by appropriately controlling the steel composition and hot rolling conditions has been previously studied. For example, Patent Document 1 discloses a method for producing a steel sheet for a can, characterized in that Nb which is a carbonitride forming element is added to an extremely low carbon steel, and hot rolling is performed in a so-called α region below A1·3 point. And after annealing, it is not annealed. However, the steel sheet obtained by the technique of Patent Document 1 is in a state of being cold-rolled, so that the ductility is poor, and it is not sufficient in some applications. As a technique for improving the above aspect, Patent Document 2 discloses a technique in which Nb and Ti which are carbonitride forming elements are added to a very low steel, and hot rolling is performed at a point A1·3 or less, and after cold rolling. Low temperature annealing is performed to improve the ductility. The term "low temperature annealing" as used herein refers to a treatment performed at a temperature at which no recrystallization occurs, so that the energy cost for heating is lowered. Further, Patent Document 3 discloses a technique of adding Nb, Ti, Zr, V, and yttrium belonging to a carbon gasification forming element to an extremely low carbon steel, and performing hot rolling at a point below, and after cold rolling, Annealing is performed at a temperature below the recrystallization temperature. [Patent Document 1] Japanese Patent Laid-Open No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. No. Hei. A common feature in the background art of 3 is the use of very low carbon steel: for the steel's further addition of carbonitride forming elements, and pure under the paper point. Lang, under this condition, there is a poor uniformity of the thickness of the steel sheet in the direction of the length of the coil. Correction, in the patent literature
/、專利文獻3 _所進行之冷乳後之退火,根據實施例係於超 過400d皿度下進行,雜與先前之再結晶退幼比係於較 低之溫度下it行’但健為高溫τ之處理,對於充分地降低加 熱所需之能量成本方面並不充分。/, Patent Document 3 _ after the cold milk annealing, according to the embodiment is carried out in the case of more than 400d, the mismatch with the previous recrystallization is lower than the lower temperature, but the heat is high The treatment of τ is not sufficient in terms of sufficiently reducing the energy cost required for heating.
本發明係繁於上述情況研究而成者,目的在於提供一種製罐 用鋼板之製造方法,該製造方法係於藉由省略再結晶退火步驟 而試圖降低鋼板製造成本時,避免因冷軋中之加工硬化所引起 之過剩之局強度化’抑制鋼板卷材之長度方向上之板厚變動, 並且最大限度地發揮因省略再結晶退火步驟所帶來之成本降 低效果。 本發明之主旨如以下所述。 [1]一種製罐用鋼板之製造方法’其特徵在於:藉由連續鑄 造而將鋼製成鋼埋,並於An變態點以下之精加工溫度下進行 熱軋,且經捲繞、酸洗後,以5〇〜96%之軋縮率進行冷軋,上 述鋼係鋼成分以重量%計,包含c : 0.005%以下、Μη : 〇.〇5 〜0.5%、Α1 : 0.01 〜0.12%、Ν : 0.0010〜0.0070%、β : 〇.ΐ5χ 098110593 5 200948984 N〜0·75χΝ(以原子比計’為〇.2〇χΝ〜0.97χΝ) ’且更進一步包 含 Nb : 4xC〜20xC(以原子比計,為 〇.52xC〜2.58xC)、Ti : 2χ C〜10xC(以原子比計,為〇.5〇xC〜2.51xC)中之一種或兩種, 且剩餘部分由Fe及不可避免的雜質元素構成之鋼。 [2] 如上述[1]之製罐用鋼板之製造方法,其中,於64〇〜75〇 °C之溫度下進行上述捲繞。 [3] 如上述[1]或[2]之製罐用鋼板之製造方法,其中,於上述 冷軋後,於150〜400°C之溫度下進行熱處理。 再者,於本發明中,表示鋼之成分之%均為重量%。 根據本發明,藉由省略再結晶退火步驟而可實現鋼板製造成 本之降低。並且,可獲得已抑伽板卷材之長度方向上之板厚 變動之鋼板。 如上所述,省略再結晶退火而可獲得已抑制鋼板卷材之長度 方向上之板厚變動之鋼板,藉此可製造成本較絲更低之鋼 板,亦可有助於降低罐體本身之成本。 【實施方式】 以下’對本發明進行詳細說明。 鋼於 =明者㈣_鶴_物航素之極低碳 ;r3點町之溫度下進行絲,且更進 以 鋼板卷材長度方向上之板厚變動進行探討, 下’對本發明進行詳細說明。 成本發月 首先,對鋼成分之限定理由分別加以說明。 098110593 200948984 c ·· 0.005%以下 本發明係藉由省略再結晶退火步驟而試圖降低成本之製罐 用鋼板之製造方法。但是,於冷軋後不進行再結晶之鋼板因加 工硬化而處於強度過高之狀態,而且延展性亦欠佳,因此不適 於製罐加工。因此,必需預先使用低強度之鋼作為鋼本身。因 此,必需使用已減少高固溶強化能之碳之極低碳鋼作為鋼成 分。若C超過0.005%,則鋼於冷軋後會變為強度過高且延展 Ο 性亦欠佳之狀態,從而不適於製罐加工。因此,c之含量設為 0.005%以下’較佳為_3%以下。再者,就預先使用低強度 之鋼作為鋼本身而言,c之含量越低越好,但為了降低c之含 量而進行去碳操作需要時間,從而會導致製造成本之上升。因 此’ C含量之下限較佳為請05%以上,更佳為議15%以上。 Μη : 0.05〜0.5% 若Μη含量未滿0·05%,則即便降低s含量亦難以避免所謂 ❹賴脆性_ sh喃ess),從而有時會產生表面破裂等之問題。 另方面^超過〇·5〇/0,則變態點過於降低,於進行變態點 以下之熱軋_峨得理想之喊。0此,隱含量設為⑽抓 以上且0.50%以下。再者,於特別注重加工性之情況時,較佳 為設為0.20%以下。 S : 0.008%以下(較佳條件) S並不會對本發明之峨躲造成_之㈣。然而,若S 含量超過_%,則於添加含量超過〇.難%之N時,會使 098110593 7 200948984 大量產生之MnS成為析出核而使作為氮化物及碳氮化物之 BN、Nb(C、N)、A1N析出,使熱延性(h〇t duc碰y)下降。因 此,理想的是S含量設為〇 〇〇8%以下。 A1 : 0.01 〜0.12% 若A1含量未滿〇.01%’則無法充分地獲得去氧效果。另外, 亦無法充分地獲得藉由形成N與施來減少鋼中之固溶N之 效果ϋ® ’若超過G12%,則不僅該等效果達到飽和, 而且易於產生氧化銘等中間物㈣订咖⑴㈣。因此,量設為 0.01%以上且0.12%以下。 N : 0.0010〜〇·〇〇7〇% 若使N未滿G.G_%,則鋼板之製造成本上升,亦難以實現 穩定的製造。另外’於本發财,如後文所述b與N之比非 常重要’若N含量少’則難以進行用以將B與N之比保持於 固定範圍内之B含量之控制。另一方面,若n超過〇 〇麵, 則鋼之熱紐魏。其在於,若N含量切咖〇%,則 因BN、Nb(N、〇、施等氮化物及碳氮化物析出而會引起脆 化,尤其係於連續鑄造時產生_破裂之危險性會增加。若產 生触破裂,騎於触破狀部分,f要進行角部之切割或 利用研磨叙健之步驟,由於要㈣大量勞力與成本, 因此會極大地阻礙生產率。因此,N含量設為〇 _%以上且 0.0070%以下。較佳為〇 〇〇44%以下。 B ·· 0.15χΝ〜〇,75xn 098110593 200948984 ❹ ❹ B係本發明中對鋼板之特性具有重大影響力之重要元素。 本發月係藉由省略再結晶退火步驟而試圖降低成本之製罐 用鋼板之製造方法,因此⑴使用極低碳鋼作為鋼⑺添加碳 氮化物形成元素,(3)於Ar3點以下之溫度下進行執札。缺而, 於該條件下製造之鋼板存在鋼板卷材長度方向上之板厚均句 性欠佳之問題。因此,本發明對該現象進行了詳細研究,結果 獲得以下見解:藉由在鋼中適量添純,可良好地保持鋼板卷 材長度方向上之板厚均勾性。該見解可認為絲於以下之機制 者。首先,鋼板卷材長度方向上之板厚之不均句性係於熱札鋼 板之階段產生。可認為其原因在於,由於添加有碳氮化物形成 凡素之極低仙於Μ點自沃斯顿(咖_魏成為鐵氧 體(We)時變形阻力會間斷地發生變化,因此當熱札支架間 產生變態時,會產生熱軋支架間張力、熱軋負重之變動,結果 導致板厚之變動。可認為藉由添加B,可抑制此種變形阻力之 間斷的變化,從而使板厚均勻性得到改善。即,本發明中之重 點在於適當地規定B之添加量來抑㈣形阻力之間斷的變 化。研究之結果得知,B之添加量必需以與形成bn之N之添 加量保持適當之關係來添加,為了獲得該效果,必需添加以重 量比計0遍以上之B。另―方面,若以重量%計添加· N以上之B ’則不僅上述之效果達到飽和,而且會導致成本之 上升。因此,B之添加量設為〇·ΐ5χΝ〜〇75χΝ(以原子 為 0_20χΝ〜0.97χΝ)。 098110593 9 200948984The present invention has been developed in view of the above circumstances, and an object of the present invention is to provide a method for producing a steel sheet for can making, which is to avoid the cold rolling in the case of attempting to reduce the manufacturing cost of the steel sheet by omitting the recrystallization annealing step. The excessive strength due to work hardening reduces the variation in the thickness of the steel sheet coil in the longitudinal direction, and maximizes the cost reduction effect caused by omitting the recrystallization annealing step. The gist of the present invention is as follows. [1] A method for producing a steel sheet for can making, characterized in that: steel is buried in steel by continuous casting, and hot rolling is performed at a finishing temperature below An transformation point, and is wound and pickled. Thereafter, cold rolling is performed at a rolling reduction ratio of 5 〇 to 96%, and the steel-based steel component contains, by weight %, c: 0.005% or less, Μη: 〇.〇5 to 0.5%, Α1: 0.01 to 0.12%, Ν : 0.0010~0.0070%, β : 〇.ΐ5χ 098110593 5 200948984 N~0·75χΝ (in atomic ratio '〇.2〇χΝ~0.97χΝ)' and further contains Nb: 4xC~20xC (in atomic ratio) One or two of 〇.52xC~2.58xC), Ti: 2χ C~10xC (in atomic ratio, 〇.5〇xC~2.51xC), and the remainder consists of Fe and unavoidable impurities. The steel of the elements. [2] The method for producing a steel sheet for can making according to the above [1], wherein the winding is carried out at a temperature of from 64 Torr to 75 °C. [3] The method for producing a steel sheet for can making according to the above [1] or [2] wherein, after the cold rolling, heat treatment is performed at a temperature of 150 to 400 °C. Further, in the present invention, the % of the components representing steel is % by weight. According to the present invention, the reduction in the manufacturing cost of the steel sheet can be achieved by omitting the recrystallization annealing step. Further, a steel sheet having a variation in the thickness of the squash coil in the longitudinal direction can be obtained. As described above, the recrystallization annealing is omitted, and a steel sheet having a variation in the thickness of the steel sheet coil in the longitudinal direction can be obtained, whereby a steel sheet having a lower cost can be produced, and the cost of the tank itself can be reduced. . [Embodiment] Hereinafter, the present invention will be described in detail. Steel in the = Ming (4) _ crane _ the end of the extremely low carbon; r3 point of the temperature of the wire, and further into the thickness of the steel coil in the direction of the thickness of the discussion, the next 'detailed' . The cost of the month First, the reasons for limiting the steel components are explained separately. 098110593 200948984 c ·· 0.005% or less The present invention is a method for producing a steel sheet for can making which is intended to reduce the cost by omitting the recrystallization annealing step. However, since the steel sheet which is not subjected to recrystallization after cold rolling is in an excessively high strength due to work hardening, and the ductility is also poor, it is not suitable for can making. Therefore, it is necessary to use low-strength steel as the steel itself in advance. Therefore, it is necessary to use extremely low carbon steel which has reduced carbon of high solid solution strengthening energy as a steel component. If C exceeds 0.005%, the steel will become too high in strength and inferior in ductility after cold rolling, and thus it is not suitable for can making. Therefore, the content of c is made 0.005% or less', preferably _3% or less. Further, in the case where the low-strength steel is used in advance as the steel itself, the lower the content of c, the better, but it takes time to perform the decarburization operation in order to lower the content of c, which leads to an increase in manufacturing cost. Therefore, the lower limit of the 'C content is preferably 05% or more, and more preferably 15% or more. Μ η : 0.05 to 0.5% If the content of Μη is less than 0·05%, it is difficult to avoid the so-called brittleness _ sh ess if the s content is lowered, and problems such as surface cracking may occur. On the other hand, if it exceeds 〇·5〇/0, the metamorphic point is too low, and the hot rolling below the metamorphic point is yelling. 0, the hidden content is set to (10) above and below 0.50%. Further, in the case where the workability is particularly emphasized, it is preferably 0.20% or less. S: 0.008% or less (better conditions) S does not hide the ambiguity of the present invention (4). However, when the S content exceeds _%, when the added content exceeds 〇.%, the MnS which is produced in a large amount in 098110593 7 200948984 becomes a precipitation nucleus, and BN and Nb (C, which are nitrides and carbonitrides). N) and A1N are precipitated, and the hot ductility (h〇t duc touch y) is lowered. Therefore, it is desirable that the S content is set to 〇 8% or less. A1 : 0.01 to 0.12% If the A1 content is less than 〇.01%', the deoxidation effect cannot be sufficiently obtained. In addition, it is not possible to sufficiently obtain the effect of reducing the solid solution N in the steel by forming N and applying ϋ® 'if it exceeds G12%, not only the effects are saturated, but also the intermediates such as oxidized imitation are easily generated. (1) (4). Therefore, the amount is set to 0.01% or more and 0.12% or less. N: 0.0010~〇·〇〇7〇% If N is less than G.G_%, the manufacturing cost of the steel sheet increases, and it is difficult to achieve stable production. Further, in the case of the present invention, the ratio of b to N is very important as described later. If the N content is small, it is difficult to control the B content for maintaining the ratio of B to N within a fixed range. On the other hand, if n exceeds the 〇 〇 surface, then the heat of steel is New Wei. When the N content is 5%, the BN and Nb (N, niobium, and other nitrides and carbonitrides are precipitated to cause embrittlement, especially in continuous casting, the risk of rupture increases. If there is a rupture of the contact, riding on the broken part, the step of cutting the corner or using the step of grinding and nurturing, because of the large amount of labor and cost, will greatly hinder the productivity. Therefore, the N content is set to 〇 _% or more and 0.0070% or less, preferably 〇〇〇44% or less. B ·· 0.15χΝ~〇, 75xn 098110593 200948984 ❹ ❹ B is an important element of the present invention which has a significant influence on the characteristics of the steel sheet. The method of manufacturing a steel sheet for cans which attempts to reduce the cost by omitting the recrystallization annealing step, and therefore (1) adding carbonitride forming elements using steel as the steel (7), and (3) performing the temperature below the Ar3 point. However, the steel plate manufactured under the conditions has a problem that the plate thickness in the longitudinal direction of the steel sheet coil is not uniform. Therefore, the present invention has studied the phenomenon in detail, and as a result, the following findings are obtained: in The medium amount of pure addition can well maintain the thickness of the steel sheet coil in the longitudinal direction. This opinion can be considered as the following mechanism. First, the uneven thickness of the sheet thickness in the longitudinal direction of the steel sheet coil It is produced at the stage of the hot-sand steel plate. It can be considered that the reason is that the deformation resistance is interrupted due to the addition of carbonitride to form a very low-quality singularity from Walston (Wa_Wei became ferrite (We)). The ground changes, so when there is a metamorphosis between the hot-screw brackets, the tension between the hot-rolled brackets and the load of the hot-rolling load will change, resulting in a variation in the thickness of the sheet. It can be considered that by adding B, the deformation resistance can be suppressed. The change of the thickness of the sheet is improved, that is, the focus of the present invention is to appropriately specify the amount of addition of B to suppress the change of the resistance of the (four) shape. As a result of the study, it is known that the amount of addition of B must be In order to obtain this effect, it is necessary to add B in a weight ratio of 0 or more. In addition, if B is added in % by weight or more, then Effect Saturated, but also the cost is increased. Therefore, the amount of B-ΐ5χΝ~〇75χΝ set square (in atom 0_20χΝ~0.97χΝ). 098110593 9 200948984
Nb : 4xC〜20xC(以原子比計’為 〇 52xC〜2 58xC)、Ti : 2χ C〜10xC(以原子比計,為〇.5〇xC〜2.51xC)中之一種或兩種Nb 係碳氮化物形成元素,具有將鋼中之C、N作為析出物而進行 固定以使鋼之強度下降之效果。為了充分地發揮該效果,必需 達到以重量比計4xC以上之添加量。另一方面,若Nb之添加 量過多,則不僅使固溶C減少之作用達到飽和,而且由於Nb 饧格昂貴,故生產成本亦上升。因此,必需將灿之添加量抑 制至20xC以下。因此’ Nb之添加量設為以重量比計械〜2〇 xC(以原子比s十’為〇.52xC〜2.58xC)之範圍。 Τι係碳氮化物形成兀素’具有將鋼中之C、N作為析出物而 進行固定以使鋼之強度下降之效果。為了充分地發揮該效果, 必需達到以重量比計為2xC以上之添加量。另一方面,若ή 之添加量過多’則不僅使固溶c減少之作用達到飽和,而且由 ;Tl價格昂貝’故生產成本亦上升。因此,必需將Ti之添加 量抑制至脈以下。因此,Ti之添加量設為以重量比計% 1〇xC(以原子比計,為〇 5()xC〜2 51xC)之範圍。 再者,上述以外之剩餘部分由Fe及不可避免的雜質構成。 作為不可聽雜質,可於残害本發明之侧效果之範圍内 例如含有以下之元素。Nb: 4xC~20xC (in terms of atomic ratio '〇52xC~2 58xC), Ti: 2χ C~10xC (atomic ratio, 〇.5〇xC~2.51xC) or one of two Nb-based carbons The nitride-forming element has an effect of fixing C and N in the steel as precipitates to lower the strength of the steel. In order to fully exert this effect, it is necessary to achieve an addition amount of 4xC or more by weight. On the other hand, if the amount of Nb added is too large, not only the effect of reducing the solid solution C is saturated, but also the production cost is increased because the Nb is expensive. Therefore, it is necessary to suppress the addition amount of the scent to 20xC or less. Therefore, the amount of addition of Nb is set to a range of ~2 〇 x C (in atomic ratio s tens of 〇. 52 x C to 2.58 x C) by weight ratio. The Τι-based carbonitrides form halogens' have the effect of fixing C and N in the steel as precipitates to lower the strength of the steel. In order to fully exert this effect, it is necessary to achieve an addition amount of 2xC or more in terms of a weight ratio. On the other hand, if the amount of ruthenium added is too large, not only the effect of reducing the solid solution c is saturated, but also the production cost is increased by the price of Tl. Therefore, it is necessary to suppress the addition amount of Ti to below the pulse. Therefore, the addition amount of Ti is set to a range of % 1 〇 x C (in terms of atomic ratio, 〇 5 () x C 〜 2 51 x C) by weight. Further, the remainder other than the above is composed of Fe and unavoidable impurities. As the inaudible impurity, for example, the following elements may be contained within the range of the side effects of the present invention.
Si ·· 0.020%以下 若Si含量超過0.020%,則鋼板之表面性狀會劣化不僅作 …表面處理鋼板不理想,而且鋼會發生硬化而難以進行熱乳步 〇9811〇593 200948984 驟。因此,Si含量較佳為〇 〇2〇%以下。 P : 0.020%以下 因此就兼顧兩者而 藉由P含量之減少,可獲得加雜之轉與耐錄之改善效 果,但過度減少則會引起製造成本之增加, 言’ p含量較佳為0.020%以下。Si ·· 0.020% or less When the Si content exceeds 0.020%, the surface properties of the steel sheet are deteriorated. Not only is the surface-treated steel sheet unsatisfactory, but the steel is hardened and it is difficult to carry out the hot milk step 〇 9811〇593 200948984. Therefore, the Si content is preferably 〇 〇 2 〇 or less. P: 0.020% or less. Therefore, by reducing the P content, the effect of improving the mixing and the recording resistance can be obtained, but excessive reduction causes an increase in the manufacturing cost, and the 'p content is preferably 0.020. %the following.
…除上述成分以外,亦可含有Cr、cu等不可避免的雜質,但 该等成分並科對本發日月之鋼婦性造鱗別之影響,因此可 於不影響其他特性之範圍内適宜含有。另外,於不會對鋼板之 特性造成π料之範_,亦可添加上述以外之元素。 其次,就製造條件之限定理由加以說明。 本發明之製罐用鋼板可藉由如下方法而獲得··利用連續缚造 將調整成上述化學成分範圍之鋼製成鋼链,於知變態點以下 之精加工溫度下進行減,錄捲繞、酸洗後以5G〜96%之軋 縮率進行料。難為於64G〜75()t之馳溫度下進行上述 捲繞。更佳為於上述冷軋後,於15G〜崔。^之溫度下進行熱 處理。以下,對該等進行詳細說明。 熱軋條件 熱軋之精力口工溫度:Ah變態點以下 熱軋之精加工溫度於本發明中係重要之要件。藉由在Ah變 態點以下之精加工溫度下對本發明中所規定之成分之鋼進行 熱軋’可獲得能夠承受製罐加I之纖材質。可認為其原因在 ί藉由進行Α1·3變態點以下之熱軋,熱軋鋼板之粒徑會變得 098110593 11 200948984 足夠粗大,冷軋中之加工硬化得到抑制而使得冷軋後之強度不 會過剩。 再者,A1·3變態點可作為實施有熱軋時之加工及再現熱歷程 之加工熱處理試驗時的伴隨著A1·3變態之體積變化所產生之溫 度而求得。本發明中所規定之鋼成分之Αι>3變態點大概為9〇〇 °C附近,精加工溫度只要低於該溫度即可,但為了可靠地達成 此點,理想的是設為860°C以下。 此外,雖然詳細之機制並不明確,但藉由使Ar3變態點以下 ❹ 之總軋縮率為40%以上’且使最終軋縮率為25%以上,可使組 織之均勻性優異,材質穩定性得到提高。為了進一步提高上述 效果,較佳為使總軋縮率為50%以上,且使最終軋縮率為3〇0/〇 以上。 再者,藉由使精軋機入口侧溫度為95CTC以下,能夠可靠地 於Ah變態點以下進行熱軋,並且可實現組織之均勻化,故於 本發明中更佳。關於詳細之機制無法充分闡明,但可推測其與 ❾ 即將開始精軋之前之沃斯田體粒徑有關。就防止產生鏽皮 (scale)瑕疵之觀點而言,更理想的是使精軋機入口侧溫度為 920°C以下。 捲繞溫度:640〜750°C (適宜條件) 捲繞溫度必需以不給下一步驟即酸洗與冷軋帶來障礙之方 式進行設定。即,當於超過750°C之溫度下進行捲繞時,不僅 鋼板之鏽皮厚度顯著增大,酸洗時之去鏽皮性惡化,有時亦會 098110593 12 200948984 =TL板本身之高溫強度之下降而產生卷材之變形等 == 未滿6贼,則捲繞後之保熱效果並不充 为,熱軋鋼板之粒徑難以充分地粗大化。 规鋼板實施 酸洗後之冷軋條件:軋縮率為50〜96% 酸洗後之冷軋係使乾縮率為5〇〜96%。若乾縮率未滿篇, 則結晶組織變得不㈣,因此進行製罐加工時變形會不均句, 產品之表面變得_。另外’該冷軋亦發揮調整鋼板之形狀斑 城度之作用,因此進行大概術χ上之⑽於該等方面械 為必需之條件。另外,上限取決於被視為必需之產品之強度與 厚度、熱軋或冷軋之設備能力,但超過96%進行冷乾將難以避 免局部延展性之劣化,因此除極其特殊之崎以外無法應用。 冷乳後之熱處理溫度:15〇〜4〇〇°C(適宜條件)... In addition to the above-mentioned components, it may contain unavoidable impurities such as Cr and cu. However, these components are affected by the gender of the sun and the moon. Therefore, it can be contained within a range that does not affect other characteristics. . Further, elements other than the above may be added without causing a π-material _ for the characteristics of the steel sheet. Next, the reasons for limiting the manufacturing conditions will be explained. The steel sheet for can making of the present invention can be obtained by the following method: • Steel which is adjusted to the above chemical composition range by continuous assembly, and is reduced in the finishing temperature below the known deformation point, and is recorded and wound. After pickling, the material was subjected to a rolling reduction of 5 G to 96%. It is difficult to perform the above winding at a temperature of 64 G to 75 () t. More preferably after the above cold rolling, at 15G ~ Cui. Heat treatment at a temperature of ^. Hereinafter, the details will be described. Hot rolling conditions Energy-cutting temperature of hot rolling: Below the Ah point of hot rolling The finishing temperature of hot rolling is an important requirement in the present invention. By subjecting the steel of the component specified in the present invention to hot rolling at a finishing temperature below the Ah transformation point, a fiber material capable of withstanding the can and I can be obtained. It can be considered that the reason is that by hot rolling below the Α1·3 metamorphic point, the particle size of the hot-rolled steel sheet becomes 098110593 11 200948984, which is sufficiently coarse, the work hardening in cold rolling is suppressed, and the strength after cold rolling is not There will be excess. Further, the A1·3 metamorphic point can be obtained as a temperature which is caused by a volume change of the A1·3 metamorphosis in the processing heat treatment test in the hot rolling process and the heat history test. The steel component specified in the present invention has a metamorphosis point of about 9 〇〇 ° C, and the finishing temperature is lower than the temperature, but in order to achieve this reliably, it is desirable to set it to 860 ° C. the following. In addition, although the detailed mechanism is not clear, the uniformity of the structure is excellent and the material is stabilized by making the total rolling reduction ratio of the Ar3 transformation point below 40% or more and the final reduction ratio is 25% or more. Sexuality is improved. In order to further improve the above effects, it is preferred to have a total reduction ratio of 50% or more and a final reduction ratio of 3 〇 0 / 〇 or more. Further, by setting the inlet side temperature of the finishing mill to 95 CTC or less, hot rolling can be reliably performed below the Ah transformation point, and uniformity of the structure can be achieved, which is more preferable in the present invention. The detailed mechanism cannot be fully clarified, but it is presumed that it is related to the particle size of the Worth field before the start of finish rolling. From the viewpoint of preventing the occurrence of scale, it is more preferable to set the temperature at the inlet side of the finishing mill to 920 ° C or lower. Winding temperature: 640 to 750 ° C (suitable conditions) The winding temperature must be set in such a way as not to cause an obstacle to the next step, pickling and cold rolling. That is, when winding at a temperature exceeding 750 ° C, not only the thickness of the steel sheet is significantly increased, but also the descaling property during pickling is deteriorated, and sometimes 098110593 12 200948984 = high temperature strength of the TL plate itself The deformation of the coil is caused by the decrease, etc. == If the thief is less than 6 thieves, the heat retention effect after winding is not sufficient, and the particle size of the hot-rolled steel sheet is difficult to be sufficiently coarsened. The steel plate is subjected to cold rolling conditions after pickling: the rolling reduction ratio is 50 to 96%, and the cold rolling after pickling is such that the dry shrinkage ratio is 5 〇 to 96%. If the shrinkage rate is not full, the crystal structure becomes not (4), so the deformation will be uneven when the can making process, and the surface of the product becomes _. In addition, the cold rolling also plays a role in adjusting the shape of the steel sheet. Therefore, it is necessary to perform the above-mentioned (10) on these aspects. In addition, the upper limit depends on the strength and thickness of the product deemed to be necessary, and the equipment capacity of hot rolling or cold rolling. However, if it is more than 96%, it is difficult to avoid the deterioration of local ductility, so it cannot be applied except for extremely special. Heat treatment temperature after cold milk: 15 〇 ~ 4 〇〇 ° C (suitable conditions)
。當於冷軋後進行熱處理時,熱處理之溫度設為15〇〜棚 c。本發明之成分之再結晶温度大概為73(rc以上,因此於⑼ 400 C下不會引起再結晶,但根據本發明中所規定之C、Nb、 N、B之含量關係’藉由在上述溫度範圍内進行熱處理可實現 強度之下降與延展性之改善。該現象可認為仙於味低之溫 度下產生軟化,故於該溫度下易於進行擴散之(:、?^等固溶元 素與藉由冷軋而導入之差排相互作用所引起。即,可認為藉由 本發明中所規定之C、Nb、Ti、N、B之含量關係而使得鐵氧 098110593 13 200948984 體相下之固溶(:、;^達到理想的狀態,藉此可於較低溫度下獲 付強度之下降與延展性之改善。尤其可認為,於本發明中所規 定之B之添加條件之影響重大’藉由b與n形成bn而使得 固办N降低、固溶B向粒界偏析以妨礙c、N向粒界之偏析、 於基質中藉由熱處理而自C、N黏著有藉由冷軋而導入之差排 之狀態變成黏著被解除,能夠獲得強度之下降與延展性之改 善。能夠期待此種改善效果之下限之溫度為15〇艺。另一方面, 若溫度達到40(TC以上,則冷軋中之應變能(strainenergy)蓄積 車乂大之。卩分的結晶粒優先開始進行恢復,從而導致於進行製 罐力口工時變形不均勻,產品之表面變得粗才造。因此,使冷札後 之熱處理溫度為15〇〜4G(rc。再者,為了穩定地獲得強度、 延展性,該熱處理溫度較佳為200〜350°C之範圍。再者,關 於熱處理時間,只要為足以供固溶元素自本發明中所推斷之元 素脫離差排之時間即可,並無制限定,但較佳為大概1〇〜 90 s之範圍。 [實施例] [實施例1] 以下,說明實施例。 將表1所示之各種鋼加以熔鑄而製成鋼坯,於11〇〇〜125〇 ◦C之加熱溫度下騎加減,於表丨所故精加工溫度下進行 熱軋’然後於之捲繞溫度下進行捲繞。_,於酸洗後, 以90%之軋縮率進行冷軋。 098110593 14 200948984 對藉由以上方法而獲得之鋼板之板厚變動進行評價。板厚變 動係利用設置於冷札設備中之X射線板厚計,針對鋼板卷材 長度之全長而測定冷軋後之板厚,以相對於平均板厚之變動率 來進行評價,將變動率為作為產品可容許之±3%以下者視為合 格而以〇來表示,將變動率超過±3%者視為不合格而以χ來表 示〇 另外,於表1中,將熱軋之精加工溫度為本發明中所規定之 ❹Αι·3㈣點以下者視為〇,將於本發明巾除外之超過Μ變態 者視為X將猎由以上方法而獲得之結果與條件一併示於表. When heat treatment is performed after cold rolling, the heat treatment temperature is set to 15 〇 to shed c. The recrystallization temperature of the component of the present invention is about 73 (rc or more, and therefore does not cause recrystallization at (9) 400 C, but according to the content relationship of C, Nb, N, and B as defined in the present invention' The heat treatment in the temperature range can achieve a decrease in strength and an improvement in ductility. This phenomenon can be considered to soften at a temperature at a low taste, so that it is easy to diffuse at this temperature (:, ?^, etc. It is caused by the poor row interaction introduced by cold rolling. That is, it can be considered that the solid solution of the ferrite 098110593 13 200948984 is obtained by the content relationship of C, Nb, Ti, N, B as defined in the present invention ( :,; ^ to achieve the desired state, whereby the decrease in strength and the improvement in ductility can be obtained at a lower temperature. In particular, it can be considered that the influence of the addition condition of B specified in the present invention is significant. Forming bn with n causes the fixed N to decrease, the solid solution B to segregate to the grain boundary to prevent the segregation of c and N to the grain boundary, and the difference between the C and N adhesions introduced by cold rolling in the matrix by heat treatment. The state of the row becomes sticky and is released, and can be obtained The decrease in strength and the improvement in ductility. The temperature at which the lower limit of the improvement effect can be expected is 15 。. On the other hand, if the temperature reaches 40 (TC or more, the strain energy in the cold rolling is large. The crystal grains of the bismuth are preferentially restored, resulting in uneven deformation during the potting process, and the surface of the product becomes coarse. Therefore, the heat treatment temperature after the cold is 15 〇 to 4 G ( Further, in order to stably obtain strength and ductility, the heat treatment temperature is preferably in the range of 200 to 350 ° C. Further, as long as the heat treatment time is sufficient, the element is sufficient for the solid solution element to be inferred from the present invention. The time for leaving the difference row is not limited, but is preferably in the range of about 1 〇 to 90 s. [Examples] [Example 1] Hereinafter, examples will be described. Various steels shown in Table 1 are cast and cast. The billet is made into a billet, which is heated and rolled at a heating temperature of 11 〇〇 to 125 〇◦C, and hot rolled at the finishing temperature of the watch, and then wound at a winding temperature. _, pickling After that, cold rolling is performed at a rolling reduction rate of 90%. 098110593 14 200948984 The thickness variation of the steel sheet obtained by the above method was evaluated. The thickness variation was measured by the X-ray thickness gauge provided in the cold-rolling equipment, and the length of the steel coil was measured. The plate thickness is evaluated as a rate of change with respect to the average plate thickness, and the rate of change is considered to be acceptable as ±3% or less of the product, and is expressed as 合格, and the rate of change exceeding ±3% is regarded as not In addition, in Table 1, the finishing temperature of hot rolling is regarded as 〇 · · · 3 3 3 3 四 四 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 〇 For X, the results obtained by the above method are shown together with the conditions.
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ISI 161 03 - SSI1860 200948984 · • 自表1可知’於本發明例中,板厚變動為±3%以下,已獲得 ‘抑制了鋼板卷材之長度方向上之板厚變動之鋼板。即,可知作 為本發明之第1課題之板厚㈣之抑制如表丨所示般,已藉由 滿足第1發明中所規定之條件而得到解決。 [實施例2] 將表2所示之各種鋼加以賴而製成鋼达,於膽〜⑽ °C之加熱溫度下進行加熱後,於Μ變態點以下即8腕之精 β加玉溫度下進行熱軋,然後於表2所示之捲繞溫度下進行捲 繞。繼而,進行酸洗,並以表2所示之⑽率進行冷乳。 對藉由以上方法啸得之鋼板之板厚變動進行評價。板厚變 動係利用設置於冷軋設備中之χ射線板厚計,針對鋼板卷材 ’ 長度之全長而測定冷軋後之板厚,以相對於平均板厚之變動率 ’來進行評價。將評價結果示於表2。將變動率為作為產品可容 4之±3 Α以下者視為合格*以〇來表示,將變動率超過士者 © 視為不合格而以χ來表示。 繼而,於表2所示之熱處理溫度下對上述鋼板進行3〇 s之 熱處理。其後’進行兩種表面處理。-種係於表面鐘Cr而形 成無錫鋼板(以下稱為TFS(Tin Free Steel)),且更進一步層壓聚 對本一曱酸乙二酯(PET,polyethylene terephthalate)樹脂薄膜。 另一種係於表面鍍Sn而形成鍍錫鋼板。 將於TFS上層壓PET樹脂薄膜者加工成擠壓比為2·2之 DRD罐’並以目視判定對罐體部及罐底部之粗糙度進行評 098110593 17 200948984 價。許價以與優、良、欠佳之界限樣本之對 優係未出現粗財,㈣出現略餘触為進仃」此處, 者,欠佳—财訂衫容 《各許範圍 nn心“,、〜許之粗_度者。評價結果係將 表2 …將良4 △’將欠佳記為χ。將所獲得之結果示於 另外,將形成為鍍錫鋼板者製成直徑為52 mm之焊接罐, 進行擴張率為6%及8%之凸緣加工,並對凸緣破裂之產生進行 評價。評價結果係將於6 %及8 %之凸緣加工中未產生破裂者記 為〇,將即便於8%之凸緣加工中產生破裂但於6%之凸緣加工 中未產生破裂者記為△,將於6%及8%之凸緣加工中均產生破 裂者記為X。將所獲得之結果示於表2。 098110593 18ISI 161 03 - SSI 1860 200948984 • From Table 1, it can be seen that in the example of the present invention, the variation in the thickness of the sheet is ±3% or less, and the steel sheet in which the thickness variation in the longitudinal direction of the steel sheet coil is suppressed has been obtained. In other words, it is understood that the suppression of the thickness (4) of the first object of the present invention is solved by satisfying the conditions specified in the first invention as shown in the table. [Example 2] The various steels shown in Table 2 were made into steel, and heated at a heating temperature of biliary to (10) ° C, and then at a temperature below the Μ metamorphic point, that is, under the temperature of 8 wrists. Hot rolling was performed, and then winding was performed at the winding temperature shown in Table 2. Then, pickling was carried out, and cold milk was carried out at a rate of (10) shown in Table 2. The plate thickness variation of the steel sheet which was whipped by the above method was evaluated. The thickness of the steel sheet was measured by the thickness of the steel sheet coil by the thickness of the steel sheet coil, and the thickness of the sheet was measured with respect to the average sheet thickness. The evaluation results are shown in Table 2. The rate of change is considered to be qualified as *3 Α or less of the product. * It is expressed as 〇, and the rate of change exceeds the evaluator. Then, the steel sheets were heat-treated at 3 s in the heat treatment temperature shown in Table 2. Thereafter, two surface treatments were carried out. A type of tin-free steel sheet (hereinafter referred to as TFS (Tin Free Steel)) is formed on the surface clock Cr, and a polyethylene terephthalate (PET) resin film is further laminated. The other is to form a tin-plated steel sheet by plating Sn on the surface. The PET resin film laminated on the TFS was processed into a DRD can having an extrusion ratio of 2.2 and the roughness of the can body and the bottom of the can was evaluated by visual inspection at 098110593 17 200948984. There is no such thing as a good balance between the price and the excellent, good, and poor boundaries. (4) There is a slight change in the experience. Here, the poor, the wealth of the dress, the "range of nn heart" , , ~ 〜 粗 粗 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 The welding can of mm is subjected to flange processing with an expansion ratio of 6% and 8%, and the occurrence of flange cracking is evaluated. The evaluation result is that no crack is generated in the flange processing of 6% and 8%. 〇, even if cracking occurs in the 8% flange processing, if no crack occurs in the 6% flange processing, it is recorded as △, and cracks will be generated in the 6% and 8% flange processing. The results obtained are shown in Table 2. 098110593 18
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0.0029 ,0.0049 ! 0.0029 1 0.0023 1 10.0029 10.0030] i 0.0032 10.0024 | 10.0023 ] [0.0025 | 10.0031 | |0.0015| 10.0029 | ΓΟ <s o d [0.0032 | 10.0025 | 10.0049 1 10.00301 10.0032 1 |0.0029| 10.0029 1 10.00291 10.0029 1 10·0029| 0.0029! 10.0029 1 ^Η CN m 寸 ΙΟ 卜 00 o m 1—H 寸 in οο Os 61 C6SH860 200948984 表可去I發明之第1課題即板厚變動之抑制已藉由滿 足第1發明中所規定之條件而得到解決。另外,於實際之罐之 成型中’粗Μ、凸緣破裂相可容許之水準。 而且付知’藉由更進—步滿足第2發明及第3發明中所規定 之條件’將於實際之罐之成财,更進—步良好地抑制粗糖、 (產業上之可利用性)k^l—-I (%#¥) Μ =α 〇〇〇〇XX 〇< X 〇XXX 〇X 〇〇〇<] 〇X 〇〇<1 〇〇XI 〇〇〇XX 〇〇〇 〇〇〇〇〇〇〇〇〇X 〇X 〇<1 <<< X 〇ΤΡι n 岭〇Η - ΐι X ΐι 〇〇〇XXX 〇〇X 〇XXX 〇X 〇〇X 〇XX 〇 〇〇〇XXW According to P ο s Ο 沄Ο ΙΤΪ ο ο ο Art ο 丨 丨»^1 沄CS ooo CN o in cs o 沄o O 宕o 00 cn 宕丨 inch i 宕丨τ··^1 ο 00 ο 〇〇ο 沄ο 00 ο οι 沄1 ο ο ο ο 00 00 00 00 VO oo JO g V〇oo 00 〇\ CN ON g 00 00 § Ό 00 ν〇00 Ό 00 00 00 00 00 00 00 癍〇υ S S S g g g g g g g g g o o o o o o o o o o o o o o o o o o v v v v v v v v v v v v v v v v s s s s s s s s s s s s s s s s s s s s s s s s s s s s s _α dH ηΐβη ffi CS tn ο Ο 5 ο d 00 ν〇ο 〇\ 00 ο ν〇ο CS tN 〇o *Ti o cs On O o ... oo 00 Ό o C4 (N 〇CsJ o Ο ο CS <Ν Ο 幻 幻ο ο 幻ο d ιη CN ο g ο Ο II I 1 1 1 1 1 1 1 1 1 o 〇 W \ WJ 卜 2| 卜 1 00 ο I ^η| ο τ-Η 1 *"Η 00 \〇iri 00 Buboo 00 00 1 1 1 1 1 ^οι 卜卜00 οο 1 00 m\ I 00 CQ |0.0013| 10.0013| 10.0011 1 10.00141 10.00131 10.00081 1 0.0008 1 10.00151 10.0008 | 10.0004 1 10.00231 | 0.0011 I 10.0013] 10.0013 1 10.00131 |0.0015| |0.0018| 1 0.0011 1 10.00081 |0.0015| 10.0005 1 |0·(8) 10| 10.0010 1 10.0010 1 1 o.ooio 1 10.00101 10.0003 1 P 1 1 1 1 I 1 1 1 1 1 1 1 SO o rs fs oo CN O o cs iS oo cn CN 〇 d CN ο ο CN < Ν Ο Ο ο ο ο ο I (SS ο 〇 S S S S S CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CN CS S Ο Ο S ο CN CN 〇〇 inch s 〇cn <N 〇d 〇s o' in CN 〇o 1 1 1 1 1 〇\ ο ο ο S ο CS CN Ο ο CS CN Ο ο CN S Ο I CM S Ο Ο Ο 1 <Ν Ο Ο 0.0025 10.0023 1 i 0.0025 1 10.00191 10.0019 1 10.00091 10.00121 10.0068 1 10.0075 1 10.0026 | 10.0025 | |0.0023| 10.0025 | 10.0023 | |0.0019| |0.0068| 10.0025 | 10.0025] |0.0012 | 10.0068 1 0. 00 00 00 00 00 00 00 00 00 00 00 00 00 o Ό 〇 〇 Os dooooso ΓΊ 〇d Ό s 〇 VJ ο 5 ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο Η *—< ο ο ο ο Ο do T—^ od CN doooo T ooo Ο τ—4 Ο »-Η Ο ο Τ' < ο Ο ο Ο »-Η ο Ο ο CL, Ό Ο Ο Ο g ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο ο S ο ο ο S S S S 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 00 CN o 00 CM d 沄dmmo Ο CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS CS ο ο ο ο ο ο 1-H dodo c> iH o T-H oooo ο ο ο ο ο Ο Ο Η Ο ο Ο a 0.0015 ! 0.0029 ,0.0049 ! 0.0029 1 0.0023 1 10.0029 10.0030] i 0.0032 10.0024 | 10.0023 ] [0.0025 | 10.0031 | |0.0015| 10.0029 | ΓΟ <sod [0.0032 | 10.0025 | 10.0049 1 10.00301 10.0032 1 |0.0029| 10.0029 1 10.00291 10.0029 1 10·0029| 0.0029! 10.0029 1 ^Η CN m inch 卜 00 om 1—H inch in οο Os 61 C6SH860 200948984 Table can go to the first subject of I invention, that is, the suppression of thickness variation has been satisfied by 1 The conditions specified in the invention are solved. In addition, the thickness of the rough, flange fracture phase can be tolerated in the actual can forming. In addition, it is possible to satisfy the conditions stipulated in the second invention and the third invention by the progress of the actual invention, and it is possible to further suppress the raw sugar and improve the industrial availability.
本發明最合適作為食品罐或飲料罐^而且,除該等以外,^ =用:將如本發明中所假定之有機樹脂薄膜層壓鋼板作為 損傷二2前之DVD—,拉伸)成形,避免_ 、昜並要求罐體之抽取性之用途。The present invention is most suitably used as a food can or a beverage can. Moreover, in addition to the above, the organic resin film laminated steel sheet as assumed in the present invention is formed as a DVD-, stretched, before the damage. Avoid _, 昜 and require the extraction of the tank.
098110593 20098110593 20
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JP2008089924A JP5262242B2 (en) | 2008-03-31 | 2008-03-31 | Manufacturing method of steel plate for can manufacturing |
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JP (1) | JP5262242B2 (en) |
KR (1) | KR101235415B1 (en) |
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MY171370A (en) | 2014-05-30 | 2019-10-10 | Jfe Steel Corp | Steel sheet for cans and manufacturing method thereof |
WO2016157760A1 (en) * | 2015-03-27 | 2016-10-06 | Jfeスチール株式会社 | Steel sheet for can and method for producing same |
CN107429348B (en) * | 2015-03-27 | 2019-05-10 | 杰富意钢铁株式会社 | Steel plate for tanks and its manufacturing method |
KR102353731B1 (en) * | 2019-12-20 | 2022-01-19 | 주식회사 포스코 | Formable blackplate and manufacturing method the same |
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JP3023385B2 (en) | 1991-03-11 | 2000-03-21 | 川崎製鉄株式会社 | Manufacturing method of steel sheet for cans |
JPH06248339A (en) * | 1993-02-26 | 1994-09-06 | Nippon Steel Corp | Production of steel sheet for vessel with high rigidity |
JP3596037B2 (en) * | 1994-08-01 | 2004-12-02 | Jfeスチール株式会社 | Manufacturing method of steel plate for can-making |
JP3422852B2 (en) * | 1994-09-14 | 2003-06-30 | 新日本製鐵株式会社 | Manufacturing method of steel sheet for cans |
JPH08127816A (en) * | 1994-10-28 | 1996-05-21 | Nippon Steel Corp | Production of starting steel sheet for vessel, excellent in wrinkling resistance |
JPH08176673A (en) * | 1994-12-21 | 1996-07-09 | Kawasaki Steel Corp | Production of steel sheet for can |
JPH08246060A (en) * | 1995-03-10 | 1996-09-24 | Kawasaki Steel Corp | Production of steel sheet for can |
JPH08269568A (en) * | 1995-03-30 | 1996-10-15 | Kawasaki Steel Corp | Production of steel sheet for can making excellent in flange formability |
JPH1150211A (en) * | 1997-08-05 | 1999-02-23 | Kawasaki Steel Corp | Thick cold rolled steel plate excellent in deep drawing workability and its production |
EP1741800A1 (en) * | 2004-04-27 | 2007-01-10 | JFE Steel Corporation | Steel sheet for can and method for production thereof |
WO2006100796A1 (en) * | 2005-03-24 | 2006-09-28 | Jfe Steel Corporation | Flexible sheet steel for can and process for producing the same |
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2008
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- 2009-03-27 EP EP09726961.7A patent/EP2275581A4/en not_active Withdrawn
- 2009-03-27 CN CN2009801121551A patent/CN101983246B/en not_active Expired - Fee Related
- 2009-03-31 TW TW98110593A patent/TWI440725B/en not_active IP Right Cessation
Also Published As
Publication number | Publication date |
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EP2275581A4 (en) | 2015-09-02 |
EP2275581A1 (en) | 2011-01-19 |
KR20100122941A (en) | 2010-11-23 |
KR101235415B1 (en) | 2013-02-20 |
TWI440725B (en) | 2014-06-11 |
CN101983246A (en) | 2011-03-02 |
JP5262242B2 (en) | 2013-08-14 |
CN101983246B (en) | 2013-11-27 |
JP2009242857A (en) | 2009-10-22 |
WO2009123294A1 (en) | 2009-10-08 |
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