EP0662523B1 - Stahlblech mit hoher spannungsrisskorrosionsbeständigkeit für die herstellung von dosen - Google Patents

Stahlblech mit hoher spannungsrisskorrosionsbeständigkeit für die herstellung von dosen Download PDF

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Publication number
EP0662523B1
EP0662523B1 EP94921814A EP94921814A EP0662523B1 EP 0662523 B1 EP0662523 B1 EP 0662523B1 EP 94921814 A EP94921814 A EP 94921814A EP 94921814 A EP94921814 A EP 94921814A EP 0662523 B1 EP0662523 B1 EP 0662523B1
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steel sheet
steel
stress corrosion
corrosion cracking
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French (fr)
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EP0662523A4 (de
EP0662523A1 (de
Inventor
Kuniaki Maruoka
Yoshikuni Furuno
Yasuhiko Yahata Seitetsusyo Yamashita
Masayuki Yahata Seitetsusyo Matsuda
Yasushige Yahata Seitetsusyo Yoshitomi
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Nippon Steel Corp
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Nippon Steel Corp
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Classifications

    • 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
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C21D8/0436—Cold rolling
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • 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

Definitions

  • the present invention relates to a thin steel sheet for a two-piece can and a thin steel sheet for a three-piece can, having high resistance to stress corrosion cracking, and a process for producing the same.
  • Steel sheets for cans such as a tinplate, which is a tinned steel sheet, or a tin-free steel sheet, which is a chromate-treated steel sheet, are used widely in food cans, aerosol cans, easy-open cans, and the like. These cans can be classified roughly into a two-piece can and a three-piece can.
  • the two-piece can comprises two components of a barrel integral with a bottom and of a cover.
  • the two-piece can By virtue of low can- making cost, there is an ever-increasing tendency for an increase in the proportion of the two-piece can to the whole cans.
  • forming under severe conditions such as multistage drawing or DWI (the abbreviation for drawing and wall ironing; that is, deep drawing followed by ironing), is carried out, requiring for the steel sheet used to have corrosion resistance as well as excellent formability.
  • DWI multistage drawing or DWI
  • a blank sheet in a disk form is punched from a steel strip by means of a cupping press.
  • the blank sheet is subjected to shallow drawing using a punch and a die to form a cup.
  • the cup is stretched by means of a DWI press while ironing the side wall of the cup using a punch and a die having a smaller clearance than the thickness of the side wall of the cup to reduce the thickness of the side wall, thereby forming a can body having a cup form having a desired depth.
  • This forming is called "DWI.”
  • the bottom of the can body is formed by a bottom former into a dome with the bottom being protruded inward.
  • ears are formed by a phenomenon called "earring" wherein the top end of the barrel after forming is waved in a circumferential direction due to the anisotropy of forming of the material.
  • the ear is trimmed with a trimmer to regulate the top end of the barrel.
  • the can body is then cleaned and dried, and printing and painting are carried out on the external surface of the can. Subsequently, the can is subjected to multistage necking wherein the opening diameter of the can body is reduced with a necker-flanger. Further, in order to provide a cover at the opening end of the can body, flanging is carried out wherein a flange radially extending toward the outside of the can is formed at the opening end.
  • Important properties required of steel sheets for a DWI can include DWI property, earring property, neck forming property, flange forming property, and, in the form of a can, additionally compressive strength and paneling strength.
  • the DWI property is a property which, in DWI, is less likely to cause abrasion of a mold and less likely to cause scoring of a mold and requires no large energy in the forming.
  • the earring property is a property which, in DWI, minimizes earring. Since the ear portion is cut out with a trimmer prior to necking, large earring lowers the yield of the material.
  • the neck forming property is a property which causes no wrinkle in multistage necking.
  • the flange forming property is a property which, in flanging, is less likely to cause cracking causative of leakage of the contents of the can into the flange portion, that is, a defect called "flange cracking.”
  • the compressive strength is a critical internal pressure of the can at which, after seaming of the cover, a buckling phenomenon occurs causing weak portions of the can body to be unfavorably protruded outward by internal pressure.
  • the can in its portions weak against the internal pressure are the bottom and cover of the can, and the compressive strength too is, in many cases, governed by the mechanical strength of the bottom and cover of the can.
  • the paneling strength is a critical external pressure at which, after seaming of the cover, the barrel of the can body is recessed inward by external pressure.
  • the strength against external force applied during handling of canned goods, such as packing, transport, unpacking, falling in a vending machine, and the like is represented by the paneling strength.
  • the three-piece can will now be described.
  • the three-piece can has advantages over the two-piece can, such as higher paneling strength, there is an ever-increasing tendency for an increase in the absolute quantity of the three-piece cans produced.
  • predetermined printing and coating of the internal surface are carried out on a steel sheet, and the printed and coated steel sheet is dried. It is then cut with a cutter into a square blank sheet having a desired size in two steps of cutting in the rolling direction and cutting normal to the rolling direction.
  • the square blank sheet is formed by means of a barrel making machine into a cylinder which is then subjected to joining by welding, bonding, soldering, or other methods to prepare a can barrel.
  • the diameter of the opening of the can body is reduced by multistage necking with a necker-flanger.
  • a flange radially extending toward the outside of the can body is formed at the opening end by flanging. Thereafter, one of a cover and a bottom is mounted on the flange portion by means of a double seamer.
  • the three-piece can can be classified into a welded can, a bonded can, and a soldered can according to the joining method.
  • the width of lapped portion in the joint leads to a lowering in yield of the material, resulting in a gradually increasing tendency for use of the welded can having the smallest width.
  • Important properties required of the steel sheet for a welded can include weldability, neck forming property, flange forming property, and paneling strength.
  • the weldability is a property that welding can be carried out in a broad current range, that is, the current range capable of providing satisfactory joint strength and causing no splash is broad.
  • the neck forming property, flange forming property, and paneling strength are as described above.
  • both the two-piece can and the three-piece can from the viewpoint of saving resources, there is an ever-increasing tendency for can manufacturers to demand a thinner steel sheet for a can to can steel sheet manufacturers.
  • a reduction in the sheet thickness however, unfavorably results in deteriorated earring property, neck forming property, and flange forming property and lowered can strength.
  • the supply of steel sheets, for cans which have a small thickness and can ensure desired earring property, neck forming property, flange forming property, and can strength, has become a large task to be performed.
  • Japanese Patent Application No. 132712/1992 Japanese Patent Laid-Open No. 345924/1993.
  • This invention relates to a technique where a steel sheet, for a two-piece can, having a small thickness and excellent earring property and DWI property and a very thin steel sheet, for a welded can, having an excellent flange forming property can be provided by combining proper regulation of chemical ingredients, particularly a reduction in C content to the extremity, and addition of Ti, Nb, or B with regulation of conditions for secondary cold rolling.
  • Stress corrosion cracking is a failure passing through the sheet in the thicknesswise direction, which failure is a serious defect leading to leakage of the contents of the can and inclusion of foreign materials from the outside of the can.
  • the cause of the stress corrosion cracking has not been fully elucidated yet, the stress corrosion cracking is generally said to occur by a combination of several unfavorable conditions in respect of stress in the steel sheet, shape of the can, can forming conditions, composition of the contents, hydrogen ion concentration (pH), and the like.
  • An object of the present invention is to solve the above problems of the prior art and to provide a steel sheet for a two-piece can and a steel sheet for a three-piece can, having a small thickness and high resistance to stress corrosion cracking, and a process for producing the same.
  • the steel sheet, for a can, having high resistance to stress corrosion cracking according to the present invention is characterized by comprising, by weight percent, C: not more than 0.0015%, Mn: 0.05 to 0.40%, P: not more than 0.06%, S: not more than 0.06%, sol. Al: not more than 0.10%, and N: not more than 0.0100% and
  • the present inventors have found that a close correlation exists between the sharpness of an electron channeling pattern of a steel sheet and the occurrence of stress corrosion cracking. Further, they have systematically investigated the correlation and conducted various experiments on the process for producing a steel sheet. As a result, the following facts were found.
  • the present invention has been made base on these novel findings.
  • ECP electron channeling patterns
  • ECP In the case of steel sheets produced on a commercial scale, sharp ECP is not always provided.
  • the space between three sets of parallel pseudo-Kikuchi lines in ECP and the coordinate of the center of a pallalelogram formed by intersection of these parallel lines are important to the study of crystal orientation.
  • the unsharpness of ECP is processed as a noise.
  • the present inventors have found that there is a correlation between the sharpness of ECP and the rate of occurrence of stress corrosion cracking and that a steel sheet, for a can, having a sharpness smaller than a given value has high resistance to stress corrosion cracking.
  • the sharpness can be quantified by several methods.
  • the present inventors quantified the sharpness by using, among these methods, a method described in an article entitled "ECP Gazo Kaiseki Ni Yoru Kessho Hizumi Sokutei Hoho (Crystal Strain Measuring Method Using ECP Image Analysis” (Journal of the Japan Institute of Metal, Vol. 55, No. 1 (1991) pp. 22-28).
  • the input of an image refers to average adding input of an ECP image from a scanning electron microscope into an image analyzer.
  • the density varying image processing refers to a processing involving a series of steps of (1) smoothing the input image with an intermediate-value filter, (2) conducting linear transformation so that the maximum value and the minimum value of the density level are the maximum value and the minimum value of the density level in an image analyzer, (3) conducting selective local averaging, (4) conducting two-dimensional differentiation with a Sobel filter, (5) conducting gamma transformation, log transformation, and again gamma transformation, and (6) finally smoothing again the object image plane with an intermediate-value filter.
  • the digitization refers to setting of a fixed threshold value with respect of the image after the density varying image processing followed by conversion to two values based on whether the value is larger or smaller than the set value.
  • the digital image processing refers to a processing involving a series of steps of (1) removing isolated points from the image after the digitization and conducting expansion and contraction processing, (2) conducting smoothing and then padding, and (3) conducting line width reduction processing by the Tamura's method (Shinzendaishi, Vol. 1539 (1974) p. 1390) and finally conducting again expansion processing.
  • the present inventors used Model TOSPIX-II for the image analysis.
  • the above image processing can be carried out using any image analyzer so far as the image analyzer has an image analyzing capability equal or superior to TOSP IX-II.
  • the sharpness S is a physical quantity for a steel sheet and does not depend upon the type of the image analyzer. Further, the scanning electron microscope need not be necessarily connected on-line with the image analyzer, and the data may be transferred through a medium such as a magnetic tape.
  • Sharp pseudo-Kikuchi lines are, in fact, nothing but all curves in the image after the above image processing. This is because unsharp pseudo-Kikuchi lines are removed in the course of the image processing. Whether or not the pseudo-Kikuchi line is sharp can be judged based on the threshold value in the digitization.
  • the present inventors used 50 as the threshold value.
  • the sum L of the lengths of sharp pseudo-Kikuchi lines within an ECP image plane is the sum of the lengths of all intermittent curves in the image after the above image processing. This quantity can be easily determined by means of a conventional image analyzer.
  • the width W of sharp pseudo-Kikuchi lines within an ECP image plane is a constant and can be easily determined again by a conventional image analyzer.
  • the area A of an ECP image plane is a constant independent of samples.
  • X-ray analysis provides information on average crystal orientation of a steel sheet, which is a polycrystalline material.
  • ECP uses a fine electron beam and, hence, has a feature that information on the crystal orientation of individual grains can be provided.
  • the sharpness S greatly depends upon the orientation of grain irradiated with an electron beam.
  • the orientation of grain however, has no direct correlation with the stress corrosion cracking. Therefore, in order to correlate the sharpness with the stress corrosion cracking, it is necessary to separate the contribution of the orientation from the sharpness.
  • the present inventors measured the sharpness for 20 or more grains located in a central portion of the sheet thickness and not less than 50 ⁇ m apart from one another and the arithmetic average of the measured values was determined as the average sharpness AS.
  • the expression "central portion of the sheet thickness” may be any portion which is located about 1/4 or less of the sheet thickness from the center of the sheet thickness toward the obverse or reverse surface. Since the steel sheet for a can is a polycrystalline material, the average sharpness AS is a quantity from which the influence of the orientation of individual grains has been removed, enabling the sharpness to be correlated with the stress corrosion cracking.
  • the relative average sharpness RAS is a value standardized by dividing the average sharpness AS of a material under test by the average sharpness AS of a standard sample free from work strain.
  • the relative average sharpness RAS is a physical quantity for a steel sheet and can be determined using a scanning electron microscope and an image analyzer by reference to the above article (Journal of the Japan Institute of Metal, Vol. 55, No. 1 (1991) pp. 22-28).
  • the relative average sharpness RAS shows a correlation with stress corrosion cracking.
  • the upper limit of the relative average sharpness RAS is limited to 0.85 because if this value exceeds 0.85 the stress corrosion cracking cannot be completely prevented.
  • the sample applied to the ECP measurement is polished from one surface to the central portion of the sheet thickness and finished by chemical polishing to bring the surface to be exposed to an electron beam to a specular state.
  • the C content exceeds 0.0015%, the stress corrosion cracking cannot be completely prevented.
  • the earring property, DWI property, and flange forming property are deteriorated in the case of a very thin steel sheet for a two-piece can, and the flange forming property is deteriorated in the case of a very thin steel sheet for a welded can.
  • the C content is limited to not more than 0.0015%.
  • the C content is preferably 0.0010% or less.
  • Mn should be present in an amount of not less than 0.05 % because when the Mn content is less than 0.05%, hot shortness occurs, making it impossible to prepare a steel sheet for a can.
  • Mn content exceeds 0.40%, the steel sheet is excessively hardened to deteriorate flange forming property and DWI property and, at the same time, the composition purification effect attained by reduction in C content is reduced, causing the earring property to be deteriorated. Further, the cost is increased. For this reason, the Mn content is limited to 0.05 to 0.40%.
  • P is an element that need not be intentionally added. Specifically, it is an unavoidable impurity element that significantly hardens the steel. When the P content exceeds 0.06%, the steel sheet is excessively hardened, deteriorating the flange forming property and the DWI property. In addition, the composition purification effect attained by reduction in C content is reduced, causing the earring property to be deteriorated. Further, the corrosion resistance is deteriorated. For this reason, the upper limit of the P content is 0.06%. In order to provide better flange forming property, DWI property, earring property, and corrosion resistance, it is preferred for the P content to be not more than 0.02%.
  • S is also an element that need not be intentionally added. Specifically, it is an unavoidable impurity element that increases the hot shortness. When the S content exceeds 0.06%, a sheet for a can cannot be produced due to hot shortness. For this reason, the upper limit of the S content is 0.06%.
  • the S content is still preferably not more than 0.02%.
  • Al is necessary as a deoxidizing element but need not be present as acid sol. Al. Further, when the relationship of Al with other steel ingredients is taken into consideration, the effect of the present invention is not lost when the acid sol. Al content is not more than 0.100%. When this content exceeds 0.100%, the Al 2 O 3 inclusions are increased, causing flange cracking at the time of can making and deterioration in DWI property. Further, the cost is increased. For this reason, the upper limit of the acid sol. Al content is 0.100%.
  • N is also an element that need not be intentionally added. It is an unavoidable impurity element that hardens the steel. When the N content exceeds 0.0100%, the steel sheet is excessively hardened to deteriorate the flange forming property and the DWI property. In addition, the composition purification effect attained by reduction in C content is reduced, causing the earring property to be deteriorated. For this reason, the upper limit of the N content is 0.0100%.
  • B The addition of B can further enhance the effect of the present invention.
  • the B content is lower than 0.0001%, the stress corrosion cracking is likely to occur.
  • the earring property, DWI property, and neck forming property are deteriorated.
  • the lower limit of the B content is preferably 0.0001%.
  • the upper limit of the B content is preferably 0.0060%.
  • Ti and Nb The addition of Ti and Nb can further enhance the effect of the present invention.
  • these elements are added in large amounts, the production of a very thin steel sheet, for a two-piece can, having an excellent earring property and a very thin steel sheet, for a welded can, having an excellent flange forming property can be facilitated. This, however, unfavorably makes it difficult to prevent stress corrosion cracking, increases the alloy cost, and raises the recrystallization temperature.
  • the present inventors have made detailed studies on the amounts of Ti and Nb added, while taking the relationship of these amounts with the other steel ingredients into consideration, which amounts can limit the increase in alloy cost and the rise in recrystallization temperature to a level acceptable from the viewpoint of industry and enable the production of a very thin steel sheet for a two-piece can, and a very thin steel sheet for a welded can, having high resistance to stress corrosion cracking.
  • the limitation of the C content to the content range specified above in combination with the regulation of the amounts of these elements Ti and Nb added to the following amount ranges determined by taking the relationship between these amounts with the N content into consideration is useful for the above purpose.
  • the upper limit of the Ti content is 0.06%.
  • Nb When the Nb content, in relation to the N content, is below 6.6 x ([wt% of N] - 0.0010)%, the earring property, DWI property, and neck forming property of the product are deteriorated. Therefore, the lower limit of the Nb content is 6.6 x ([wt% of N] - 0.0010)%. On the other hand, when the Nb content exceeds 0.06%, it becomes difficult to completely prevent the stress corrosion cracking. In addition, the recrystallization temperature is remarkably increased, and the alloy cost becomes excessively high. For this reason, the upper limit of the Nb content is 0.06%.
  • C in a solid solution form and N in a solid solution form should be present in respective given amounts or more.
  • the use of a simpler method is desired. According to the studies conducted by the present inventors, the above elements can be easily controlled by measuring the aging index without direct measurement of C in a solid solution form and N in a solid solution form.
  • aging index refers to a difference between a flow stress when a tensile prestrain of 10% is applied to a tensile specimen and a lower yield stress after the above specimen is further subjected to artificial aging under conditions of 100°C x one hr.
  • the aging index is below 15 MPa, it becomes difficult to completely prevent the stress corrosion cracking. Therefore, the lower limit of the aging index is limited to 15 MPa.
  • a steel produced by a conventional melt process is subjected to continuous casting or ingot making and slabbing to prepare a hot slab which is then hot-rolled.
  • the slab Prior to hot rolling, the slab may be heat-treated by any method commonly used in the art. Specifically, the hot slab may be directly hot-rolled or alternatively may be reheated in a heating furnace.
  • a hot rolling finishing temperature of 810°C or above should be ensured. Therefore, the reheating cannot be carried out at such an excessively low reheating temperature as will make it impossible to ensure the finishing temperature in the hot rolling operation.
  • the reheating temperature is preferably 1000°C or above.
  • the lower limit of the final sheet thickness in hot rolling is 2.0 mm.
  • the studies conducted by the present inventors have revealed that the time taken from the emergence of a hot-rolled steel strip from a finishing final stand to the initiation of cooling of the hot-rolled steel strip on a run-out table (cooling initiation time) and the temperature at which the cooling is initiated (cooling initiation temperature) have an effect on the flange forming property and the relative average sharpness of ECP of the product steel sheet.
  • cooling initiation time When the time taken from the emergence of a hot-rolled steel strip from a finishing final stand to the initiation of cooling of the hot-rolled steel strip on a run-out table (cooling initiation time) exceeds 1.5 sec, the flange forming property of the product steel sheet is deteriorated and, at the same time, the relative average sharpness of ECP becomes large. Therefore, this cooling initiation time should be limited to not more than 1.5 sec.
  • the cooling initiation temperature When the cooling initiation temperature is below [finishing temperature - 30]°C, the flange forming property of the product steel sheet is deteriorated and, at the same time, the relative average sharpness of ECP becomes large. Therefore, the cooling initiation temperature should be limited to [finishing temperature - 30]°C or above. Although the reason why these phenomena occur has not been fully elucidated yet, it is considered that a reduction in size of grains of the hot-rolled steel strip by the above limitations is involved in the above phenomena.
  • the coiling temperature of the hot-rolled steel strip when the coiling temperature is above 720°C, the amount of scale of the hot-rolled steel strip formed becomes excessively large, deteriorating the efficiency of the step of pickling. For this reason, the coiling temperature is preferably 720°C or below.
  • the steel strip After the completion of the hot rolling, the steel strip is subjected to a series of steps of pickling, cold rolling, and recrystallization annealing by conventional methods.
  • the cold-rolled material is subjected to secondary cold rolling.
  • the reduction ratio (r) in secondary cold rolling is less than 0.7%, the stress corrosion cracking is likely to occur and, at the same time, the can strength becomes unsatisfactory. Therefore, the lower limit of the reduction ratio is 0.7%.
  • the reduction ratio exceeds 60% the steel sheet is excessively hardened, causing the flange forming property and the DWI property to be deteriorated. For this reason, the upper limit of the reduction ratio is 60%.
  • the surface of the steel sheet of the present invention may be covered or coated by any method. Specifically, a good effect can be attained by applying any surface covering or coating commonly used in a steel sheet for a two-piece can and a steel sheet for a welded can, for example, plating such as tinning, nickel plating, and special substrate treatment followed by tinning at a very small coverage, or the application of a polymeric organic film.
  • the can When the steel of the present invention is applied to a two-piece can, the can may be manufactured by any of DWI and multistage drawing.
  • the can When the steel of the present invention is applied to a three-piece can, the can can be manufactured without limitation of blanking direction, that is, by any of a normal method (a method wherein blanking is carried out so that the rolling direction of the steel sheet is normal to the axial direction of the can barrel), a reverse method (a method wherein blanking is carried out so that the rolling direction of the steel sheet is parallel to the axial direction of the can barrel), and a method wherein the above blanking methods are combined. Further, the effect of the present invention can be attained also when the steel of the present invention is applied to a cemented can.
  • Steels comprising chemical ingredients specified in Table 1 were prepared by the melt process in a converter, and slabs of these steels were cooled to room temperature, reheated to a slab reheating temperature in the range of from 1000 to 1290°C and hot-rolled at a finishing temperature in the range of from 800 to 950°C to a thickness of 3.0 mm.
  • the resultant hot-rolled steel strips 0.4 to 1.9 sec after the emergence from a finishing final stand, were started to be cooled on a run-out table, coiled, pickled, cold-rolled, continuously annealed, subjected to secondary cold rolling to a thickness of 0.17 mm, and finally plated with tin in a very small thickness.
  • the aging index, relative average sharpness in ECP, resistance to stress corrosion cracking, flange forming property, earring property, and paneling strength of the very thinly tinned steel sheets thus obtained are given in Table 2.
  • sample Nos. 1 to 6 fall within the scope of the present invention
  • sample Nos. 7 to 10 are comparative examples which are outside the scope of the present invention.
  • the chemical ingredients C and Ti, the aging index, and the relative average sharpness are outside the scope of the present invention.
  • the sharpness is outside the scope of the present invention although the chemical ingredients fall within the scope of the present invention.
  • the sharpness is outside the scope of the present invention.
  • sample No. 10 the chemical ingredient Ti and the aging index are outside the scope of the present invention.
  • the resistance to stress corrosion cracking was evaluated in terms of the ratio E 1 /E 0 wherein E 0 represents the elongation at break as measured by pulling a tensile specimen in the atmosphere at room temperature at a strain rate of 10 -6 s -1 and E 1 represents the elongation at break as measured by pulling the specimen taken from used in the measurement of E 0 in a corrosion accelerating solution at the same strain rate at 80°C.
  • E 1 represents the resistance to stress corrosion cracking as "acceptable,” while when it was less than 0.90, the resistance to stress corrosion cracking was evaluated as "unacceptable.”
  • the flange forming property was evaluated in terms of the degree of forming to failure in a simulation of flanging of a welded can by means of a flange forming machine. When the degree of forming was not less than 9.0%, the flange forming property was evaluated as "acceptable,” while when the degree of forming was less than 9.0%, the flange forming property was evaluated as "unacceptable.”
  • the earring property was evaluated in terms of a percentage of a value determined by molding a cup using a drawer and dividing a difference between the average height of crests and the average height of roots of the earring by the average height of the roots. When the degree of earring was not more than 3.5%, the earring property was evaluated as "acceptable,” while when it exceeded 3.5%, the earring property was evaluated as "unacceptable.”
  • the paneling strength was evaluated as follows. A barrel of a can was first prepared by means of a wire seam welder, and a rubber liner was pressed against both ends of the barrel to temporarily seal the can. Then, the air within the can was gradually discharged by means of a vacuum pump to measure the difference between the external pressure and the internal pressure at a moment of the occurrence of paneling (depression of the barrel of the can by the external pressure). When the paneling strength was not less than 2.20 kg/cm 2 , the paneling strength was evaluated as "acceptable,” while when it was less than 2.20 kg/cm 2 , the paneling strength was evaluated as "unacceptable.”
  • the aging index, relative average sharpness in ECP, resistance to stress corrosion cracking, flange forming property, earring property, and compressive strength of the tinned steel sheets thus obtained are also given in Table 4.
  • sample Nos. 11 to 18 the chemical composition falls within the scope of the present invention, and sample Nos. 19 to 22 are comparative examples which are outside the scope of the present invention.
  • the chemical ingredients C and Ti are outside the scope of the present invention; for sample No. 20, the chemical ingredients C, S, and N are outside the scope of the present invention; for sample No. 21, the chemical ingredients Mn, P, and sol. Al are outside the scope of the present invention; and for sample No. 22, the chemical ingredient Ti is outside the scope of the present invention.
  • sample Nos. 19 to 22 production conditions are also outside the scope of the present invention.
  • the aging index is outside the scope of the present invention.
  • the cooling initiation time, cooling initiation temperature, average strain rate, aging index, and relative average sharpness are outside the scope of the present invention;
  • the hot rolling finishing temperature, average strain rate, secondary cold rolling reduction ratio, and sharpness are outside the scope of the present invention;
  • the average strain rate, secondary cold rolling reduction ratio, aging index, and sharpness are outside the scope of the present invention.
  • the flange forming property was evaluated in terms of the degree of forming to failure in a test wherein, after an open end of a DWI can body is trimmed, the diameter of the open end is widened while inserting a conical punch into the open end by means of a flanging tester.
  • the degree of forming is not less than 9.0%, the flange forming property was evaluated as "acceptable,” while when the degree of forming is less than 9.0%, the degree of forming was evaluated as "unacceptable.”
  • the earring property was evaluated in the same manner as in Example 1.
  • the compressive strength was evaluated by preparing a can body of a steel sheet for a DWI can, subjecting the can body to heat treatment corresponding to drying of a coating in an atmosphere drier, sealing the opening of the can body with a rubber liner, and gradually introducing compressed air into the can body to determine a critical pressure which causes the can bottom to buckle.
  • the critical pressure was not less than 7.5 kgf/cm 2
  • the compressive strength was evaluated as "acceptable,” while when it was less than 7.5 kgf/cm 2 , the compressive strength was evaluated as "unacceptable.”
  • the present invention can be utilized in steel sheets for two-piece cans and steel sheets for three-piece cans, which steel sheets are thin, can ensure desired earring property, neck forming property, flange forming property, and can strength, and further have high resistance to stress corrosion cracking.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)

Claims (4)

  1. Stahlblech für eine Dose mit einer hohen Spannungsrißkorrosionsbeständigkeit, dadurch gekennzeichnet, daß es an Gewicht höchstens 0,0015 % C, 0,05 bis 0,40 % Mn, höchstens 0,06 % P, höchstens 0,06 % S, höchstens 0,10 % säurelöslicher Al und höchstens 0,0100 % N beinhaltet, wobei der Rest aus Eisen und unvermeidbaren Verunreinigungen besteht,
    wobei das Stahlblech einen Alterungsindex von mindestens 15 MPa und eine relative mittlere Schärfe von Elektronenkanalmustern von höchstens 0,85 aufweist, die an 20 oder mehr Körnern gemessen wurden, die sich in einem mittleren Abschnitt der Blechdicke und mindestens 50 µm voneinander entfernt befinden.
  2. Stahlblech für eine Dose mit einer hohen Spannungsrißkorrosionsbeständigkeit nach Anspruch 1, dadurch gekennzeichnet, daß es zusätzlich zu den in Anspruch 1 beschriebenen chemischen Inhaltsstoffen weiterhin mindestens 3,4 x ([Gew.-% von N] - 0,0010) % bis höchstens 0,06 % an Ti und mindestens 6,6 x ([Gew.-% von N] - 0,0010) % bis höchstens 0,06 % an Nb beinhaltet.
  3. Verfahren zur Herstellung eines Stahlblechs für eine Dose mit einer hohen Spannungsrißkorrosionsbeständigkeit, dadurch gekennzeichnet, daß es die folgenden Schritte aufweist:
    Warmwalzen einer heißen Stahlbramme, die an Gewicht höchstens 0,0015 % C, 0,05 bis 0,40 % Mn, höchstens 0,06 % P, höchstens 0,06 % S, höchstens 0,10 % säurelöslicher Al und höchstens 0,0100 % N beinhaltet, wobei der Rest aus Eisen und unvermeidbaren Verunreinigungen besteht, bei einer Endbearbeitungstemperatur von mindestens 810 °C bis zu einer Dicke von mindestens 2,0 mm, Wasserkühlen des sich ergebenden warmgewalzten Stahlstreifens auf einem Auslaufrollgang innerhalb von 1,5 s oder weniger nach dem Austreten aus einer Endbearbeitungsstation einer Warmwalzmaschine von einer Temperatur von mindestens [Endbearbeitungstemperatur - 30] °C, und Aufrollen, Beizen, Kaltwalzen und Rekristallisationsausglühen des abgekühlten Stahlbandes, und
    sekundäres Kaltwalzen mit einem Reduktionsverhältnis von 0,7 bis 60 % des ausgeglühten Stahlbandes, so daß die durch die folgende Gleichung (1) definierte mittlere Streckrate (SR) mindestens 12,4 s-1 beträgt,
    wodurch ein Stahlblech hergestellt wird, dessen Alterungsindex mindestens 15 MPa beträgt und bei dem die relative mittlere Schärfe eines Elektronenkanalmusters, welche an 20 oder mehr Körnern gemessen wird, die sich in einem mittleren Abschnitt der Blechdicke und mindestens 50 µm voneinander entfernt befinden, höchstens 0,85 beträgt: SR = 160r · 1000 · v R·t ln 11 - r wobei
    r: Reduktionsverhältnis (-),
    R: Radius der Arbeitswalze in mm,
    t: Blechdicke auf der Einlaßseite in mm und
    v: Umfangsgeschwindigkeit der Arbeitswalze in m/min.
  4. Verfahren zur Herstellung eines Stahlblechs für eine Dose mit einer hohen Spannungsrißkorrosionsbeständigkeit nach Anspruch 3, dadurch gekennzeichnet, daß der Stahl zusätzlich zu den in Anspruch 3 beschriebenen chemischen Inhaltsstoffen weiterhin mindestens 3,4 x ([Gew.-% von N] - 0,0010) % bis höchstens 0,06 % an Ti und mindestens 6,6 x ([Gew.-% von N] - 0,0010) % bis höchstens 0,06 % an Nb beinhaltet.
EP94921814A 1993-07-28 1994-07-26 Stahlblech mit hoher spannungsrisskorrosionsbeständigkeit für die herstellung von dosen Expired - Lifetime EP0662523B1 (de)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP18626793 1993-07-28
JP186267/93 1993-07-28
PCT/JP1994/001226 WO1995004166A1 (fr) 1993-07-28 1994-07-26 Tole d'acier pour boites de conserve a resistance elevee a la fissuration par corrosion sous contraintes, et son procede de fabrication

Publications (3)

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EP0662523A1 EP0662523A1 (de) 1995-07-12
EP0662523A4 EP0662523A4 (de) 1995-12-13
EP0662523B1 true EP0662523B1 (de) 1999-04-28

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EP (1) EP0662523B1 (de)
KR (1) KR0179419B1 (de)
CN (1) CN1043904C (de)
DE (1) DE69418172T2 (de)
WO (1) WO1995004166A1 (de)

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2739581B1 (fr) * 1995-10-06 1997-10-31 Lorraine Laminage Procede de fabrication d'une boite metallique du type boite boisson
DE10247998B4 (de) * 2002-10-15 2004-07-15 Thyssenkrupp Stahl Ag Verfahren zum Herstellen eines besonders gut verformbaren kaltgewalzten Stahlbands oder -blechs
CN100500912C (zh) * 2005-03-24 2009-06-17 杰富意钢铁株式会社 软质罐用钢板及其制造方法
CN101880821B (zh) * 2010-06-11 2012-08-15 武汉钢铁(集团)公司 抗拉强度为280MPa级的钢铝复合热轧钢及生产方法
US9315877B2 (en) 2010-12-06 2016-04-19 Nippon Steel & Sumitomo Metal Corporation Steel sheet for bottom covers of aerosol cans and method for producing same
CN103045937A (zh) * 2012-12-14 2013-04-17 宝山钢铁股份有限公司 一种二次冷轧钢及其制造方法
CA2916040C (en) * 2013-07-17 2019-02-12 Jfe Steel Corporation Steel sheet for can and method for manufacturing the same
MY174356A (en) * 2015-02-26 2020-04-09 Jfe Steel Corp Steel sheet for crown cap, method for manufacturing steel sheet for crown cap, and crown cap

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS6126756A (ja) * 1984-07-17 1986-02-06 Kawasaki Steel Corp 良化成処理性を有する極低炭素鋼板
JPS63203721A (ja) * 1987-02-18 1988-08-23 Kobe Steel Ltd 耐水素誘起割れ性及び耐応力腐食割れ性にすぐれる熱延鋼板の製造方法
JPH0711031B2 (ja) * 1988-06-01 1995-02-08 東洋鋼鈑株式会社 異方性の小さい硬質薄鋼板の製造方法
EP0421087B1 (de) * 1989-08-09 1994-11-30 KABUSHIKI KAISHA KOBE SEIKO SHO also known as Kobe Steel Ltd. Verfahren zur Herstellung eines Stahlbleches
JPH0747773B2 (ja) * 1990-03-30 1995-05-24 川崎製鉄株式会社 ３ピース缶の製造方法
JP3164853B2 (ja) * 1991-10-30 2001-05-14 川崎製鉄株式会社 食缶用薄鋼板の製造方法

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WO1995004166A1 (fr) 1995-02-09
CN1114113A (zh) 1995-12-27
KR950703660A (ko) 1995-09-20
DE69418172T2 (de) 1999-12-02
EP0662523A4 (de) 1995-12-13
CN1043904C (zh) 1999-06-30
DE69418172D1 (de) 1999-06-02
EP0662523A1 (de) 1995-07-12
KR0179419B1 (ko) 1999-02-18

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