US20090250147A1 - Dr Steel Sheet and Manufacturing Method Thereof - Google Patents

Dr Steel Sheet and Manufacturing Method Thereof Download PDF

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Publication number
US20090250147A1
US20090250147A1 US12/227,505 US22750507A US2009250147A1 US 20090250147 A1 US20090250147 A1 US 20090250147A1 US 22750507 A US22750507 A US 22750507A US 2009250147 A1 US2009250147 A1 US 2009250147A1
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equal
mass
less
steel sheet
rolling
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US12/227,505
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English (en)
Inventor
Hiroshi Nishida
Shigeru Hirano
Takahiro Aitoh
Seiichi Tanaka
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Nippon Steel Corp
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Individual
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Assigned to NIPPON STEEL CORPORATION reassignment NIPPON STEEL CORPORATION ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: AITOH, TAKAHIRO, HIRANO, SHIGERU, NISHIDA, HIROSHI, TANAKA, SEIICHI
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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
    • 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
    • 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
    • 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
    • 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
    • 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

Definitions

  • the present invention relates to a DR (Double Reduced) steel sheet for EOE (Easy Open End) which enables an easy-opening by hand of a portion of a can cover that is widely used for a drink can, a food can and the like, and to a manufacturing method thereof.
  • DR Double Reduced
  • EOE Easy Open End
  • a can cover having an easy-open function is being widely used for a metal can.
  • Such a can cover generally includes a partial-open type can cover that is mainly used for a drink can, and a full-open type can cover that is mainly used for a food can.
  • Both types of can covers generally employ an easy-open function in which an opening formed in a can cover panel is broken by pulling up a tab fixed by a rivet.
  • a body of an easy-open can cover are formed with a rivet and an opening guide groove, which are not provided on a can cover having no easy-open function.
  • the opening guide groove is formed to a depth of above 1 ⁇ 2 of thickness of a can cover plate by pressing a surface of the can cover with high load using a working tool having a knife-shaped projection formed in a predetermined opening contour.
  • the rivet is formed by a combined process of stretching and drawing.
  • the formed rivet is inserted in a hole provided in the tab, and then, a rivet mechanism is formed by performing a caulking process to a resultant structure.
  • a tine As a material for the aforementioned easy-open can cover, a tine, a surface-treated steel sheet, such as an electrolytic chromium coat steel sheet, and an aluminum steel sheet are used.
  • a coated material is used to protect contents in a can, although an uncoated tin may be used for, for example, a fruit can.
  • Patent Document 3 discloses a technique in which B oxide is used to realize achieving both of the can openability and the cover manufacturability.
  • the following Patent Document 3 states that: a starting point of a void in a steel sheet facilitates opening of a can; and rivet formability is not deteriorated by limiting a size of B oxide.
  • impurities such as oxide existing in steel may be a starting point of breakage due to working, Patent Document 3 does not present a substantial solution for this problem.
  • the above-mentioned suggestions have not been put into practical use since a thin hard material has cracks produced in a rivet forming process.
  • Patent Document 4 discloses a complex stretching process using bending and bending-back with three or more steps. The hard material has bee put into practical use in combination with such a multi-step complex stretching process.
  • Patent Document 1 Japanese Unexamined Patent Application, First Publication No. S63-109121
  • Patent Document 2 Japanese Unexamined Patent Application, First Publication No. S64-015326
  • Patent Document 3 Japanese Unexamined Patent Application, First Publication No. H10-251799
  • Patent Document 4 French Patent, Publication No. FR9004264
  • the use of the thin hard material is likely to produce cracks in stretching in the typical rivet forming process. It could be estimated that this is due to insufficient material stretchability.
  • the rivet forming process including the complex stretching using the multi-step bending and bending-back was required. It is believed that the multi-step bending and bending-back gives the effect of increasing a limitative drawing ratio and stretching a material by the bending and bending-back, and thereby enabling the rivet forming.
  • the present invention was made in view of the above-mentioned circumstances and has an object of providing a DR steel sheet with excellent rivet workability which enables EOE working even with the conventional production facility used for a two step rivet forming process, and a manufacturing method of the DR steel sheet at low costs.
  • the present invention provides a DR steel sheet and a manufacturing method thereof, which are inexpensive and are capable of restricting an average Lankford value after an aging process by limiting a steel component and securing total stretchability in a rolling direction and a sheet width direction after the aging process.
  • the gist of the present invention is as follows.
  • a DR steel sheet of the present invention includes the following steel components: C: 0.02 to 0.06 mass %, Si: equal to or less than 0.03 mass %, Mn: 0.05 to 0.5 mass %, P: equal to or less than 0.02 mass %, S: equal to or less than 0.02 mass %, Al: 0.02 to 0.10 mass %, and N: 0.008 to 0.015 mass %.
  • the amount of solute N (Ntotal ⁇ NasAlN) in the steel sheet containing a residual iron and inevitable impurities, is equal to or more than 0.006%; and the total stretchability in a rolling direction after aging is equal to or more than 10%, total stretchability in a sheet width direction after aging is equal to or more than 5%, and an average Lankford value after aging is equal to or less than 1.0.
  • a manufacturing method of a DR steel sheet of the present invention including the following steel components: C: 0.02 to 0.06 mass %, Si: equal to or less than 0.03 mass %, Mn: 0.05 to 0.5 mass %, P: equal to or less than 0.02 mass %, S: equal to or less than 0.02 mass %, Al: 0.02 to 0.10 mass %, and N: 0.008 to 0.015 mass %, wherein: the amount of solute N (Ntotal ⁇ NasAlN) in the steel sheet containing a residual iron and inevitable impurities, is equal to or more than 0.006%; and the total stretchability in a rolling direction after aging is equal to or more than 10%, total stretchability in a sheet width direction after aging is equal to or more than 5%, and an average Lankford value after aging is equal to or less than 1.0.
  • the manufacturing method includes: heating a steel work piece at equal to or more than 1200° C., and then hot-rolling the steel work piece at a finishing temperature of equal to or more than an Ar3 transformation point; forming a winding hot-rolled steel sheet at a winding temperature of equal to or less than 600° C.; subjecting a cold rolling to the wind hot-rolled steel sheet with a rolling rate of equal to or more than 80% after acid washing; subjecting annealing to the cold-rolled steel sheet at a temperature of equal to or more than a recrystallization temperature and equal to or less than an Ac1 transformation point; and subjecting DR rolling to the annealed steel sheet with a tempering rolling rate of 6% to 15%.
  • the DR steel sheet of the present invention enables a rivet forming process in two steps by: improving the steel components and the manufacturing method thereof; and specifying the total stretchability in the rolling direction and in the rolling sheet width direction after aging, and specifying the Lankford value after stretching after aging.
  • FIG. 1 is a sectional view after a first step of rivet forming.
  • FIG. 2 is a sectional view after a second step of rivet forming.
  • FIG. 3 is a sectional view after rivet caulking, where the reference symbol t denotes a tab while the reference symbol d represents a rivet diameter.
  • FIG. 4 is a graph showing a relationship between a solute N and a Lankford value.
  • the present invention relates to a DR steel sheet and a manufacturing method thereof, which are inexpensive and are capable of restricting an average Lankford value after an aging process by limiting steel components and securing the total stretchability in a rolling direction and a sheet width direction after the aging process.
  • FIG. 1 shows a sectional view after stretching at a first step
  • FIG. 2 shows a sectional view after rivet forming by drawing at a second step
  • FIG. 3 shows a sectional view of a rivet mechanism obtained by the caulking.
  • the rivet forming requires a characteristic that follows processing.
  • the inventors have found that the total stretchability of equal to or more than 10% in a rolling direction after an aging process and stretchability of equal to or more than 5% in a sheet width direction after the aging process follow the rivet forming smoothly.
  • the reason why it could follow the rivet forming is unclear in spite of the smaller total stretchability in the rolling direction comparing to the total stretchability in the sheet direction.
  • drawing included in the rivet forming has an effect on a Lankford value. In other words, it is known that the Lankford value in the sheet width direction increases over that in the rolling direction in a steel sheet having the Lankford value of less than 1.0.
  • processing in the sheet width direction may have the same possibility as working in the rolling direction as total stretchability interacts with the Lankford value complementarily.
  • the total stretchability in the rolling direction after the aging process is less than 10% or the total stretchability in the sheet width direction after the aging process is less than 5%, a material will be broken at the time of stretching at a first step or drawing at a second step.
  • a rivet diameter is important in caulking with a tab. If the rivet diameter is small, the tab may be detached.
  • the inventors have found that a steel sheet with a caulked tab is different in an average Lankford value after an aging process from a steel sheet with a detached tab. If the average Lankford value exceeds 1.0, the rivet diameter becomes small. On the contrary, if the average Lankford value is equal to or less than 1.0, the rivet diameter becomes large and the tab is not detached.
  • an aging process which is generally carried out at 180 to 220° C. (200 to 210° C.) for 7 to 30 minutes, is carried out at 210° C. for 30 minutes in an evaluation test.
  • the important thing is to provide a method of achieving the aforementioned material property in a continuous annealing DR steel sheet which can be inexpensively manufactured using a thin steel sheet material.
  • components of the DR steel and a manufacturing method thereof will be described.
  • C is one of factors that dominate crystalline grain growth. As the addition amount of C decreases, coarsening of crystalline grains of a hot rolling steel sheet and grain growth in annealing are accelerated, thereby raising the average Lankford value (r value) of the steel sheet. Accordingly, the lower limit of the amount of C needs to be less than 0.02% in order to make an r value equal to or less than 1.0. On the other hand, as the amount of C increases, the crystalline grains become refined and much cementite is extracted from steel. The refined grains and the extracted cementite, which are the starting point of void generation in a tensile test, facilitate propagation of cracks, thereby making the total stretchability of a product sheet small. Accordingly, the upper limit of the amount of C is set to be 0.06%.
  • the addition amount of Si is small.
  • the upper limit of the amount of Si is set to be 0.03%. In case of need for excellent abrasion-resistance, it is preferable to set the upper limit of the amount of Si to be equal to or less than 0.02%.
  • Mn is an element useful for preventing red brittleness in a hot rolling with S fixed. To achieve this effect, Mn is necessarily added by double or more of the addition amount of S. Accordingly, when the addition amount of S is equal to or less than 0.02%, the lower limit of the amount of Mn has to be less than 0.05%. On the other hand, crystalline grains are apt to be granulized in a steel sheet that contains a quantity of Mn, which may result in hardness and deterioration of stretchability. In addition, since Mn is enriched on a surface of a steel sheet by a heat treatment, which may result in deterioration of abrasion-resistance, the upper limit of the amount of Mn is set to be 0.5%.
  • P makes a steel sheet hard to thereby deteriorate the total stretchability and abrasion-resistance.
  • the amount of P exceeds 0.02%, segregation of crystalline grains is remarkable, which may result in brittleness of a steel sheet and difficulty in obtaining the required total stretchability. Accordingly, the upper limit of the amount of P is set to be 0.02%.
  • S exists as an intervenient and is a useless element causing deterioration of the total stretchability and abrasion-resistance. Accordingly, the less amount of S is more preferable. However, since S is an element to be inevitably mixed in a refining process and since no practical problem occurs if S is small in amount, the upper limit of the amount of S is set to be 0.02%.
  • Al is an element which is required as a deoxidizer in producing a solution and is preferably used to increase purity of a steel sheet. Accordingly, the addition amount of Al has to be sufficient to exclude oxygen from steel. If the amount of Al is small, deoxidization is insufficient, which may result in increase of an intervenient in steel and hence deterioration of total stretchability like cementite. Accordingly, the lower limit of the amount of Al is set to be 0.02%. On the other hand, if the amount of Al is large, excessive Al after deoxidization is combined with N in steel to be AlN extract, which may decrease the total stretchability and cause surface defects due to alumina cluster or the like. Accordingly, the upper limit of the amount of Al is set to be 0.10%.
  • N is the most important factor in manufacturing a steel sheet and exerts the effect of the present invention by acting on the steel sheet as solute N.
  • N is a solid solution-reinforced element, which is superior to P, and does not deteriorate abrasion-resistance unlike P.
  • N reduces the average Lankford value of a product sheet by acting on an aggregate important in the present invention.
  • the upper limit of the amount of N is set to be 0.015%, but in consideration of material stability and good yield in a series of manufacturing processes, it is preferable that the upper limit of the amount of N is set to be 0.010%.
  • the EOE DR steel sheet contains the following components: C: 0.02 to 0.06 mass %, Si: equal to or less than 0.03 mass %, Mn: 0.05 to 0.5 mass %, P: less than 0.02 mass %, S: equal to or less than 0.02 mass %, Al: 0.02 to 0.10 mass %, and N: 0.008 to 0.015 mass %.
  • the steel sheet may contain elements commonly existing in a known DR steel sheet for a welded can.
  • the steel sheet may contain the following components: Cr; equal to or less than 0.10 mass %, Cu: equal to or less than 0.20 mass %, Ni: equal to or less than 0.15 mass %, Mo: equal to or less than 0.05 mass %, B: less than 0.0020 mass %, one or two or more of Ti, Nb, Zr, V and so on: less than 0.3 mass %, Ca: equal to or less than 0.01 mass %, and the like, depending on its purpose.
  • a steel work piece as a rolling material is not particularly limited, but is preferably obtained using a continuous casting method in order to minimize macro segregation. Since the continuous work piece does not always need cooling before being hot-rolled, the continuous steel work piece is preferably cast, hot-rolled and directly inserted into a heating furnace. This is for preventing available solute N from decreasing due to cooling of the steel work piece. Although a detailed mechanism is unclear, it is proved that if a steel work piece is cooled and re-heated, the amount of solute N decreases in accordance with decreasing temperature. Accordingly, when a cooled steel work piece is re-heated, it is preferable to apply heating temperature of the process capability upper limit to close to situation of a casting process. In the present invention, it is necessary to re-heat the cooled steel work piece with heating temperature of at least equal to or more than 1200° C.
  • Finishing hot rolling is carried out with temperature of the steel work piece keeping at above an Ar3 transformation point.
  • By performing rolling process at above the transformation point enables obtaining a uniform and fine hot rolling structure.
  • the AlN extraction is reduced by forcedly water-cooling the steel work piece.
  • the cooling after the finishing hot rolling is carried out as quickly as possible, and winding temperature is set to be equal to or less than 600° C.
  • winding temperature is set to be equal to or less than 600° C. The reason for this is that the solute Al not used for deoxidization in steel is likely to combine with N in a temperature range from a point immediately before an Ar3 transformation point to a point exceeding 600° C., and it is very preferable that the steel sheet passes through this temperature range in a short time to prevent the solute N from being reduced due to increased generation of AlN.
  • the hot-rolled steel sheet obtained as above is subjected to a descaling step using acid washing, and then to a cold rolling step. If a cold rolling rate is less than 80%, the average Lankford value may exceed 1.0 due to remarkable grain growth in a continuous annealing step. Accordingly, the cold rolling rate is preferably somewhat equal to or more than 80%, more preferably 80% to 95%.
  • a recrystallizing step after the cold rolling is carried out in an annealing furnace. If annealing temperature exceeds an Ac1 transformation point, the average Lankford value of a product plate exceeds 1.0 due to remarkable grain growth. Accordingly, the upper limit of the annealing temperature is set to be 700° C. On the other hand, a cold rolling structure remains at below recrystallization temperature, thereby making it impossible to secure total stretchability. Accordingly, the lower limit of the annealing temperature is set to be equal to or more than the recrystallization temperature.
  • a secondary cold rolling after the annealing is a important factor in manufacturing the steel sheet of the present invention, next to the solute N.
  • a reduction rate of 6% to 15% is applied to the continuous annealed steel sheet including the solute N of equal to or more than 0.006% of the present invention. This condition allows suppression of deterioration of the total stretchability due to work strengthening and secure of anisotropy of stretchability of a steel sheet, that is, secure of stretchability of equal to or more than 10% in a rolling direction and equal to or more than 5% in a sheet width direction.
  • the solute N in steel is equal to or more than 0.006%, there is a possibility in that it acts on the density and the movement of dislocations generated by rolling, thereby preventing forming cells.
  • the lower limit of the optimal reduction rate is 6%. In rolling at less than this lower limit of the optimal reduction rate, a stable property of rolling is lost while the total stretchability increases, thereby making it impossible to secure steel sheet flatness required for coating and continuous manufacture of can covers.
  • the reduction rate exceeds 15%, anisotropy of stretchability of the steel sheet increases to turn the dislocations into cells, thereby making the stretchability in the sheet width direction less than 5%. Accordingly, the upper limit of the reduction rate has to be 15%.
  • Sheet thickness of the final product is not particularly limited.
  • the upper limit of the sheet thickness is preferably 0.20 mm in consideration of the costs of a can body after manufacture of a can. If the sheet thickness is less than 0.14 mm, the workability and the strength of a can cover are likely to be insufficient. Accordingly, the practical lower limit of the sheet thickness is preferably 0.14 mm.
  • a surface treatment for the steel sheet is not particularly limited as long as it can be applied to a steel sheet for typical cans.
  • a surface treatment may be carried out for the steel sheet using a tin plating, a chromium plating, a nickel plating, combinations thereof, or the like.
  • the present invention is also applicable to a precoating steel sheet manufactured by attaching a coat or an organic resin film to any of the aforementioned plated steel sheet.
  • Table 1 shows components, properties, and rivet workability of steel sheets
  • Table 2 shows manufacture conditions, properties, and rivet workability of steel sheets.
  • the manufacturing conditions for the steel materials shown in Table 1 are as follows; heating temperature of a steel work piece: 1211° C. to 1248° C., finishing temperature of hot rolling: 851° C. to 896° C., winding temperature: 546° C. to 599° C., cold rolling rate: 88.2% to 92.6%, continuous annealing temperature: 642° C. to 686° C., tempering rolling rate: 6% to 15%, and product sheet thickness: 0.160 mm to 0.200 mm.
  • Example 2 The steel materials shown in Table 2 are manufactured using the same steel work pieces as Example 2 shown in Table 1.
  • the obtained Ar3 transformation point of the Example 2 is 834° C.
  • Comparative Examples 23 to 28 are SR (Single Reduce) materials, other comparative examples and examples are DR steel sheets having product sheet thickness of 0.168 mm to 0.200 mm. Surfaces of these steel sheets are subjected to an electrolytic chromium process or a Sn plating process and then a chemical treatment. Subsequently, outer and inner surfaces are in turn coated (at dry film thickness of 10 ⁇ m) and then baked (at 190° C. for 10 minutes).
  • FIG. 4 is a graph showing the relationship between the solute N and the Lankford value.
  • the DR steel sheet of the present invention enables a rivet forming process in two steps by improving the component composition and the manufacturing method, that ism by specifying the stretching in rolling direction and in the width direction after aging, and the Lankford value after aging.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
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US12/227,505 2006-08-11 2007-08-09 Dr Steel Sheet and Manufacturing Method Thereof Abandoned US20090250147A1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP2006-219066 2006-08-11
JP2006219066 2006-08-11
PCT/JP2007/065590 WO2008018531A1 (fr) 2006-08-11 2007-08-09 Tôle d'acier pour emboutissage et procédé de fabrication de celle-ci

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US (1) US20090250147A1 (ja)
EP (1) EP2050834A4 (ja)
JP (1) JP5047970B2 (ja)
KR (1) KR20090007796A (ja)
CN (1) CN101454470A (ja)
TW (1) TW200827460A (ja)
WO (1) WO2008018531A1 (ja)

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US9943894B2 (en) * 2011-07-20 2018-04-17 Salzgitter Flachstahl Gmbh Method for producing a component by hot forming a pre-product made of steel
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JP6838685B1 (ja) * 2019-07-18 2021-03-03 Ｊｆｅスチール株式会社 箱型焼鈍ｄｒ鋼板およびその製造方法
JP7131596B2 (ja) * 2019-12-04 2022-09-06 Ｊｆｅスチール株式会社 高強度缶用鋼板およびその製造方法

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