TWI390053B - Method for manufacturing steel sheet for high strength container - Google Patents
Method for manufacturing steel sheet for high strength container Download PDFInfo
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- TWI390053B TWI390053B TW098111997A TW98111997A TWI390053B TW I390053 B TWI390053 B TW I390053B TW 098111997 A TW098111997 A TW 098111997A TW 98111997 A TW98111997 A TW 98111997A TW I390053 B TWI390053 B TW I390053B
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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
- C21D8/0236—Cold 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
- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0268—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment between cold rolling steps
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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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0273—Final recrystallisation annealing
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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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- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/004—Dispersions; Precipitations
Description
本發明係關於適於在熔接等三片加工或DI等二片加工後，施行徑形狀縮小或擴大加工的容器用素材之高強度容器用鋼板及其製造方法。The present invention relates to a steel sheet for a high-strength container suitable for a material for a container which is subjected to reduction in diameter or enlargement after three-piece processing such as welding or DI processing, and a method for producing the same.
近年，作為降低成本之目的，並削減資材使用或減輕環境負荷之目的，正朝為將素材的鋼材(鋼板)之製品板厚削薄之製品開發演進。In recent years, in order to reduce the cost, and to reduce the use of materials or to reduce the environmental load, we are evolving to develop products with thinner and thinner products of steel (steel sheet).
再者，若將製品板厚變薄，因為剛性會降低，因而為彌補此剛性降低，亦必需謀求鋼材高強度化。但是，因為謀求鋼材高強度化時會施行硬質化，因而在凸緣加工或頸縮加工中有發生破裂的問題。Further, if the thickness 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, since it is hardened when the steel material is made high in strength, there is a problem that cracking occurs in the flange processing or the necking processing.
針對上述，目前考慮有各種製造方法。In view of the above, various manufacturing methods are currently considered.
例如在專利文獻1中提案有：將鋼中成分管理於一定範圍內，且在(Ar3 變態點-30℃)以上結束熱軋，然後，經施行酸洗、冷軋後，再施行連續退火而進行2次冷軋的方法。For example, Patent Document 1 proposes to manage the steel components in a certain range and to finish hot rolling at (Ar 3 metamorphic point -30 ° C) or higher, and then perform continuous annealing after pickling and cold rolling. The method of performing cold rolling twice.
然而，專利文獻1的方法中，為使凸緣加工性、頸縮加工性及耐蝕性不致劣化，便將P設在0.02wt%以下，更將2次冷軋的軋延率設為15~30%，因而頗難有效率地對較薄製品施行有效率處理，導致生產不易，且有容易發生外觀不良的問題。此外，亦有在鋼坯表層發生破裂，導致成為製品良率降低肇因的問題。且，較難安定地進行製造，必需予以改善。However, in the method of Patent Document 1, in order to prevent the flange workability, neck workability, and corrosion resistance from deteriorating, P is set to 0.02 wt% or less, and the rolling ratio of the secondary cold rolling is set to 15~ 30%, so it is difficult to efficiently process thinner products, resulting in production difficulties, and problems that are prone to poor appearance. In addition, there is also a problem that the surface of the steel slab is cracked, which causes a decrease in the yield of the product. Moreover, it is difficult to carry out manufacturing with stability and must be improved.
再者，硬質容器用鋼板的代表性製造方法係提案有下述方法，配合退火種類適當選擇使用(例如非專利文獻1)。In the representative production method of the steel sheet for a hard container, the following method is proposed, and it is appropriately selected and used in accordance with the type of annealing (for example, Non-Patent Document 1).
熱軋→酸洗→冷軋→箱型退火(BAF)→第2次冷軋(軋延率：20~50%)Hot rolling→acid washing→cold rolling→box annealing (BAF)→second cold rolling (rolling rate: 20~50%)
熱軋→酸洗→冷軋→連續退火(CAL)→第2次冷軋(軋延率：20~50%)Hot rolling→acid washing→cold rolling→continuous annealing (CAL)→second cold rolling (rolling rate: 20~50%)
然而，上述方法中因為在提升軋延時的潤滑性目的下，使用高黏度的各種軋延油，因而有因軋延油的濃度不均或部分性油附著等情形，導致軋延後外觀不良的問題發生。此外，當軋延軋延率較高時，因為利用軋延將鋼板施行拉伸，因而鋼板寬度方向與軋延方向的耐力差會變大。However, in the above method, since various rolling properties of high viscosity are used for the purpose of improving the lubricity of the rolling delay, the unevenness of the rolling oil or the adhesion of the partial oil may result in poor appearance after rolling. The problem has occurred. Further, when the rolling rolling ratio is high, since the steel sheet is stretched by rolling, the difference in the endurance between the width direction of the steel sheet and the rolling direction becomes large.
對此，考慮有降低第2次冷軋時的軋延率之方法。但是，降低軋延率時，較難獲得必要的耐力。In view of this, a method of reducing the rolling rate at the time of the second cold rolling is considered. However, when the rolling rate is lowered, it is difficult to obtain the necessary endurance.
專利文獻1：日本專利第3108615號公報Patent Document 1: Japanese Patent No. 3108615
非專利文獻1：「我國罐用表面處理鋼板的技術史」日本鋼鐵協會平成10年10月30日出版p.188Non-Patent Document 1: "Technical History of Surface Treated Steel Sheets for Cans in China" published by the Japan Iron and Steel Association on October 30, 2010. p.188
依此，當欲獲得製品板厚較薄的容器用鋼板時，現況下尚無能滿足強度、加工性以及生產性的製造方法，期盼出現能滿足的製造方法。Accordingly, when a steel sheet for a container having a thin plate thickness is obtained, there is no manufacturing method capable of satisfying strength, workability, and productivity in the present case, and a satisfactory manufacturing method is expected.
本發明係有鑑於該等實情而完成，目的在於提供具有拉伸強度TS達500MPa以上的強度，且板寬方向與軋延方向的耐力差在20MPa以下，加工性優異的容器用鋼板及其製造方法。The present invention has been made in view of the above-mentioned circumstances, and it is an object of the present invention to provide a steel sheet for a container having a tensile strength TS of 500 MPa or more and a difference in endurance between the sheet width direction and the rolling direction of 20 MPa or less and excellent workability. method.
本發明者等為解決上述問題而進行深入鑽研。結果獲得以下的發現。The inventors of the present invention have conducted intensive studies to solve the above problems. As a result, the following findings were obtained.
發現藉由調整作為成分組成的P含有量，且施行軋延率20~50%的第2次冷軋而進行高強度化，更於連續退火時施行過時效處理，而均勻析出碳化物，並將該碳化物利用為加工時使應力分散的空隙，便可減少外觀不適合，且可縮小寬度方向與軋延方向的耐力差，能確保高強度材質。而且，更發現藉由規範上述碳化物的粒徑、密度、比例，亦可獲得加工性更優異的容器用鋼板。It has been found that by adjusting the P content as a component composition and performing the second cold rolling at a rolling ratio of 20 to 50%, the strength is increased, and the aging treatment is performed even during continuous annealing to uniformly precipitate carbides. By using this carbide as a void which disperses stress during processing, it is possible to reduce the appearance unsuitable, and it is possible to reduce the difference in endurance between the width direction and the rolling direction, and to secure a high-strength material. Further, it has been found that a steel sheet for a container which is more excellent in workability can be obtained by standardizing the particle diameter, density, and ratio of the above-mentioned carbide.
依如上述，本發明係根據上述發現，藉由對成分進行管理，遂完成高強度罐用鋼板。As described above, according to the above findings, the present invention accomplishes the high-strength steel sheet for cans by managing the components.
本發明係根據以上發現而完成，主旨係如下：[1]一種高強度容器用鋼板，係依質量%計，含有：C：0.01~0.05%、Si：0.04%以下、Mn：0.1~1.2%、S：0.10%以下、Al：0.001~0.100%、N：0.10%以下、P：0.0020~0.100%，其餘由Fe及不可避免的雜質構成，拉伸強度TS達500MPa以上，板寬方向與軋延方向的耐力差在20MPa以下。The present invention has been completed based on the above findings, and the subject matter thereof is as follows: [1] A steel sheet for a high-strength container containing, by mass%, C: 0.01 to 0.05%, Si: 0.04% or less, and Mn: 0.1 to 1.2%. , S: 0.10% or less, Al: 0.001 to 0.100%, N: 0.10% or less, P: 0.0020 to 0.100%, and the balance is composed of Fe and unavoidable impurities, and the tensile strength TS is 500 MPa or more, and the sheet width direction and rolling are performed. The difference in endurance in the extension direction is below 20 MPa.
[2]一種高強度容器用鋼板，係依質量%計，含有：C：0.01~0.05%、Si：0.04%以下、Mn：0.1~1.2%、S：0.10%以下、Al：0.001~0.100%、N：0.10%以下、P：0.0020~0.020%，其餘由Fe及不可避免的雜質構成，拉伸強度TS達500MPa以上，板寬方向與軋延方向的耐力差在20MPa以下。[2] A steel sheet for a high-strength container containing C: 0.01 to 0.05%, Si: 0.04% or less, Mn: 0.1 to 1.2%, S: 0.10% or less, and Al: 0.001 to 0.100%, by mass%. N: 0.10% or less, P: 0.0020 to 0.020%, and the balance is composed of Fe and unavoidable impurities, and the tensile strength TS is 500 MPa or more, and the difference in the resistance between the sheet width direction and the rolling direction is 20 MPa or less.
[3]一種高強度容器用鋼板之製造方法，係將依質量%計含有：C：0.01~0.05%、Si：0.04%以下、Mn：0.1~1.2%、S：0.10%以下、Al：0.001~0.100%、N：0.10%以下、P：0.0020~0.100%，其餘由Fe及不可避免的雜質構成的鋼，依精軋溫度：(Ar3 變態點溫度-30)℃以上、捲取溫度：400~750℃施行熱軋，經施行酸洗、冷軋後，再施行含過時效處理的連續退火，接著，依軋延率：20~50%施行第2次的冷軋。[3] A method for producing a steel sheet for a high-strength container, which comprises, by mass%, C: 0.01 to 0.05%, Si: 0.04% or less, Mn: 0.1 to 1.2%, S: 0.10% or less, and Al: 0.001. ~0.100%, N: 0.10% or less, P: 0.0020~0.100%, and the remaining steel consisting of Fe and unavoidable impurities, depending on the finishing temperature: (Ar 3 metamorphic point temperature -30) °C or more, coiling temperature: After hot rolling at 400~750 °C, after acid pickling and cold rolling, continuous annealing with overaging treatment is carried out, and then the second cold rolling is carried out according to the rolling rate: 20-50%.
[4]一種高強度容器用鋼板之製造方法，係將依質量%計含有：C：0.01~0.05%、Si：0.04%以下、Mn：0.1~1.2%、S：0.10%以下、Al：0.001~0.100%、N：0.10%以下、P：0.0020~0.020%，其餘由Fe及不可避免的雜質構成的鋼，依精軋溫度：(Ar3 變態點溫度-30)℃以上、捲取溫度：400~750℃施行熱軋，經施行酸洗、冷軋後，再施行含過時效處理的連續退火，接著，依軋延率：20~50%施行第2次的冷軋。[4] A method for producing a steel sheet for a high-strength container, which comprises, by mass%, C: 0.01 to 0.05%, Si: 0.04% or less, Mn: 0.1 to 1.2%, S: 0.10% or less, and Al: 0.001. ~0.100%, N: 0.10% or less, P: 0.0020~0.020%, and the remaining steel consisting of Fe and unavoidable impurities, depending on the finishing temperature: (Ar 3 metamorphic point temperature -30) °C or more, coiling temperature: After hot rolling at 400~750 °C, after acid pickling and cold rolling, continuous annealing with overaging treatment is carried out, and then the second cold rolling is carried out according to the rolling rate: 20-50%.
另外，本說明書中，表示鋼成分的「%」均指「質量%」。此外，本發明中，「高強度容器用鋼板」係指拉伸強度TS(以下簡稱「TS」)達500MPa以上的容器用鋼板。In addition, in this specification, "%" of a steel component means "mass %." In the present invention, the "steel plate for high-strength containers" refers to a steel sheet for containers having a tensile strength TS (hereinafter referred to as "TS") of 500 MPa or more.
再者，本發明的高強度容器用鋼板係以容器用素材、罐用素材為對象。不管有無施行表面處理，將施行鍍錫、鍍鎳錫、鍍鉻(所謂無錫鍍敷)、或有機被覆等，可適用於極廣範圍的用途。In addition, the steel sheet for high-strength containers of the present invention is intended for the material for containers and the material for cans. With or without surface treatment, tin plating, nickel-plated tin, chrome plating (so-called tin-free plating), or organic coating can be applied to a wide range of applications.
此外，相關板厚並無特別的限制，惟從獲得本發明最大極限活用效果的觀點而言，較佳板厚0.30mm以下、更佳0.20mm以下。特佳0.170mm以下。Further, the relevant thickness is not particularly limited, but from the viewpoint of obtaining the maximum limit utilization effect of the present invention, the thickness is preferably 0.30 mm or less, more preferably 0.20 mm or less. Very good 0.170mm or less.
以下，針對本發明進行詳細說明。Hereinafter, the present invention will be described in detail.
本發明的容器用鋼板係TS達500MPa以上，板寬方向與軋延方向的耐力差在20MPa以下的高強度容器用鋼板。而，本發明係藉由調整P含有量，且將第2次的冷軋(以下稱「2次冷軋」)的軋延率設為20~50%，便可提供高強度的容器用鋼板。The steel sheet for containers of the present invention has a steel sheet of a high strength container having a resistance of 500 MPa or more and a difference in sheet width direction and a rolling direction of 20 MPa or less. In the present invention, by adjusting the P content and setting the rolling ratio of the second cold rolling (hereinafter referred to as "secondary cold rolling") to 20 to 50%, it is possible to provide a high-strength steel sheet for containers. .
以下針對本發明容器用鋼板的成分組成進行說明。The component composition of the steel sheet for containers of the present invention will be described below.
C：0.01~0.05%C: 0.01~0.05%
若C成分偏多，則2次冷軋後的鋼板便被硬質化達必要以上，導致製罐性與頸縮加工性劣化。且其成為因熔接部的明顯硬質化，在凸緣加工時會導致發生HAZ破裂的元素。若C超過0.05%，因為該等的影響趨於明顯，因而將C設定在0.05%以下。另一方面，若C成分極端偏低，則為了維持容器的強度便必需施行高軋延率的二次冷軋，因而C設定在0.01%以上。較佳0.02%以上0.04%以下、更佳0.02%以上0.03%以下。When the amount of the C component is too large, the steel sheet after the second cold rolling is hardened more than necessary, and the potability and the necking workability are deteriorated. Further, it becomes an element which causes the HAZ to be broken at the time of flange processing due to the apparent hardening of the welded portion. If C exceeds 0.05%, since the influence of these tends to be conspicuous, C is set to 0.05% or less. On the other hand, if the C component is extremely low, it is necessary to perform secondary cold rolling at a high rolling ratio in order to maintain the strength of the container, so C is set to 0.01% or more. It is preferably 0.02% or more and 0.04% or less, more preferably 0.02% or more and 0.03% or less.
Si：0.04%以下Si: 0.04% or less
若大量添加Si，則會發生表面性狀劣化、耐蝕性劣化等。所以，Si係設為0.04%以下。When Si is added in a large amount, surface properties are deteriorated, corrosion resistance is deteriorated, and the like. Therefore, the Si system is set to 0.04% or less.
Mn：0.1~1.2%Mn: 0.1~1.2%
Mn係防止因S所造成之熱軋破裂情形的有效元素。藉由配合S量進行添加，便可獲得防止破裂的效果。此外，亦具有將結晶粒細微化的作用。為了發揮該等效果，Mn必需至少添加達0.1%以上。反之，若大量添加，則有耐蝕性劣化的傾向，且鋼板被硬質化達必要以上，凸緣加工性、頸縮加工性均劣化，因而上限係設為1.2%。較佳設定在0.35%以下。Mn is an effective element for preventing hot rolling cracking caused by S. By adding the amount of S, the effect of preventing cracking can be obtained. In addition, it also has the effect of refining crystal grains. In order to exert such effects, Mn must be added at least 0.1% or more. On the other hand, when it is added in a large amount, the corrosion resistance tends to be deteriorated, and the steel sheet is hardened more than necessary, and both the flange workability and the necking workability are deteriorated, so the upper limit is 1.2%. It is preferably set to be 0.35% or less.
P：0.0020~0.100%P: 0.0020~0.100%
P係使鋼硬質化的成分，本發明中配合所要求強度而含有既定量。若未滿0.0020%，便無法獲得500MPa以上的TS，因而設為0.0020%以上。反之，若P成分含有必要以上的過剩量，會使耐蝕性劣化。且凸緣加工性與頸縮加工性均劣化。該等情形係在超過0.100%趨於明顯，因此上限設為0.100%。若設為0.0020~0.020%，則藉由利用P添加所造成的適度強度與後述二次冷軋的效果，便可獲得更高強度，因而較佳。The P-based component which hardens the steel is contained in the present invention in an amount equal to the required strength. If it is less than 0.0020%, TS of 500 MPa or more cannot be obtained, so it is set to 0.0020% or more. On the other hand, if the P component contains an excess amount more than necessary, the corrosion resistance is deteriorated. Both the flange workability and the necking workability are deteriorated. These cases tend to be more than 0.100%, so the upper limit is set to 0.100%. When it is set to 0.0020 to 0.020%, it is preferable to obtain higher strength by the moderate strength caused by the addition of P and the effect of the secondary cold rolling described later.
S：0.10%以下S: 0.10% or less
S係在鋼中依夾雜物形式存在，屬於減少鋼板延性且使耐蝕性劣化的元素。所以，設定在0.10%以下。較佳0.030%以下。The S system exists in the form of inclusions in steel, and is an element which reduces the ductility of the steel sheet and deteriorates the corrosion resistance. Therefore, it is set to 0.10% or less. Preferably it is 0.030% or less.
Al：0.001~0.100%Al: 0.001~0.100%
Al係鋼的脫氧所必要元素。若含量未滿0.001%，則脫氧嫌不足，會因夾雜物而導致凸緣加工性劣化與頸縮加工性劣化。所以，設定在0.001%以上。另一方面，Al雖會與N成分鍵結而使固溶N減少，但若固溶N過度減少，便無法獲得必要強度。所以，設定在0.100%以下。較佳0.035~0.075%。An essential element for deoxidation of Al-based steel. When the content is less than 0.001%, the deoxidation is insufficient, and the flange workability deterioration and necking workability are deteriorated due to inclusions. Therefore, it is set at 0.001% or more. On the other hand, although Al is bonded to the N component to reduce the solid solution N, if the solid solution N is excessively decreased, the necessary strength cannot be obtained. Therefore, it is set to 0.100% or less. Preferably it is 0.035~0.075%.
N：0.10%以下N: 0.10% or less
N係屬於在不導致熔接部硬度上升情況下，能有效提高強度的元素。但是，若含有量過多，鋼板明顯硬質化，軋延素材(鋼坯)發生破裂缺陷的危險性明顯增加，反而導致凸緣加工性與頸縮加工性劣化。所以，N設定為0.10%以下。較佳0.05%以下。此外，從防止鋼坯破裂的觀點而言，更佳係設定為未滿0.01%。特佳0.005%以下。依此，藉由減少N，便可減輕鋼坯破裂，不需要鋼坯處理，可提升良率。The N system is an element which can effectively increase the strength without causing an increase in the hardness of the welded portion. However, if the content is too large, the steel sheet is remarkably hardened, and the risk of occurrence of cracking defects in the rolled material (steel billet) is remarkably increased, and the flange workability and the necking workability are deteriorated. Therefore, N is set to be 0.10% or less. It is preferably 0.05% or less. Further, from the viewpoint of preventing the slab from being broken, it is more preferable to set it to less than 0.01%. Excellent 0.005% or less. Accordingly, by reducing N, the slab rupture can be reduced, and the slab treatment is not required, and the yield can be improved.
其餘係Fe及不可避免雜質。The rest are Fe and inevitable impurities.
除上述成分以外的其餘係Fe及不可避免的雜質。另外，不可避免的雜質係可容許例如Sn：0.01%以下。Other than the above components are Fe and unavoidable impurities. Further, an unavoidable impurity can be, for example, Sn: 0.01% or less.
本發明容器用鋼板係具有上述組成，且具有達500MPa以上的TS，板寬方向與軋延方向的耐力差在20MPa以下。藉由具有500MPa以上的TS，即使將板厚削薄，仍不會降低剛性。再者，因為將板寬方向與軋延方向的耐力差設定在20MPa以下，在凸緣加工與頸縮加工時便不會發生破裂情形。The steel sheet for containers of the present invention has the above-described composition and has TS of 500 MPa or more, and the difference in endurance between the sheet width direction and the rolling direction is 20 MPa or less. By having a TS of 500 MPa or more, even if the thickness is reduced, the rigidity is not lowered. Further, since the difference in the endurance between the sheet width direction and the rolling direction is set to 20 MPa or less, cracking does not occur at the time of flange processing and necking processing.
接著，針對本發明高強度容器用鋼板之製造方法進行說明。Next, a method of producing a steel sheet for a high-strength container according to the present invention will be described.
將上述組成的熔鋼利用使用了轉爐等通常公知的熔製方法施行熔製，接著，利用連續鑄造法等通常公知的鑄造方法形成軋延素材(鋼坯)。接著，使用該等軋延素材，利用熱軋形成熱軋板。The molten steel having the above composition is melted by a generally known melting method such as a converter, and then a rolled material (slab) is formed by a generally known casting method such as a continuous casting method. Next, using these rolled materials, hot rolled sheets are formed by hot rolling.
鋼坯萃取溫度：1050~1300℃(較佳條件)Billet extraction temperature: 1050~1300°C (better conditions)
若將鋼坯萃取溫度設為1050℃以上，在下一步驟的熱軋中則可確保充分高的熱軋結束溫度。另一方面，若將萃取溫度設定在1300℃以下，最終的鋼板表面性狀不會劣化。所以，鋼坯萃取溫度較佳係1050℃以上、1300℃以下。When the slab extraction temperature is set to 1050 ° C or higher, a sufficiently high hot rolling end temperature can be secured in the hot rolling in the next step. On the other hand, if the extraction temperature is set to 1300 ° C or lower, the surface properties of the final steel sheet are not deteriorated. Therefore, the billet extraction temperature is preferably 1050 ° C or more and 1300 ° C or less.
精軋溫度(熱軋結束溫度)：(Ar3 變態點溫度-30)℃以上Finishing temperature (hot rolling end temperature): (Ar 3 metamorphic point temperature -30) °C or more
熱軋結束溫度係為使後續步驟的冷軋性、以及製品特性較良好，必需設為(Ar3 變態點-30)℃以上。若未滿(Ar3 變態點-30)℃，則最終製品的金屬組織粗粒化，在製罐時容易發生表皮粗糙。此外，若熱軋結束溫度呈低溫，則發生脊現象，導致在成形加工後容易發生外觀不良情況。所以，熱軋結束溫度係設定為(Ar3 變態點-30)℃以上。The hot rolling end temperature is such that the cold rolling property and the product characteristics in the subsequent step are relatively good, and it is necessary to set it as (Ar 3 transformation point -30) ° C or more. If it is less than (Ar 3 metamorphic point -30) °C, the metal structure of the final product is coarsened, and the skin roughness is likely to occur during canning. Further, if the hot rolling end temperature is low, a ridge phenomenon occurs, which may cause appearance defects after the forming process. Therefore, the hot rolling end temperature is set to (Ar 3 metamorphic point -30) ° C or more.
捲取溫度：400~750℃Coiling temperature: 400~750°C
若捲取溫度過低，則熱軋板形狀劣化，在下一步驟的酸洗、冷軋操作時造成障礙，因而設為400℃以上。反之，若過高，則在熱軋母板的階段會析出氮化鋁，而無法確保強化所需要的充分固溶N。況且，熱軋母板會形成碳化物凝聚的組織，而無法獲得依後述過時效所造成的碳化物均勻析出效果，且亦對鋼板耐蝕性造成不良影響。更會因鋼板表面所產生的銹皮厚度增加，導致酸洗性劣化。為迴避該等不良情況，必需設定在750℃以下。When the coiling temperature is too low, the shape of the hot-rolled sheet is deteriorated, which causes an obstacle in the pickling and cold-rolling operation in the next step, and is therefore 400 ° C or higher. On the other hand, if it is too high, aluminum nitride is precipitated at the stage of hot rolling of the mother board, and sufficient solid solution N required for strengthening cannot be ensured. In addition, the hot-rolled mother sheet forms a structure in which carbides are agglomerated, and it is impossible to obtain a uniform precipitation effect of carbides due to overaging as described later, and also adversely affects the corrosion resistance of the steel sheets. Further, the thickness of the scale generated on the surface of the steel sheet is increased to deteriorate the pickling property. In order to avoid such adverse conditions, it is necessary to set it below 750 °C.
對依此所製得之熱軋板施行酸洗、冷軋而形成冷軋板。酸洗係只要依照常法利用鹽酸、硫酸等酸將表面銹皮除去便可。The hot rolled sheet thus obtained is subjected to pickling and cold rolling to form a cold rolled sheet. In the pickling system, the surface scale may be removed by an acid such as hydrochloric acid or sulfuric acid according to a usual method.
(酸洗後的)冷軋之軋延率：80%以上(較佳條件)Rolling rate of cold rolling (after pickling): 80% or more (better conditions)
若軋延率未滿80%，在退火後有無法獲得組織充分細粒化的情況，因而較佳為80%以上。另外，如本發明素材的鋼板，為能達成組織的充分細微化，軋延率更佳係85%以上。另一方面，相關軋延率的上限並無特別的限制，可考慮熱軋、冷軋的設備裝置能力等之後再適當設定。If the rolling rate is less than 80%, the structure may be sufficiently finely granulated after annealing, and thus it is preferably 80% or more. Further, in the steel sheet of the material of the present invention, in order to achieve sufficient miniaturization of the structure, the rolling ratio is more preferably 85% or more. On the other hand, the upper limit of the relevant rolling ratio is not particularly limited, and may be appropriately set after considering the equipment capacity of hot rolling or cold rolling.
退火溫度：800℃以下的再結晶溫度(較佳條件)Annealing temperature: recrystallization temperature below 800 ° C (better conditions)
若鋼板中有殘存未再結晶組織，則製罐時會導致成形性不良、外觀不良等情形，因而必需利用連續退火施行再結晶處理。但是，若過度提高退火溫度，則連續退火時會發生熱挫曲(heat buckle)、板斷裂等缺陷。而且，因異常的結晶粒成長，導致外觀特性劣化的危險性亦會提高。所以，退火溫度較佳係在800℃以下的再結晶溫度區域中實施。If there is a residual non-recrystallized structure in the steel sheet, it may cause poor formability and poor appearance when the can is formed. Therefore, it is necessary to perform recrystallization treatment by continuous annealing. However, if the annealing temperature is excessively increased, defects such as heat buckle and plate fracture occur during continuous annealing. Further, the risk of deterioration of appearance characteristics due to abnormal crystal grain growth also increases. Therefore, the annealing temperature is preferably carried out in a recrystallization temperature region of 800 ° C or lower.
再者，若在溫度範圍內，便不需要特別保持於一定的溫度。從操作的安定性觀點而言，若設為5s以上60s以下的均熱相當時間便足夠。若設為5s以上的均熱時間，在加工時成為使應力分散空隙的碳化物析出充分，屬較佳。Furthermore, if it is in the temperature range, it is not necessary to maintain a certain temperature. From the viewpoint of the stability of the operation, it is sufficient to set the soaking temperature of 5 s or more and 60 s or less for a considerable period of time. When it is set to a soaking time of 5 sec or more, it is preferable to precipitate a carbide which is a stress dispersion void during processing.
過時效處理Overaging
為使利用上述退火所析出碳化物能更均勻分散，而有效地發揮應力分散空隙的效果，必需施行過時效處理。過時效處理較佳係在上述退火後，依10℃/s以上的冷卻速度冷卻至300~500℃溫度區域，並在300~500℃溫度區域中保持5s以上。藉由10℃/s以上的冷卻速度冷卻至300~500℃溫度區域，容易析出碳化物，若在300~500℃溫度區域中保持5s以上，便可確保均勻碳化物析出。此外，藉由施行此種過時效處理，即使依20~50%軋延率施行以下所示之第2次的冷軋，仍可使板寬方向與軋延方向的耐力差在20MPa以下。藉由依此種條件施行過時效處理，便可使粒徑1.5μm以下及粒徑超過1.5μm、3.0μm以下的碳化物密度與比例在後述較佳範圍。In order to more effectively disperse the carbides precipitated by the above annealing, and effectively exert the effect of stress-dispersing voids, it is necessary to perform an overaging treatment. The overaging treatment is preferably cooled to a temperature range of 300 to 500 ° C at a cooling rate of 10 ° C/s or more after the annealing, and maintained at a temperature of 300 to 500 ° C for 5 sec or more. By cooling to a temperature range of 300 to 500 ° C at a cooling rate of 10 ° C / sec or higher, carbides are easily precipitated, and if it is kept at a temperature of 300 to 500 ° C for 5 sec or more, uniform carbide precipitation can be ensured. Further, by performing such an overaging treatment, even if the second cold rolling shown below is performed at a rolling ratio of 20 to 50%, the difference in the resistance between the sheet width direction and the rolling direction can be made 20 MPa or less. By performing the aging treatment under such conditions, the carbide density and ratio of the particle diameter of 1.5 μm or less and the particle diameter of more than 1.5 μm and 3.0 μm or less can be preferably in the preferred range described later.
第2次冷軋的軋延率：20~50%(較佳20~30%)Rolling rate of the second cold rolling: 20~50% (preferably 20~30%)
連續退火後的第2次冷軋(以下稱「2次冷軋」)，係用於確保熔接罐耐壓強度(即鋼板降伏強度)的必要步驟。特別係若考慮使用本發明之經調整P含有量的素材時，2次冷軋的軋延率至少必需設為20%。另一方面，若軋延率超過50%，材質特性的非等向性變大，板寬方向與軋延(軋延)方向的耐力差會超過20MPa。且，新取板法(使鋼板軋延方向平行於罐身軸方向的取板法)的凸緣加工性與頸縮加工性會明顯劣化。再者，因製罐時的熔接，會使應變開放量變大，熔接熱影響部的軟化趨於明顯，因而容易發生凸緣破裂。所以，設定在50%以下。較佳20%以上30%以下，只要配合P含有量、與目標鋼板強度再適當選擇便可。具體係當P含有量超過0.020%、0.100%以下的較高情況時，最好設為較低的軋延率。The second cold rolling after continuous annealing (hereinafter referred to as "secondary cold rolling") is a necessary step for securing the compressive strength of the welded can (i.e., the steel plate fall strength). In particular, when considering the use of the material having the adjusted P content of the present invention, the rolling rate of the secondary cold rolling must be at least 20%. On the other hand, when the rolling ratio exceeds 50%, the anisotropy of the material properties becomes large, and the difference in the resistance between the sheet width direction and the rolling (rolling) direction exceeds 20 MPa. Further, the flange workability and the necking workability of the new plate take-up method (the plate take-up method in which the rolling direction of the steel sheet is parallel to the axis of the can body) are remarkably deteriorated. Further, since the strain at the time of canning is increased, the strain opening amount is increased, and the softening of the heat-affected portion of the welding tends to be conspicuous, so that the flange cracking easily occurs. Therefore, it is set below 50%. It is preferably 20% or more and 30% or less, and may be appropriately selected in accordance with the P content and the strength of the target steel sheet. Specifically, when the P content exceeds 0.020% and 0.100% or less, it is preferable to set a lower rolling ratio.
本發明中，經2次冷軋後，再於冷軋鋼板表面(至少單面)上形成鍍層，便可形成鍍鋼板。表面所形成的鍍層係在能適用於容器用鋼板的前提下均可適用。鍍層係可例示如：鍍錫、鍍鉻、鍍鎳、鍍鎳．鉻。且，經該等鍍敷處理後，再施行塗裝、或貼附有機樹脂薄膜等亦無妨。In the present invention, after two times of cold rolling, a plating layer is formed on the surface (at least one side) of the cold rolled steel sheet to form a plated steel sheet. The plating layer formed on the surface can be applied to a steel sheet for a container. The plating system can be exemplified by tin plating, chrome plating, nickel plating, and nickel plating. chromium. Further, after the plating treatment, it may be applied by coating or attaching an organic resin film.
將含有表1所示之成分、其餘由Fe及不可避免的雜質構成之鋼，利用轉爐施行熔製，並依連續鑄造法形成鋼坯。接著，將該等鋼坯在鋼坯萃取溫度設為1200℃、熱軋精軋溫度設為900℃、捲取溫度設為650℃的條件下，施行熱軋，而形成精軋厚度2.0mm熱軋板。然後，對該等熱軋板利用酸洗施行去銹處理(descaling treatment)，再施行軋延率90%的冷軋，而形成精軋厚度0.20mm的冷軋板，接著施行將均熱溫度設為750℃、均熱時間設為10~30s的連續退火、過時效處理及2次冷軋，而形成冷軋鋼板。The steel containing the components shown in Table 1 and the remainder consisting of Fe and unavoidable impurities was melted by a converter and formed into a slab by a continuous casting method. Next, the slabs were subjected to hot rolling under conditions of a slab extraction temperature of 1200 ° C, a hot rolling finishing temperature of 900 ° C, and a coiling temperature of 650 ° C to form a hot rolled sheet having a thickness of 2.0 mm. . Then, the hot-rolled sheets are subjected to descaling treatment by pickling, and then subjected to cold rolling at a rolling rate of 90% to form a cold-rolled sheet having a finish rolling thickness of 0.20 mm, followed by a soaking temperature setting. A cold-rolled steel sheet is formed by continuous annealing, overaging treatment, and secondary cold rolling at 750 ° C and a soaking time of 10 to 30 s.
另外，過時效處理條件及2次冷軋軋延率，係如表2及表3所示。In addition, the overaging treatment conditions and the secondary cold rolling rolling ratio are shown in Tables 2 and 3.
針對由以上所獲得鋼板，利用以下方法施行組織觀察，求取碳化物粒徑的密度及比例。並施行以下的試驗，而評估特性。With respect to the steel sheet obtained above, the structure was observed by the following method, and the density and ratio of the carbide particle diameter were determined. The following tests were performed to evaluate the characteristics.
將依上述所獲得冷軋鋼板埋藏於酚醛樹脂中，對截面施行研磨。接著，腐蝕液中係使用將苦酸、氫氧化鈉進行調合而成的苦酸鈉溶液，依80℃、60秒在腐蝕液中施行浸漬處理。接著，將碳化物依400倍光學顯微鏡觀察3視野(0.1375mm×0.1375mm左右範圍)。各視野中，依目視，求取粒徑1.5μm以下、粒徑超過1.5μm、3.0μm以下、超過3.0μm的碳化物個數，並求取3視野的密度與比例平均值。此時，碳化物粒徑設為最小徑，例如當碳化物形狀呈矩形或橢圓狀而存在有短軸與長軸時，便將最小徑設為本發明中的粒徑。The cold-rolled steel sheet obtained as described above was buried in a phenol resin, and the cross section was polished. Next, a sodium sulphate solution obtained by blending bitter acid and sodium hydroxide was used in the etching solution, and immersion treatment was performed on the etching solution at 80 ° C for 60 seconds. Next, the carbon crystals were observed under a 400-fold optical microscope for 3 fields (a range of about 0.1375 mm × 0.1375 mm). In each of the fields of view, the number of carbides having a particle diameter of 1.5 μm or less, a particle diameter of more than 1.5 μm, 3.0 μm or less, and more than 3.0 μm was determined by visual observation, and the density and the average value of the three fields of view were obtained. At this time, the carbide particle diameter is set to the minimum diameter. For example, when the carbide shape is rectangular or elliptical, and the short axis and the long axis exist, the minimum diameter is set as the particle diameter in the present invention.
從該等冷軋鋼板的寬度方向中央部朝軋延(L)方向，採取JIS 13號-B拉伸試驗片，並依應變速度衝頭速度：10mm/s實施拉伸試驗，測定拉伸強度TS與降伏強度YS。另外，拉伸試驗係在製品化後1日以內實施。將拉伸試驗片設為JIS 13號-B試驗片的理由係為了盡量減輕在標點外發生斷裂現象。A 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 (L) direction, and a tensile test was performed at a strain rate of 10 mm/s at a strain rate, and tensile strength was measured. TS and the drop strength YS. In addition, the tensile test was carried out within 1 day after the product was produced. The reason why the tensile test piece was set to JIS No. 13-B test piece was to minimize the occurrence of cracking outside the punctuation.
求取利用上述(i)拉伸試驗所測定之YS，與在板寬方向所採取之JIS 13號-B拉伸試驗片依與(i)同樣測得之YS間的差。The difference between the YS measured by the above (i) tensile test and the JIS No. 13-B tensile test piece taken in the sheet width direction in accordance with (i) was determined.
對該等冷軋鋼板施行鍍Sn處理(每單面的Sn附著量2.8g/m2 )，而形成鍍鋼板。在該鍍鋼板表面上，施行塗裝．印刷．透明漆塗裝之後，於未使用鍛壓油的情況下，對上述鋼板施行依以下條件施行杯拉伸，更施行第2次之再拉伸加工的深拉伸成形計100次，並調查頸縮的拉伸起皺發生率。The cold-rolled steel sheets were subjected to a Sn plating treatment (the amount of Sn adhesion per one surface was 2.8 g/m 2 ) to form a plated steel sheet. On the surface of the plated steel plate, coating is applied. print. After the clear varnish was applied, the forged steel was subjected to cup stretching under the following conditions, and the deep drawing forming of the second re-stretching process was performed 100 times, and the necking was investigated. The rate of stretching wrinkles.
深拉伸成形條件Deep drawing forming condition
胚料徑：200mmφBillet diameter: 200mmφ
潤滑條件：未使用鍛壓油Lubrication conditions: no forging oil
第1拉伸的拉伸比：1.5Stretch ratio of the first stretch: 1.5
第2拉伸的拉伸比：1.2Stretch ratio of the second stretch: 1.2
第3拉伸的拉伸比：1.2Stretch ratio of the third stretch: 1.2
第1~3拉伸的皺摺壓住壓力：最佳條件1~3 stretched wrinkles to suppress pressure: optimal conditions
凸緣加工：拉伸率8%Flange processing: 8% elongation
再拉伸模具圓角半徑：0.45mmRe-stretching mold fillet radius: 0.45mm
加工速度：0.3m/sProcessing speed: 0.3m/s
在(iii)的深拉伸成形中，調查凸緣破裂發生率。In the deep drawing of (iii), the incidence of flange fracture was investigated.
依目視觀察該等冷軋鋼板，將判斷屬光澤或色調不同的部分視為外觀不良。所觀察的100m單位中，即便僅有1個地方發生外觀不良，亦將該100m視為「外觀不良部」，觀察10000m並求取外觀不良率。These cold-rolled steel sheets were visually observed, and it was judged that the portions having different gloss or color tone were poor in appearance. Among the observed 100 m units, even if only one place had a poor appearance, the 100 m was regarded as a "defective appearance portion", and 10,000 m was observed to obtain an appearance defect rate.
依目視觀察連續鑄造後的鋼坯表面之鋼坯破裂狀況。The rupture condition of the slab on the surface of the slab after continuous casting was visually observed.
所觀察的1m單位中即便僅有1個地方出現破裂，便將該1m視為「外觀不良部」，觀察10m並求取外觀不良率。Even if only one of the observed 1 m units was broken, the 1 m was regarded as a "defective appearance portion", and 10 m was observed to obtain an appearance defect rate.
所獲得結果合併條件一起整理於表2及表3中。The obtained result combination conditions are collectively compiled in Tables 2 and 3.
由表2及表3中得知，本發明例的No.8~10、13~18、26~28、31~36係具有充分強度，且板寬方向與軋延方向的耐力差在20MPa以下，充分達成例如三片加工所必要的性能。此外，發現其外觀優異，亦不會發生頸縮起皺與凸緣破裂。此外，得知碳化物的密度、比例在較佳範圍的No.8~10、13~15、26~28、31~33將呈更優異的加工性。It is understood from Tables 2 and 3 that No. 8 to 10, 13 to 18, 26 to 28, and 31 to 36 of the present invention have sufficient strength, and the difference in endurance between the width direction and the rolling direction is 20 MPa or less. , fully achieve the performance necessary for three pieces of processing, for example. In addition, it was found to be excellent in appearance, and neck wrinkling and flange cracking did not occur. Further, it is found that the density and ratio of the carbides are in a preferable range of No. 8 to 10, 13 to 15, 26 to 28, and 31 to 33, which are more excellent in workability.
另一方面，未施行過時效處理的比較例No.1、2、19、20，二次冷軋的軋延率較低，並無法獲得強度。No.3~5、21~23係二次冷軋的軋延率達20%以上，雖強度提高，但L方向與C方向的耐力差超過20MPa，頸縮起皺與凸緣破裂的發生較為明顯。此外，易發生外觀不良情形。On the other hand, in Comparative Examples No. 1, 2, 19, and 20 in which the aging treatment was not performed, the rolling reduction rate of the secondary cold rolling was low, and the strength could not be obtained. No.3~5, 21~23 series secondary cold rolling rolling rate of 20% or more, although the strength is improved, but the L-direction and C-direction endurance difference exceeds 20MPa, necking wrinkles and flange cracking occur obvious. In addition, it is prone to poor appearance.
再者，二次冷軋的軋延率未滿20%的No.6、7、11、12、24、25、29、30並無法獲得強度。Further, No. 6, 7, 11, 12, 24, 25, 29, and 30 in which the rolling reduction ratio of the secondary cold rolling was less than 20% did not obtain strength.
再者，相關碳化物的密度、比例獲得以下發現。本發明的高強度容器用鋼板從加工性的觀點而言，較佳為粒徑1.5μm以下的碳化物密度超過102個/10000μm2 ，且粒徑超過1.5μm、3.0μm以下的碳化物密度超過63個/10000μm2 。此外，較佳係粒徑1.5μm以下的碳化物個數相對於總碳化物個數的比例超過52%，且粒徑3.0μm以下的碳化物個數相對於總碳化物個數的比例超過85%。Furthermore, the density and ratio of the relevant carbides were found as follows. The steel sheet for a high-strength container of the present invention preferably has a carbide density of more than 102 particles/10000 μm 2 having a particle diameter of 1.5 μm or less and a carbide density exceeding 1.5 μm and 3.0 μm or less in terms of workability. 63 / 10000 μm 2 . Further, it is preferable that the ratio of the number of carbides having a particle diameter of 1.5 μm or less to the total number of carbides exceeds 52%, and the ratio of the number of carbides having a particle diameter of 3.0 μm or less to the total number of carbides exceeds 85. %.
藉由粒徑1.5μm以下的碳化物密度超過102個/10000μm2 ，且粒徑超過1.5μm、3.0μm以下的碳化物密度超過63個/10000μm2 ，便可確保加工時發揮應力分散空隙機能的碳化物充分量，可形成更優異的加工性。更佳係粒徑1.5μm以下的碳化物密度達130個/10000μm2 以上、粒徑超過1.5μm、3.0μm以下的碳化物密度達80個/10000μm2 以上。When the carbide density of the particle diameter of 1.5 μm or less exceeds 102/10000 μm 2 and the carbide density of the particle diameter of more than 1.5 μm and 3.0 μm or less exceeds 63/10000 μm 2 , it is possible to ensure the stress dispersion void function during processing. A sufficient amount of carbide can form more excellent workability. More preferably, the carbide density of the particle diameter of 1.5 μm or less is 130/10000 μm 2 or more, and the carbide density of the particle diameter of more than 1.5 μm and 3.0 μm or less is 80/10000 μm 2 or more.
再者，若粒徑1.5μm以下的碳化物相個數相對於總碳化物個數的比例超過52%，且粒徑3.0μm以下的碳化物個數相對於總碳化物個數的比例超過85%，便將更加提高發揮應力分散空隙機能的碳化物效果，可更加改善加工性。更佳係粒徑1.5μm以下的碳化物個數相對於總碳化物個數的比例達55%以上，且粒徑3.0μm以下的碳化物個數相對於總碳化物個數的比例達90%以上。In addition, the ratio of the number of carbide phases having a particle diameter of 1.5 μm or less to the total number of carbides exceeds 52%, and the ratio of the number of carbides having a particle diameter of 3.0 μm or less to the total number of carbides exceeds 85. %, the carbide effect of the stress-dispersing void function can be further improved, and the workability can be further improved. More preferably, the ratio of the number of carbides having a particle diameter of 1.5 μm or less to the total number of carbides is 55% or more, and the ratio of the number of carbides having a particle diameter of 3.0 μm or less to the total number of carbides is 90%. the above.
再者，上述碳化物的密度及比例係藉由對冷軋後的鋼板依既定條件施行退火處理便可進行控制。具體而言，在冷軋後的連續退火步驟中，將鋼板的熱經歷調整於既定範圍內並施行過時效處理。Further, the density and the ratio of the above-mentioned carbides can be controlled by subjecting the cold-rolled steel sheets to annealing treatment under predetermined conditions. Specifically, in the continuous annealing step after cold rolling, the thermal history of the steel sheet is adjusted to a predetermined range and an overaging treatment is performed.
再者，表3所示係N含有量0.0065%、0.0043%，設為較佳範圍：未滿0.01%的實施例。由表3得知，藉由將N含有量設為未滿0.01%，便完全未發現鋼坯破裂，可防止鋼坯破裂。Further, Table 3 shows an example in which the content of N is 0.0065% and 0.0043%, and is preferably in the range of less than 0.01%. As is clear from Table 3, by setting the N content to less than 0.01%, the slab crack was not found at all, and the slab was prevented from being broken.
根據本發明，可獲得具有500MPa以上的TS，板寬方向與軋延方向的耐力差在20MPa以下，且施行凸緣加工與頸縮加工時不會發生破裂，呈加工性優異的高強度容器用鋼板。According to the present invention, it is possible to obtain a TS of 500 MPa or more, and the difference in endurance between the sheet width direction and the rolling direction is 20 MPa or less, and cracking does not occur during flange processing and necking processing, and it is used for a high-strength container excellent in workability. Steel plate.
再者，本發明藉由調整P含有量，且將第2次冷軋的軋延率設為20~50%，便可高強度化，並可解決軋延後的外觀問題、以及寬度方向與軋延方向的耐力差問題。Further, in the present invention, by adjusting the P content and setting the rolling ratio of the second cold rolling to 20 to 50%, the strength can be increased, and the appearance problem after rolling and the width direction can be solved. The problem of poor endurance in the rolling direction.
再者，藉由N成分設為較佳範圍之未滿0.01%，便可防止鋼坯破裂，俾可抑制製品的良率降低。Further, by setting the N component to less than 0.01% of the preferred range, the slab can be prevented from being broken, and the yield reduction of the product can be suppressed.
本發明的容器用鋼板係在頸縮加工與凸緣加工中不會發生破裂，可獲得優異強度，因而頗適用於以例如罐等食品容器、濾油器等非食品容器、電池等電子零件等為中心的容器用素材。The steel sheet for a container of the present invention is excellent in strength during necking and flange processing, and is excellent in strength. Therefore, it is suitable for use in food containers such as cans, non-food containers such as oil filters, and electronic parts such as batteries. Material for the center of the container.
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| CN101983251A (en) * | 2008-04-03 | 2011-03-02 | 杰富意钢铁株式会社 | High-strength steel plate for a can and method for manufacturing said high-strength steel plate |
| FI122143B (en) * | 2009-10-23 | 2011-09-15 | Rautaruukki Oyj | Procedure for the manufacture of a high-strength galvanized profile product and profile product |
| CN102286688A (en) * | 2010-06-21 | 2011-12-21 | 宝山钢铁股份有限公司 | Steel for high-hardness tin plating primitive plate and manufacture method thereof |
| EP2650396B1 (en) | 2010-12-06 | 2018-11-07 | Nippon Steel & Sumitomo Metal Corporation | Steel sheet for bottom covers of aerosol cans and method for producing same |
| JP5803660B2 (en) * | 2011-12-26 | 2015-11-04 | Ｊｆｅスチール株式会社 | High-strength, high-formability steel plate for cans and method for producing the same |
| KR20140108214A (en) * | 2012-04-19 | 2014-09-05 | 신닛테츠스미킨 카부시키카이샤 | Steel foil and method for producing same |
| CN103290312B (en) * | 2013-06-05 | 2015-01-21 | 首钢总公司 | Production method for increasing work hardening value of 440MPa-level carbon structural steel |
| CN103757534B (en) * | 2013-12-27 | 2016-01-20 | 首钢总公司 | A kind of cold-rolled steel sheet and production method thereof with good flange welding property |
| MY180058A (en) | 2014-04-30 | 2020-11-20 | Jfe Steel Corp | High-strength steel sheet for containers and method for producing the same |
| JP6465265B1 (en) * | 2017-07-31 | 2019-02-06 | Ｊｆｅスチール株式会社 | Crown steel plate, crown, and method for producing crown steel plate |
| CN109423577B (en) | 2017-08-30 | 2021-01-12 | 宝山钢铁股份有限公司 | High-strength multi-phase steel tinning raw plate and manufacturing method thereof |
| CN116657048A (en) | 2019-03-29 | 2023-08-29 | 杰富意钢铁株式会社 | Steel sheet for cans and method for producing same |
| CN110541123B (en) * | 2019-09-05 | 2021-06-15 | 首钢集团有限公司 | Cold-rolled strip steel for battery case and preparation method thereof |
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| JPS63310922A (en) * | 1987-06-11 | 1988-12-19 | Nippon Steel Corp | Production of 2cr material for welded can having superior flanging workability by continuous annealing |
| JP2761594B2 (en) * | 1989-07-03 | 1998-06-04 | 東洋鋼鈑 株式会社 | Manufacturing method of high strength ultra-thin steel sheet for cans with excellent in-plane anisotropy |
| JPH086143B2 (en) * | 1990-03-06 | 1996-01-24 | 新日本製鐵株式会社 | Manufacturing method of steel plate for ultra-thin welding can with excellent stripping property |
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| JP4179024B2 (en) * | 2003-04-09 | 2008-11-12 | 日立金属株式会社 | High speed tool steel and manufacturing method thereof |
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