TWI460029B - High tensile strength and high formability steel sheet for can and its production method - Google Patents
High tensile strength and high formability steel sheet for can and its production method Download PDFInfo
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
- C21D8/0426—Hot rolling
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- C—CHEMISTRY; METALLURGY
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- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
- C21D8/0436—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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
- C21D8/0468—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment between cold rolling steps
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- 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
- 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
- C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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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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Description
本發明係關於一種高強度且具有高加工性之罐用鋼板及其製造方法。The present invention relates to a steel sheet for cans having high strength and high workability and a method for producing the same.
飲料罐或食品罐所使用之鋼板中,存在對於罐蓋或罐底、三片罐之主體、沖壓罐等使用被稱為二次冷軋(DR,Double Reduce)材之鋼板之情形。退火後再次進行冷軋之DR材與僅進行軋縮率較小之調質輥軋之一次冷軋(SR,Single Reduce)材相比,容易使板厚變薄,且藉由使用薄鋼板而可降低成本。In the steel sheet used for the beverage can or the food can, there is a case where a steel sheet called a secondary cold rolling (DR) material is used for the can lid or the bottom of the can, the main body of the three-piece can, and the press can. The DR material which is cold-rolled again after annealing is easier to make the sheet thickness thinner than the one-time cold rolling (SR, Single Reduce) material which is only subjected to the temper rolling in which the rolling reduction is small, and by using a steel sheet. Can reduce costs.
製造DR材之DR法係藉由在退火後實施冷軋而產生加工硬化,因此可製造薄且硬之鋼板。然而,另一方面,藉由DR法製造之DR材缺乏延展性,因此與SR材相比,加工性較差。The DR method for producing a DR material is work hardened by performing cold rolling after annealing, so that a thin and hard steel sheet can be produced. On the other hand, however, the DR material produced by the DR method lacks ductility and is therefore inferior in workability compared with the SR material.
由三片構成之食品罐或飲料罐之主體材料於成形為筒狀之後,為了捲緊罐蓋或罐底而於兩端實施凸緣加工。因此,對罐體端部要求有良好之伸長率。After the main body material of the three-piece food can or beverage can is formed into a cylindrical shape, flange processing is performed at both ends in order to wind up the can lid or the can bottom. Therefore, a good elongation is required for the end of the can body.
另一方面,作為製罐素材之鋼板必需有對應於板厚之強度,於DR材之情形時,為了確保變薄而產生之經濟效應,必需有SR材以上之拉伸強度(約520 MPa以上)。On the other hand, the steel sheet as the material for the can is required to have a strength corresponding to the thickness of the sheet. In the case of the DR material, in order to ensure the economic effect of thinning, it is necessary to have a tensile strength of SR or more (about 520 MPa or more). ).
於一直以來所使用之DR材中,難以兼顧如上述之加工性 與強度該兩者,對於食品罐或飲料罐之主體材料主要使用SR材。然而,目前就成本降低之觀點而言,為了使板厚變薄,對於食品罐或飲料罐之主體材料亦期望使用DR材,擴大DR材之應用之要求提高。In the DR materials used in the past, it is difficult to balance the processability as described above. Both the strength and the strength, the SR material is mainly used for the main material of the food can or the beverage can. However, from the viewpoint of cost reduction, in order to make the thickness of the sheet thinner, it is also desired to use the DR material for the main material of the food can or the beverage can, and the application for expanding the DR material is increased.
根據該等情況,於專利文獻1中揭示有藉由使低碳鋼中之固溶N量為固定量以上、且規定總伸長值及蘭克福特值(Lankford value)而獲得之凸緣加工性優異之DR材。According to such a case, Patent Document 1 discloses flange workability obtained by setting the amount of solid solution N in the low carbon steel to a fixed amount or more and defining a total elongation value and a Rankford value. Excellent DR material.
於專利文獻2中揭示有藉由規定低碳鋼中之固溶N量及固溶C量而獲得之凸緣加工性優異之DR材。Patent Document 2 discloses a DR material which is excellent in flange workability obtained by specifying the amount of solid solution N and the amount of solid solution C in the low carbon steel.
專利文獻1:日本專利特開2007-177315號公報Patent Document 1: Japanese Patent Laid-Open Publication No. 2007-177315
專利文獻2:日本專利特開2002-294399號公報Patent Document 2: Japanese Patent Laid-Open Publication No. 2002-294399
然而,上述習知技術均存在問題。However, the above conventional techniques all have problems.
於專利文獻1中,揭示有於將輥軋方向之總伸長值以X表示,將平均蘭克福特值以Y表示之情形時,滿足X≧10%且Y≧0.9或X<10%且Y≧-0.05X+1.4之關係之DR鋼板,但因焊接條件仍會產生熱影響區軟化(HAZ,Heat-Affected Zone softening),產生凸緣碎裂。Patent Document 1 discloses that when the total elongation value in the rolling direction is represented by X and the average Rankford value is represented by Y, X≧10% and Y≧0.9 or X<10% and Y are satisfied. DR steel plate with a relationship of -0.05X+1.4, but due to welding conditions, HAZ (Heat-Affected Zone softening) is generated, resulting in flange fracture.
於專利文獻2所記載之製造方法中,因連續退火步驟中必 需進行過時效處理,故而製造成本變得過大。In the manufacturing method described in Patent Document 2, it is necessary in the continuous annealing step. The aging treatment is required, so the manufacturing cost becomes too large.
本發明係有鑑於該情況而完成者,其目的在於提供一種適宜作為罐蓋、罐底及三片罐主體等之材料的高強度高加工性罐用鋼板及其製造方法。The present invention has been made in view of the above circumstances, and an object thereof is to provide a steel sheet for high-strength, high-workability cans which is suitable as a material for a can lid, a can bottom, and a three-piece can body, and a method for producing the same.
本發明者等人為解決上述問題而進行了深入研究。其結果獲得以下之發現。The present inventors conducted intensive studies to solve the above problems. As a result, the following findings were obtained.
為了兼顧加工性及強度該兩者,有效的是,添加適當量之N而賦予強度,並且將退火後之二次冷軋率限制於適當之範圍而確保加工性。In order to achieve both workability and strength, it is effective to add an appropriate amount of N to impart strength, and to limit the secondary cold rolling rate after annealing to an appropriate range to ensure workability.
又,若熱軋前之鋼坯再加熱溫度較低,則鑄造後析出之AlN之再溶解無法充分地進行,若熱軋後之捲取溫度較高,則析出之AlN變得過多。於任一情形時,承擔強度之固溶N均為不足,因此鋼坯再加熱溫度或捲取溫度均必需限制於適當之溫度範圍。Further, if the reheating temperature of the slab before hot rolling is low, re-dissolution of AlN precipitated after casting cannot be sufficiently performed, and if the coiling temperature after hot rolling is high, the precipitated AlN becomes excessive. In either case, the solid solution N of the strength is insufficient, so the reheating temperature or the coiling temperature of the billet must be limited to the appropriate temperature range.
進而,藉由將退火溫度及退火時間限制於適當之範圍,而可實現強度與加工性良好之平衡。Further, by limiting the annealing temperature and the annealing time to an appropriate range, a balance between strength and workability can be achieved.
本發明係基於以上之見解而完成者,其主旨如下所述。The present invention has been completed based on the above findings, and the gist thereof is as follows.
[1]一種高強度高加工性罐用鋼板,其特徵在於,以質量%計含有C:0.001%以上且0.080%以下、Si:0.003%以上且0.100%以下、Mn:0.10%以上且0.80%以下、P:0.001%以上且0.100%以下、S:0.001%以上且0.020%以下、Al:0.005% 以上且0.100%以下、N:0.0050%以上且0.0150%以下、B:0.0002%以上且0.0050%以下,其餘部分包含Fe及不可避免之雜質,進而,於輥軋方向剖面中,含有面積率為0.01~1.00%之結晶粒伸展度為5.0以上之結晶粒。[1] A steel sheet for high-strength and high-processability, which contains C: 0.001% or more and 0.080% or less, Si: 0.003% or more and 0.100% or less, and Mn: 0.10% or more and 0.80% by mass%. Hereinafter, P: 0.001% or more and 0.100% or less, S: 0.001% or more and 0.020% or less, and Al: 0.005% The above is 0.100% or less, N: 0.0050% or more and 0.0150% or less, B: 0.0002% or more and 0.0050% or less, and the remainder contains Fe and unavoidable impurities, and further, the area ratio is 0.01 in the cross section in the rolling direction. ~1.00% of crystal grains having a crystal grain stretch of 5.0 or more.
[2]一種高強度高加工性罐用鋼板之製造方法,其特徵在於,藉由連續鑄造使鋼成為鋼坯,將鋼坯再加熱溫度設為1200℃以上進行熱軋後以未滿650℃之溫度捲取,繼而進行一次冷軋,繼而,以均熱溫度680~760℃、均熱時間10~20秒進行連續退火,繼而以20%以下之軋縮率進行二次冷軋;上述鋼係以質量%計含有C:0.001%以上且0.080%以下、Si:0.003%以上且0.100%以下、Mn:0.10%以上且0.80%以下、P:0.001%以上且0.100%以下、S:0.001%以上且0.020%以下、Al:0.005%以上且0.100%以下、N:0.0050%以上且0.0150%以下、B:0.0002%以上且0.0050%以下,其餘部分包含Fe及不可避免之雜質。[2] A method for producing a steel sheet for high-strength and high-processability, characterized in that the steel is slab by continuous casting, and the slab reheating temperature is 1200 ° C or higher and hot rolling is performed at a temperature of less than 650 ° C. Winding, followed by a cold rolling, followed by continuous annealing at a soaking temperature of 680 to 760 ° C and a soaking time of 10 to 20 seconds, followed by secondary cold rolling at a rolling reduction of 20% or less; The mass% includes C: 0.001% or more and 0.080% or less, Si: 0.003% or more and 0.100% or less, Mn: 0.10% or more and 0.80% or less, P: 0.001% or more and 0.100% or less, and S: 0.001% or more. 0.020% or less, Al: 0.005% or more and 0.100% or less, N: 0.0050% or more and 0.0150% or less, and B: 0.0002% or more and 0.0050% or less, and the balance contains Fe and unavoidable impurities.
再者,本說明書中,表示鋼之成分之%均為質量%。In addition, in this specification, the % which shows the component of steel is a mass %.
根據本發明,可獲得拉伸強度為520 MPa以上且斷裂伸長率為7%以上之高強度高加工性罐用鋼板。According to the present invention, a steel sheet for high strength and high workability cans having a tensile strength of 520 MPa or more and an elongation at break of 7% or more can be obtained.
其結果,因原板(鋼板)之加工性提高,故而於三片罐之凸緣加工時不會產生碎裂,從而可利用板厚較薄之DR材進行製罐,達成罐用鋼板之大幅度變薄。As a result, the workability of the original plate (steel plate) is improved, so that no chipping occurs during the flange processing of the three-piece can, and the DR material having a small thickness can be used for canning, and the steel plate for the can is large. Thinning.
以下,詳細地說明本發明。Hereinafter, the present invention will be described in detail.
本發明之罐用鋼板係拉伸強度為520 MPa以上且斷裂伸長率為7%以上之高強度高加工性罐用鋼板。而且,此種鋼板可藉由使用含有0.0050%以上且0.0150%以下之N之鋼,將熱軋前之鋼坯再加熱溫度、熱軋後之捲取溫度、退火溫度、退火時間及二次冷軋率設定為適當之條件而製造。The steel sheet for cans of the present invention is a steel sheet for high strength and high workability cans having a tensile strength of 520 MPa or more and an elongation at break of 7% or more. Moreover, the steel sheet can be reheated by hot rolling, the coiling temperature after hot rolling, the annealing temperature, the annealing time, and the secondary cold rolling by using a steel containing 0.0050% or more and 0.0150% or less of N. The rate is set to the appropriate conditions for manufacture.
對本發明之罐用鋼板之成分組成進行說明。The composition of the steel sheet for cans of the present invention will be described.
C:0.001%以上且0.080%以下C: 0.001% or more and 0.080% or less
若C量超出0.080%,則加工性惡化,冷軋性亦降低。又,於鑄造時容易產生亞包晶碎裂,存在鋼坯加工等成本增加之可能性。因此,C量設為0.080%以下。另一方面,若C量未滿0.001%,則結晶粒之粗大化變得明顯,加工部中產生表面粗糙不良之危險性增大。因此,C量設為0.001%以上且0.080%以下。When the amount of C exceeds 0.080%, workability is deteriorated and cold rolling properties are also lowered. Further, sub-cracking is likely to occur during casting, and there is a possibility that the cost of billet processing increases. Therefore, the amount of C is set to 0.080% or less. On the other hand, when the amount of C is less than 0.001%, the coarsening of crystal grains becomes conspicuous, and the risk of occurrence of surface roughness defects in the processed portion increases. Therefore, the amount of C is set to be 0.001% or more and 0.080% or less.
Si:0.003%以上且0.100%以下Si: 0.003% or more and 0.100% or less
若Si量超出0.100%,則產生表面處理性之降低、耐蝕性之惡化等問題,因此上限設為0.100%。另一方面,若未滿0.003%,則精煉成本變得過大,因此下限設為0.003%。When the amount of Si exceeds 0.100%, problems such as a decrease in surface treatment property and deterioration in corrosion resistance occur, so the upper limit is made 0.100%. On the other hand, if it is less than 0.003%, the refining cost becomes too large, so the lower limit is made 0.003%.
Mn:0.10%以上且0.80%以下Mn: 0.10% or more and 0.80% or less
Mn具有防止由S導致之熱軋中之赤熱脆性,使結晶粒微細化之作用,在確保較理想之材質方面為必要之元素。為了 發揮該等效果,必需添加至少0.10%以上。另一方面,若過量地添加Mn,則耐蝕性惡化,且鋼板過度地硬質化,因此上限設為0.80%。Mn has an effect of preventing red hot brittleness in hot rolling caused by S and refining crystal grains, and is an essential element for securing a preferable material. in order to To achieve these effects, it is necessary to add at least 0.10% or more. On the other hand, when Mn is excessively added, the corrosion resistance is deteriorated and the steel sheet is excessively hardened, so the upper limit is made 0.80%.
P:0.001%以上且0.100%以下P: 0.001% or more and 0.100% or less
P係使鋼硬質化、使加工性惡化,同時亦使耐蝕性惡化之有害元素。因此,上限設為0.100%。另一方面,若將P設為未滿0.001%,則脫P成本變得過大。因此,下限設為0.001%。P is a harmful element that hardens steel and deteriorates workability, and also deteriorates corrosion resistance. Therefore, the upper limit is set to 0.100%. On the other hand, if P is set to less than 0.001%, the cost of removing P becomes excessive. Therefore, the lower limit is set to 0.001%.
S:0.001%以上且0.020%以下S: 0.001% or more and 0.020% or less
S係作為中介物存在於鋼中,且係導致加工性降低、耐蝕性惡化之有害元素。因此,上限設為0.020%。另一方面,若將S設為未滿0.001%,則脫S成本變得過大。因此,下限設為0.001%。The S system is present as an intermediary in steel and is a harmful element that causes deterioration in workability and deterioration in corrosion resistance. Therefore, the upper limit is set to 0.020%. On the other hand, if S is set to less than 0.001%, the cost of the S is excessively increased. Therefore, the lower limit is set to 0.001%.
Al:0.005%以上且0.100%以下Al: 0.005% or more and 0.100% or less
Al係作為製鋼時之脫酸材而必要之元素。若添加量較少,則脫酸不充分,中介物增加,加工性惡化。若含量為0.005%以上,則可視為充分地進行脫酸。另一方面,若含量超出0.100%,則由氧化鋁簇等所致之表面缺陷之產生頻度增加。因此,Al量設為0.005%以上且0.100%以下。Al is an essential element for deacidification at the time of steel making. When the amount added is small, the deacidification is insufficient, the intermediary is increased, and the workability is deteriorated. When the content is 0.005% or more, it can be considered that the deacidification is sufficiently performed. On the other hand, if the content exceeds 0.100%, the frequency of occurrence of surface defects caused by alumina clusters or the like increases. Therefore, the amount of Al is set to be 0.005% or more and 0.100% or less.
N:0.0050%以上且0.0150%以下N: 0.0050% or more and 0.0150% or less
於本發明之罐用鋼板中,抑制二次冷軋率而確保伸長率,另一方面,藉由提高N量而有助於高強度。若N量未滿 0.0050%,則無法獲得用以獲取鋼板之薄片化產生之明顯之經濟效應所需之拉伸強度520 MPa。因此,N量設為0.0050%以上。另一方面,若N量超出0.0150%,則會過剩硬質,而難以在確保加工性之狀態下藉由二次冷軋製造較薄之鋼板。因此,N量設為0.0150%以下。In the steel sheet for cans of the present invention, the secondary cold rolling ratio is suppressed to ensure elongation, and on the other hand, the amount of N is increased to contribute to high strength. If the amount of N is not full At 0.0050%, the tensile strength required to obtain the significant economic effect of the flaking of the steel sheet is 520 MPa. Therefore, the amount of N is set to 0.0050% or more. On the other hand, when the amount of N exceeds 0.0150%, it is excessively hard, and it is difficult to produce a thin steel sheet by secondary cold rolling while ensuring workability. Therefore, the amount of N is set to 0.0150% or less.
B:0.0002%以上且0.0050%以下B: 0.0002% or more and 0.0050% or less
B具有抑制焊接部附近之熱影響部之晶粒生長,防止由局部性強度降低而導致之凸緣加工時之碎裂的效果。為了充分地獲得防止碎裂之效果,B量必需為0.0002%以上。另一方面,即便超出0.0050%,亦無法期望進一步之效果,成本變高。因此,B量設為0.0002%以上且0.0050%以下。B has an effect of suppressing grain growth of the heat-affected zone in the vicinity of the welded portion and preventing chipping at the time of flange processing due to a decrease in local strength. In order to sufficiently obtain the effect of preventing chipping, the amount of B must be 0.0002% or more. On the other hand, even if it exceeds 0.0050%, further effects cannot be expected, and the cost becomes high. Therefore, the amount of B is set to be 0.0002% or more and 0.0050% or less.
其餘部分設為Fe及不可避免之雜質,但亦可包含公知之焊接罐用鋼板中通常所含之成分元素。例如,可視目的而含有Cr:0.10%以下、Cu:0.20%以下、Ni:0.15%以下、Mo:0.05%以下、Ti:0.3%以下、Nb:0.3%以下、Zr:0.3%以下、V:0.3%以下、Ca:0.01%以下等成分元素(各者之元素成分範圍包含0%)。The rest is set to Fe and unavoidable impurities, but may also contain constituent elements which are usually contained in steel sheets for welding cans. For example, it may contain Cr: 0.10% or less, Cu: 0.20% or less, Ni: 0.15% or less, Mo: 0.05% or less, Ti: 0.3% or less, Nb: 0.3% or less, and Zr: 0.3% or less, V: Component elements such as 0.3% or less and Ca: 0.01% or less (each elemental component range includes 0%).
其次,對本發明之高強度高加工性罐用鋼板之結晶粒進行說明。Next, the crystal grains of the steel sheet for high strength and high workability cans of the present invention will be described.
於輥軋方向剖面中,必需包含面積率為0.01~1.00%之伸展度為5.0以上之結晶粒。通常,若使用如上所示之N量之鋼製作DR材,則輥軋方向剖面之結晶粒之伸展度未滿3.0。 然而,藉由將退火溫度及退火時間限制於適當之範圍,一部分結晶粒之伸展度表現為變大。而且,雖機制尚不明確,但於伸展度為5.0以上之結晶粒以0.01%以上之面積率存在之情形時,加工性提高。若面積率超出1.00%,則反而會阻礙加工性。由以上可知,伸展度為5.0以上之結晶粒之面積率設為0.01~1.00%。另一方面,伸展度超出50.0之結晶粒之加工性提高之效果較小,因此更佳為將伸展度為5.0以上且50.0以下之結晶粒之面積率設為0.01~1.00%。In the cross section in the rolling direction, it is necessary to include crystal grains having an area ratio of 0.01 to 1.00% and an elongation of 5.0 or more. In general, when a DR material is produced using the N amount of steel as described above, the degree of stretching of the crystal grains in the cross section in the rolling direction is less than 3.0. However, by limiting the annealing temperature and the annealing time to an appropriate range, the elongation of a part of the crystal grains appears to be large. Further, although the mechanism is not clear, the workability is improved when the crystal grains having an elongation of 5.0 or more are present at an area ratio of 0.01% or more. If the area ratio exceeds 1.00%, it will hinder the workability. From the above, it is understood that the area ratio of the crystal grains having an elongation of 5.0 or more is set to 0.01 to 1.00%. On the other hand, since the effect of improving the workability of the crystal grains having an elongation of more than 50.0 is small, it is more preferable that the area ratio of the crystal grains having an elongation of 5.0 or more and 50.0 or less is 0.01 to 1.00%.
再者,輥軋方向剖面之結晶粒之伸展度可藉由應用文獻「JIS G 0551」所示之結晶粒度之顯微鏡試驗方法,對各結晶粒測定輥軋長度方向之長度及與輥軋長度方向成直角之長度,並計算其比而求得。又,根據本發明之鋼組成、製造方法,所形成之雪明碳鐵、波來鐵與肥粒鐵粒相比非常小,因此結晶粒徑、伸展度之測定係僅以肥粒鐵結晶粒作為對象而進行。Further, the elongation of the crystal grains in the cross-section of the rolling direction can be determined by the microscopic test method of the crystal grain size shown in the literature "JIS G 0551", and the length of the rolling direction and the length direction of the rolling are measured for each crystal grain. The length of the right angle is calculated and the ratio is calculated. Moreover, according to the steel composition and the manufacturing method of the present invention, the formed swarf carbon iron and the stellite iron are very small compared with the ferrite iron particles, and therefore the crystal grain size and the elongation are determined only by the ferrite iron crystal grains. It is carried out as an object.
結晶粒之面積率可藉由文獻「JIS G 0555附屬書1」所示之點算法進行測定。其目的在於測定鋼材中之非金屬中介物之面積率,但亦可用於如上述之特定形狀之結晶粒之面積率測定。又,亦可使用顯微鏡照片及任意之圖像解析裝置測定面積率。The area ratio of the crystal grains can be measured by a dot algorithm shown in the document "JIS G 0555 Attachment 1". The purpose is to determine the area ratio of the non-metallic interpolymer in the steel, but it can also be used for the area ratio measurement of the crystal grains of the specific shape as described above. Further, the area ratio can be measured using a microscope photograph and an arbitrary image analysis device.
其次,對本發明之罐用鋼板之製造方法進行說明。Next, a method of producing the steel sheet for a can according to the present invention will be described.
本發明之高強度高加工性罐用鋼板係藉由以下方法而製 造,即,使用藉由連續鑄造而製造出之包含上述組成之鋼坯,將熱軋前之鋼坯再加熱溫度設為1200℃以上,進行熱軋之後以未滿650℃之溫度捲取,繼而進行一次冷軋,繼而以均熱溫度680~760℃、均熱時間10~20秒進行連續退火,繼而以20%以下之軋縮率進行二次冷軋。The steel sheet for high strength and high workability of the present invention is produced by the following method The steel slab having the above composition produced by continuous casting is used, and the slab reheating temperature before hot rolling is set to 1200 ° C or higher, and after hot rolling, it is taken up at a temperature of less than 650 ° C, and then carried out. One cold rolling, followed by continuous annealing at a soaking temperature of 680 to 760 ° C and a soaking time of 10 to 20 seconds, followed by secondary cold rolling at a rolling reduction of 20% or less.
通常,難以僅藉由一次冷軋而製成如可獲得明顯之經濟效應之較薄之板厚。即,為了藉由一次冷軋而獲得較薄之板厚,對輥軋機之負載變得過大,就設備能力而言無法滿足。例如,於將最終板厚設為0.15 mm之情形時,若將熱軋後之板厚設為2.0 mm,則需要92.5%之較大之一次冷軋率。又,雖亦考慮到為使冷軋後之板厚變小而於熱軋之階段較通常薄地進行輥軋,但若使熱軋之軋縮率變大,則輥軋中之鋼板之溫度降低變大,而無法獲得既定之終軋溫度。進而,若使退火前之板厚變小,則於實施連續退火之情形時,退火中產生鋼板之斷裂或變形等故障之可能性增大。因該等原因,本發明中,於退火後實施第二次冷軋,獲得極薄之鋼板。In general, it is difficult to form a thinner sheet thickness such as to obtain a significant economic effect by only one cold rolling. That is, in order to obtain a thinner plate thickness by one cold rolling, the load on the rolling mill becomes too large, which cannot be satisfied in terms of equipment capability. For example, when the final thickness is 0.15 mm, if the thickness after hot rolling is 2.0 mm, a larger primary cold rolling ratio of 92.5% is required. Further, although it is considered that the thickness of the steel sheet after cold rolling is reduced and the rolling is performed at a hot rolling stage, if the rolling reduction ratio of the hot rolling is increased, the temperature of the steel sheet during rolling is lowered. It becomes larger and it is impossible to obtain a predetermined finishing temperature. Further, when the thickness of the sheet before annealing is made small, when continuous annealing is performed, there is a possibility that failure such as cracking or deformation of the steel sheet during annealing increases. For these reasons, in the present invention, the second cold rolling is performed after annealing to obtain an extremely thin steel sheet.
熱軋前之鋼坯再加熱溫度:1200℃以上Reheating temperature of billet before hot rolling: above 1200 °C
若熱軋前之鋼坯再加熱溫度未滿1200℃,則鑄造後所析出之AlN之再溶解無法充分地進行,承擔強度之固溶N量變得不足。因此,熱軋前之鋼坯再加熱溫度設為1200℃以上。另一方面,過度之加熱關係到能量成本之上升,因此較佳為1200~1300℃。If the reheating temperature of the slab before hot rolling is less than 1200 ° C, the re-dissolution of AlN precipitated after casting cannot be sufficiently performed, and the amount of solid solution N which is subjected to strength becomes insufficient. Therefore, the reheating temperature of the slab before hot rolling is set to 1200 ° C or higher. On the other hand, excessive heating is related to an increase in energy cost, so it is preferably 1200 to 1300 °C.
熱軋後之捲取溫度:未滿650℃Coiling temperature after hot rolling: less than 650 ° C
若熱軋後之捲取溫度為650℃以上,則AlN過剩地析出,承擔強度之固溶N量變得不足。因此,熱軋後之捲取溫度設為未滿650℃。另一方面,設為過低之捲取溫度會導致輥軋速度之降低等成本上升,因此較佳為580~620℃。When the coiling temperature after hot rolling is 650 ° C or more, AlN is excessively precipitated, and the amount of solid solution N which is subjected to strength becomes insufficient. Therefore, the coiling temperature after hot rolling is set to be less than 650 °C. On the other hand, the coiling temperature which is set too low may cause a cost increase such as a decrease in the rolling speed, and therefore it is preferably 580 to 620 °C.
一次冷軋One cold rolling
一次冷軋率並無特別限定,但為了最終獲得極薄之鋼板,一次冷軋之軋縮率必需以某種程度增大。即,根據上述原因,增大熱軋率之情形欠佳,二次冷軋率因下述原因而必需限制。因此,一次冷軋率較佳為超出85%。另一方面,若一次冷軋率超出92%,則對輥軋機之負載變得過大,因此,進而較佳為89~92%。The primary cold rolling rate is not particularly limited, but in order to finally obtain an extremely thin steel sheet, the rolling reduction rate of the primary cold rolling must be increased to some extent. That is, for the above reasons, the case where the hot rolling ratio is increased is not preferable, and the secondary cold rolling ratio is necessarily limited by the following reasons. Therefore, the primary cold rolling rate is preferably more than 85%. On the other hand, if the primary cold rolling ratio exceeds 92%, the load on the rolling mill becomes too large, and therefore, it is more preferably 89 to 92%.
退火annealing
退火係藉由連續退火而進行,均熱溫度設為680~760℃,均熱時間設為10~20秒。若均熱溫度未滿680℃,或均熱時間未滿10秒,則輥軋方向剖面之伸展度為5.0以上之結晶粒之面積率會超出1.00%,加工性變得不充分。又,若均熱溫度超出760℃,或均熱時間超出20秒,則輥軋方向剖面之伸展度為5.0以上之結晶粒之面積率未滿0.01%,無法獲得加工性提高之效果。Annealing is carried out by continuous annealing, the soaking temperature is set to 680 to 760 ° C, and the soaking time is set to 10 to 20 seconds. When the soaking temperature is less than 680 ° C or the soaking time is less than 10 seconds, the area ratio of the crystal grains having a degree of stretching of 5.0 or more in the rolling direction section exceeds 1.00%, and workability is insufficient. In addition, when the soaking temperature exceeds 760 ° C or the soaking time exceeds 20 seconds, the area ratio of the crystal grains having a degree of stretching of 5.0 or more in the rolling direction section is less than 0.01%, and the effect of improving workability cannot be obtained.
二次冷軋率:20%以下Secondary cold rolling rate: 20% or less
二次冷軋率設為20%以下。若二次冷軋率超出20%,則 加工硬化變得過大,無法獲得7%以上之斷裂伸長率。因此,二次冷軋率設為20%以下。另一方面,若二次冷軋率未滿10%,則由採用DR法而產生之板厚減小之經濟效應變小,因此,較佳為10%以上且20%以下。The secondary cold rolling ratio is set to 20% or less. If the secondary cold rolling rate exceeds 20%, then The work hardening becomes too large, and the elongation at break of 7% or more cannot be obtained. Therefore, the secondary cold rolling ratio is set to 20% or less. On the other hand, when the secondary cold rolling ratio is less than 10%, the economic effect of reducing the thickness of the sheet by the DR method is small, and therefore it is preferably 10% or more and 20% or less.
二次冷軋以後,按照慣用方法進行鍍敷等步驟,最終加工為罐用鋼板。After the secondary cold rolling, the steps such as plating are carried out in accordance with a conventional method, and finally processed into a steel sheet for cans.
將含有表1所示之成分組成、其餘部分包含Fe及不可避免之雜質之鋼於轉爐中進行熔化,藉由連續鑄造法獲得鋼坯。對於獲得之鋼坯,以表2所示之條件進行再加熱,以表2所示之條件實施熱軋、一次冷軋。熱軋之終軋溫度設為890℃,熱軋後實施酸洗。繼而,一次冷軋之後,以表2所示之條件進行連續退火,繼而,以表2所示之條件實施二次冷軋。A steel containing the composition shown in Table 1 and containing the Fe and the unavoidable impurities in the remainder was melted in a converter, and a slab was obtained by a continuous casting method. The obtained slab was reheated under the conditions shown in Table 2, and hot rolling and primary cold rolling were carried out under the conditions shown in Table 2. The finish rolling temperature of hot rolling was set to 890 ° C, and pickling was performed after hot rolling. Then, after one cold rolling, continuous annealing was carried out under the conditions shown in Table 2, and then secondary cold rolling was carried out under the conditions shown in Table 2.
對由以上所獲得之鋼板之兩面連續地實施鍍Sn,獲得單面之Sn附著量為2.8 g/m2 之鍍錫鐵皮。Sn plating was continuously performed on both surfaces of the steel sheet obtained above, and a tin-plated iron sheet having a Sn adhesion amount of 2.8 g/m 2 on one side was obtained.
對於由以上所獲得之鍍敷鋼板(鍍錫鐵皮),進行210℃、20分鐘之與塗裝燒附相當之熱處理之後,進行拉伸試驗。拉伸試驗係使用JIS5號尺寸之拉伸試驗片,測定輥軋直角方向之拉伸強度及斷裂伸長率。The plated steel sheet (tin-plated iron sheet) obtained above was subjected to a tensile test at 210 ° C for 20 minutes after heat treatment equivalent to coating and baking. In the tensile test, a tensile test piece of JIS No. 5 size was used, and the tensile strength and elongation at break in the direction perpendicular to the rolling were measured.
又,使用經實施與塗裝燒附相當之熱處理之鋼板,藉由縫焊接(Seam Welding)進行外徑52.8 mm之罐體成形,對端部進行縮幅加工(Neck Forming)直至外徑為50.4mm後,進行凸緣加工直至外徑為55.4mm,評價凸緣碎裂產生之有無。罐體成形係製成190 g飲料罐尺寸,沿鋼板輥軋方向進行焊接。縮幅加工係藉由壓鑄方式(Die-neck Processing)進行,凸緣加工係藉由旋轉凸緣方式(Spin-flange Processing)進行。將凸緣加工部產生碎裂之情形評價為×,將未產生碎裂之情形評價為○。Further, a steel plate having a heat treatment equivalent to that of the coating and baking is used, and a can body having an outer diameter of 52.8 mm is formed by seam welding, and the end portion is subjected to Neck Forming until the outer diameter is 50.4. After mm, the flange processing was performed until the outer diameter was 55.4 mm, and the presence or absence of cracking of the flange was evaluated. The can body was formed into a 190 g beverage can size and welded along the direction in which the steel sheet was rolled. The necking process is performed by Die-neck Processing, and the flange processing is performed by a spin-flange process. The case where the flanged portion was broken was evaluated as ×, and the case where no chipping occurred was evaluated as ○.
又,採取鍍敷鋼板之樣品,測定輥軋方向剖面之伸展度為5.0以上之結晶粒之面積率。輥軋方向剖面之結晶粒之伸展度係對鋼板之垂直剖面進行研磨並藉由硝酸浸蝕液蝕刻使晶界現出之後,應用文獻「JIS G 0551」所記載之直線試驗線之切割法,對各結晶粒進行測定。Further, a sample of a plated steel sheet was taken, and the area ratio of the crystal grains having a degree of extension in the rolling direction section of 5.0 or more was measured. The elongation of the crystal grains in the rolling direction section is obtained by grinding the vertical section of the steel sheet and etching the grain boundary by nitric acid etching solution, and then applying the cutting method of the straight line test line described in the document "JIS G 0551". Each crystal grain was measured.
將獲得之結果示於表3。The results obtained are shown in Table 3.
由表3可知,本發明例之No.1~5之強度優異,達成作為極薄之罐用鋼板所需之拉伸強度520 MPa以上。又,加工性亦優異,具有罐蓋或三片罐主體之加工所需之7%以上之斷裂伸長率。As is clear from Table 3, the strength of Nos. 1 to 5 of the present invention is excellent, and the tensile strength required for the extremely thin steel sheet for cans is 520 MPa or more. Moreover, it is excellent in workability, and has an elongation at break of 7% or more which is required for processing the can lid or the three-piece can body.
另一方面,比較例之No.6因C含量過多,故而因二次冷軋而損及加工性,斷裂伸長率不足。比較例之No.7因不含B,故而焊接熱影響部極端地軟質化,且凸緣加工中產生碎裂。比較例之No.8因鋼坯再加熱溫度過低,故而鑄造後所析出之AlN未充分地溶解,又,比較例之No.9因捲取溫度過高,故而AlN過剩地析出,因此任一者均為作為AlN存在之N量過多,拉伸強度不足。比較例之No.10因N含量過少,故而拉伸強度不足。比較例之No.11因連續退火之均熱溫度過低,故而伸展度為5.0以上之結晶粒之面積率變得 過大,斷裂伸長率不足。比較例之No.12因連續退火之均熱溫度過高,比較例之No.13因連續退火之均熱時間過長,故而任一者均為伸展度為5.0以上之結晶粒之面積率均變得過小,斷裂伸長率不足。比較例之No.14因二次冷軋率過大,故而加工硬化變得過大,斷裂伸長率不足。On the other hand, in No. 6 of the comparative example, since the C content was too large, workability was impaired by secondary cold rolling, and the elongation at break was insufficient. In the comparative example No. 7, since the B was not contained, the welded heat-affected zone was extremely softened, and chipping occurred during the flange processing. In Comparative Example No. 8, since the reheating temperature of the slab was too low, AlN precipitated after casting was not sufficiently dissolved, and in Comparative Example No. 9, since the coiling temperature was too high, AlN was excessively precipitated, so that either In the case where all of N is present as AlN, the tensile strength is insufficient. In Comparative Example No. 10, since the N content was too small, the tensile strength was insufficient. In Comparative Example No. 11, since the soaking temperature of continuous annealing is too low, the area ratio of crystal grains having a degree of extension of 5.0 or more becomes Too large, the elongation at break is insufficient. In Comparative Example No. 12, the soaking temperature of the continuous annealing was too high, and in Comparative Example No. 13, the soaking time of the continuous annealing was too long, so that the area ratio of the crystal grains having the elongation of 5.0 or more was It becomes too small and the elongation at break is insufficient. In the comparative example No. 14, since the secondary cold rolling ratio was too large, the work hardening became too large, and the elongation at break was insufficient.
本發明之罐用鋼板具有520 MPa以上之拉伸強度、7%以上之斷裂伸長率,可由較薄之板厚而獲得。因此,作為用於以低成本製造罐蓋、罐底、三片罐主體等之材料而最佳。The steel sheet for cans of the present invention has a tensile strength of 520 MPa or more and an elongation at break of 7% or more, and can be obtained from a relatively thin plate thickness. Therefore, it is preferable as a material for manufacturing a can lid, a can bottom, a three-piece can body or the like at low cost.
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JP6060603B2 (en) * | 2011-10-20 | 2017-01-18 | Jfeスチール株式会社 | High strength steel plate for cans with excellent flange workability and manufacturing method thereof |
JP6019719B2 (en) * | 2012-05-02 | 2016-11-02 | Jfeスチール株式会社 | Manufacturing method of high strength and high ductility steel sheet |
JP5874771B2 (en) * | 2013-03-28 | 2016-03-02 | Jfeスチール株式会社 | Steel plate for cans excellent in workability and rough skin resistance and method for producing the same |
CN106605006B (en) * | 2014-08-29 | 2018-11-06 | 杰富意钢铁株式会社 | Steel plate for tanks and its manufacturing method |
JP5958630B2 (en) | 2014-10-10 | 2016-08-02 | Jfeスチール株式会社 | Crown steel plate and manufacturing method thereof |
KR101918426B1 (en) * | 2014-11-12 | 2018-11-13 | 제이에프이 스틸 가부시키가이샤 | Steel sheet for cans and method for manufacturing steel sheet for cans |
MX2017006871A (en) * | 2014-11-28 | 2017-08-14 | Jfe Steel Corp | Steel sheet for crown cap, manufacturing method therefor, and crown cap. |
KR102026001B1 (en) | 2015-02-26 | 2019-09-26 | 제이에프이 스틸 가부시키가이샤 | Steel sheet for crown cap, method for manufacturing steel sheet for crown cap, and crown cap |
MY173780A (en) * | 2015-03-31 | 2020-02-20 | Jfe Steel Corp | Steel sheet for can and method for manufacturing the same |
MX2018010365A (en) * | 2016-02-29 | 2018-12-06 | Jfe Steel Corp | Steel sheet for cans and manufacturing method therefor. |
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JP5810714B2 (en) | 2015-11-11 |
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