EP1088905A1 - Very thin 2-piece container steel sheet excellent in pucker resistance at neck diameter reduction and in earing and production method therefor - Google Patents

Very thin 2-piece container steel sheet excellent in pucker resistance at neck diameter reduction and in earing and production method therefor Download PDF

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Publication number
EP1088905A1
EP1088905A1 EP00915519A EP00915519A EP1088905A1 EP 1088905 A1 EP1088905 A1 EP 1088905A1 EP 00915519 A EP00915519 A EP 00915519A EP 00915519 A EP00915519 A EP 00915519A EP 1088905 A1 EP1088905 A1 EP 1088905A1
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diameter
aln
steel sheet
mns
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German (de)
French (fr)
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EP1088905A4 (en
EP1088905B1 (en
EP1088905B2 (en
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Hidekuni Nippon Steel Corporation Murakami
Masayoshi Nippon Steel Corporation SUEHIRO
Seiichi Nippon Steel Corporation TANAKA
Tetsurou Nippon Steel Corporation TAKESHITA
Hirokazu Nippon Steel Corporation YOKOYA
Toru Nippon Steel Corporation CHICHIKI
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Nippon Steel Corp
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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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing
    • C21D8/0421—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing characterised by the working steps
    • C21D8/0436—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
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing
    • C21D8/0447—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing characterised by the heat treatment
    • C21D8/0468—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing characterised by the heat treatment between cold rolling steps
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • 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
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing
    • C21D8/041—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing involving a particular fabrication or treatment of ingot or slab
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing
    • C21D8/0421—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing characterised by the working steps
    • C21D8/0426—Hot rolling

Definitions

  • the present invention relates to a steel sheet used as a material for a can produced by drawing, ironing, stretching and succeeding diameter reduction forming as represented by the production of a two-piece can and a method for producing the steel sheet.
  • the present invention provides a steel sheet for an ultra-thin can, capable of being produced with high productivity, small earing and good neck wrinkling resistance and a method for producing the steel sheet.
  • two-piece cans In the field of manufacturing beverage cans and food cans, etc., the production amount of cans wherein bottoms and walls are integrally formed in one body, called two-piece cans, is increasing.
  • a two-piece can In a two-piece can, generally, in order to obtain a required can height, a method for increasing the can wall height by ironing or stretching after drawing process is adopted, as is represented by a method for manufacturing a DI can or a DTR can.
  • the present invention provides a steel sheet used for a two-piece can produced by drawing and ironing or stretching, having high drawability and avoiding
  • the anti-wrinkling property is improved, as crystal grain size becomes coarser, as the strength of ⁇ 100 ⁇ plane becomes higher and the strength of ⁇ 111 ⁇ plane becomes lower in crystalline texture, and as precipitates become coarser in size and lower in density.
  • the present invention has been completed by further considering the workability, etc. of a two-piece can annealed at a relatively low temperature for restraining heat-buckle during annealing process.
  • the inventors Based on the finding that the anti-wrinkling property is influenced by the amount and size of AlN and MnS, the inventors have further studied in detail and obtained the result that the anti-wrinkling property can be evaluated by restricting the ratio of N existing as Al nitrides to N content or the size distribution of AlN and MnS. That is, according to the present invention, a steel sheet for a two-piece can with a thickness of 0.19mm or less and having excellent neck wrinkling resistance and anti-earing property can be produced on condition that AlN and MnS satisfy the following requirements:
  • C forms cementite in steel when the content is high.
  • coarse cementite When coarse cementite is exposed on a surface, it may cause the deterioration of the plating properties of a steel sheet. Further, the coarse cementite could be a starting points cracks during ironing, stretching or flange forming in the process for manufacturing a can. It is desirable, therefore, that the upper limit of C content is set to 0.08%.
  • the properties can be markedly improved by setting the upper limit of C to 0.06% or less.
  • a reduction of the carbon content of less than 0.008% for controlling aging property it is not desirable from the aspect of insufficient can strength and the increase of decarburization cost because of the existence of C in solid solution. From these aspects, it is desirable to set C content to at least 0.008%. Further, to obtain a soft material with high ductility desirable for a two-piece can at a low cost without using a vacuum degassing process, it is desirable to limit the C content within the range between 0.02 and 0.04%.
  • N is an important element that controls the formation of nitrides. Too much N generates many nitrides, and hence the object of the present invention is hard to achieve. It is desirable, therefore, the upper limit of N be set to 0.0040%. If N is reduced to 0.0020% or less by sufficiently applying a vacuum degassing treatment, it is further desirable because the amount of nitrides generated is decreased and hence the target properties are improved.
  • the Si content is set to 0.05% or less. Further, more desirably, it should be set to 0.029% or less.
  • the Mn content is set within the range between 0.04 and 0.4%. Further, more desirably, it should be set within the range between 0.15 and 0.25%.
  • the P content is set to 0.04% or less. Further, more desirably, it should be set to 0.010% or less.
  • the S content is set to 0.04% or less. Further, more desirably, it should be set to 0.020% or less.
  • Al is, like N, an important element that controls nitrides, which is an important requirement of the present invention. From this aspect, it is desirable that the Al content is set within the range between 0.02 and 0.10%. Further, more desirably, it should be set within the range between 0.050 and 0.080%.
  • the present invention mainly utilizes Al nitrides as precipitates and does not mainly utilize compounds of B, Ti and V, etc. Therefore, B, Ti and V, etc. are not added intentionally.
  • Nitrides are mainly composed of AlN and hence the following relation must be satisfied; (N existing as AlN)/(N content)> 0.5.
  • N existing as AlN is a value obtained by converting the total amount of AlN into the amount of N, wherein the amount of Al in residuals when a steel sheet is dissolved in an iodine alcohol solution is analyzed and that total amount is regarded as composing AlN.
  • the size distributions of AlN and MnS are important factors for improving neck wrinkling resistance.
  • the present invention is preferable that, for AlN, the ratio of the number of AlN with a diameter of 0.10 ⁇ m or less to the number of AlN with a diameter of at least 0.005 ⁇ m is 10% or less and the average diameter of AlN is 0.01 to 0.10 ⁇ m, and that, for MnS, the ratio of the number of MnS with a diameter of 0.03 ⁇ m or less to the number of MnS with a diameter of at least 0.005 ⁇ m is 50% or less and the average diameter of MnS is 0.03 to 0.40 ⁇ m.
  • the size distribution can also be obtained by photographing the visual field and carrying out image analysis, etc.
  • work hardening behavior of a material including the Bauschinger Effect
  • fine precipitates greatly influence the work hardening behavior of a material.
  • the quantitative and qualitative analyses of fine precipitates are not regarded as perfect even with the latest technologies and could cause large errors. Therefore, the present invention specifies the claims in relation to coarse precipitates in which measuring errors are expected to be reduced.
  • MnS of an elongated shape can occasionally be observed, and for MnS with anisotropic shape, the average of the longest diameter and the shortest diameter is defined as the diameter of the precipitate.
  • the heat history over the overall manufacturing processes is important.
  • the influence of slab heating temperature and coiling temperature is large, and therefore it is necessary to control the slab reheating temperature to within a predetermined range.
  • a slab reheating temperature is determined in combination with a coiling temperature (CT).
  • CT coiling temperature
  • a steel sheet according to the present invention can be obtained without specifying the coiling temperature.
  • the precipitation of MnS during slab heating proceeds by setting a slab reheating temperature at a low temperature of 1150°C or less, the amount of fine MnS, which precipitates with a temperature drop during hot-rolling, is reduced, and thus the same effect as the above-mentioned AlN can be obtained. Further, in this case, it is thought that the coiling temperature need not be specified because the precipitation of AlN is also promoted during slab heating.
  • Cold-rolling reduction ratio is in the range between 82 and 94%. The figure is defined considering the productivity in producing a thin steel sheet and the suppression of in-plane anisotropy from the aspect of material quality.
  • the productivity of hot rolling goes down and in-plane anisotropy increases because the thickness of a hot band is required to be thinner.
  • the cold-rolling reduction ratio is high, the burden on the cold-rolling process becomes heavy and in-plane anisotropy also increases.
  • Annealing temperature is in the range between the recrystallization temperature and 720°C. The reason is that securing recrystallization is necessary for obtaining good ductility and the deterioration of productivity in the annealing process is of concern at a temperature exceeding 720°C. Further, more desirably, the temperature should be in the range between 650 and 670°C.
  • re-cold-rolling reduction ratio (RCR) after annealing is in the range between 1 and 10%. This is because the effect of re-cold-rolling is obtained at a re-cold-rolling reduction ratio of at least 1%, while too high re-cold-rolling reduction ratio causes the deterioration of workability due to the hardening of a material. Further, more desirably, the re-cold-rolling reduction ratio is in the range between 1 and 2%.
  • the effect of the present invention does not disappear even if strengthening elements such as Si, Mn and P, etc. are added in a large quantities, instead of employing 2CR, to increase the strength of a steel sheet.
  • a steel sheet according to the present invention is also used as a substrate for a surface treated steel sheet.
  • the surface treatment does not hurt the effect of the present invention at all.
  • a steel sheet according to the present invention when it is used as a surface treated steel sheet for a can, is usually coated with tin or chromium (tin-free), etc. Further, a steel sheet according to the present invention is also used as a substrate for a laminated steel sheet, which is coated with organic film and has been in use recently, without hurting the effect of the present invention.
  • Cans with a thickness of 125 ⁇ m at the portion where neck-forming is to be performed were produced while maintaining the drawing ratio and ironing ratio constant and the same multi-stage diameter reduction as is applied to conventional actual can manufacturing was applied to the cans and neck wrinkling resistance was evaluated by the value of a critical diameter reduction ratio calculated by the following equation (2) as a threshold of generating wrinkle. Since the allowance of material quality in actual operation becomes larger as the critical diameter reduction ratio becomes higher, wrinkle generation can be suppressed.
  • Critical diameter reduction ratio (initial diameter - diameter at the time of wrinkle generation)/(initial diameter)
  • Heat-buckle was evaluated by the occurrence of heat-buckle when a steel sheet was processed in a continuous annealing line at the temperature of recrystallization temperature + 40°C.
  • Figure 1 shows the relationship between the size distribution of MnS and neck wrinkling resistance for steel sheets with 0.03% of C in weight percent. Steel sheets having MnS size distribution within the range specified by the present invention have good neck wrinkling resistance.
  • the effects of MnS size distribution are separately shown by each slab reheating temperature category. The neck diameter reduction property is improved when slab reheating temperature is 1250°C or less and coiling temperature is at least 690°C even though the size distribution of MnS is almost the same.
  • the rate of wrinkle generation during neck diameter reduction can be reduced. Further, since a steel according to the present invention shows good properties even with an annealing temperature lower than the temperature for a conventional steel, the generation of heat-buckle can be avoided and highly efficient production of a material for an ultra-thin can is made possible.

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Abstract

The present invention provides a steel sheet for a two-piece can characterized in that the equation, (N existing as AlN)/(N content)>0.5, is satisfied, the average diameter of AlN is in the range of 0.01 to 0.10µm, the ratio of the number of AlN with a diameter of 0.01µm or less to the number of AlN with a diameter of at least 0.005µm is 10% or less, the average diameter of MnS is in the range of 0.03 to 0.40µm, and the ratio of the number of MnS with a diameter of 0.03µm or less to the number of MnS with a diameter of at least 0.005µm is 50% or less. Further, by specifying chemical composition, slab reheating temperature and coiling temperature in hot rolling, and re-cold-rolling reduction ratio after annealing, a high yield of steel sheet and good can formability can be achieved, the wrinkle generation rate during neck diameter reduction after drawing, ironing and stretching can be reduced and, further, good properties can be obtained even processed at a low annealing temperature. Thus the production of a highly efficient steel sheet for a two-piece can capable of averting heat-buckle is made possible. Further, buckling generation at an annealing process, earing generation during cup forming and wrinkle generation during the diameter reduction of a can body opening can be avoided. And thus a steel sheet for a two-piece can with a thickness of 0.19mm or less can be provided.

Description

TECHNICAL FIELD
The present invention relates to a steel sheet used as a material for a can produced by drawing, ironing, stretching and succeeding diameter reduction forming as represented by the production of a two-piece can and a method for producing the steel sheet. In the field of can manufacturing, in particular, the present invention provides a steel sheet for an ultra-thin can, capable of being produced with high productivity, small earing and good neck wrinkling resistance and a method for producing the steel sheet.
BACKGROUND TECHNOLOGY
In the field of manufacturing beverage cans and food cans, etc., the production amount of cans wherein bottoms and walls are integrally formed in one body, called two-piece cans, is increasing. In a two-piece can, generally, in order to obtain a required can height, a method for increasing the can wall height by ironing or stretching after drawing process is adopted, as is represented by a method for manufacturing a DI can or a DTR can.
In these forming processes, it is desired to restrain the generation of earing which deteriorates the yield of a steel sheet and the formability in ironing or stretching. Further, working for reducing the diameter of a can opening (neck forming) is performed in order to reduce the size of a can lid and to decrease the material cost thereof. Then, in case of a two-piece can, there occurs a problem of increasing wrinkle formation (deterioration of neck wrinkling resistance) due to material hardening caused by drawing and ironing or stretching.
For improving these shortcomings, the technologies disclosed in Japanese Unexamined Published Patent Application Nos. 1-184252, 1-184229 and 2-141535, etc. have been proposed.
For improving anti-wrinkling property, in general, it is said to be effective to decrease the yield stress of a material (when a yield point is not observed, the stress at 0.2% strain). However, the technologies disclosed in the above-mentioned prior arts do not provide the sufficient softening of a material after drawing and ironing. Therefore, when an ultra-thin sheet with a thickness of 0.2mm or less is used as a material, the work hardening of the material or the deterioration of the neck wrinkling resistance, etc. is still concerned in the forming of a can which diameter reduction ratio is further increased as a recent trend. And thus further improvement of material properties is desired.
For steel sheets developed for cans until now, no effective means has been found to restrain wrinkle formation during the diameter reduction of the material after it is subjected to heavy forming such as ironing or stretching during forming the can body of a conventional two-piece can. For a thin steel sheet with a thickness of 0.2mm or less, buckling of the steel sheet, called heat-buckle, is generated during annealing and the production efficiency is decreased.
As a countermeasure against heat-buckle, a method for processing a steel sheet thicker than a target thickness during annealing, then cold rolling again (2CR), and obtaining the steel sheet with the target thickness has been commercialized. This is a favorable method from the aspect of securing can strength since strength degradation is compensated for with work hardening even when an ultra-low carbon IF steel, which is originally soft, is applied. However, this method markedly deteriorates neck wrinkling resistance because working by drawing, ironing and stretching is applied in addition to working by 2CR.
DISCLOSURE OF THE INVENTION
The present invention provides a steel sheet used for a two-piece can produced by drawing and ironing or stretching, having high drawability and avoiding
  • 1. the deterioration of productivity due to buckling at an annealing process,
  • 2. the generation of wrinkle during reducing the diameter of the opening of a can body, and
  • 3. the development of earing for an ultra-thin material with a thickness of 0.2mm or less produced at a high cold-rolling reduction ratio,
    • and a method for producing the steel sheet.
    During the course of a study to restrict wrinkle generation during neck diameter reduction after the processes of 2CR, drawing, ironing and stretching using a low carbon steel with about 0.03% of C having a low recrystallization temperature and good drawability as a base material, the present inventors found that there is a correlation between wrinkle generation and the amount and size of precipitates such as AlN and MnS, etc. The mechanism of the phenomena is not clear but it is thought that crystal grain size and crystalline texture formation, etc. after annealing, mainly affect, in combination, the behavior of work hardening of the material and hence neck wrinkling resistance is improved.
    In particular, because the direction of working is varied in a course of processing such as cold rolling after annealing, drawing, ironing, stretching and diameter reducing, it is thought that a factor like the so-called Bauschinger Effect could have an influence.
    The anti-wrinkling property is improved, as crystal grain size becomes coarser, as the strength of {100} plane becomes higher and the strength of {111} plane becomes lower in crystalline texture, and as precipitates become coarser in size and lower in density. The present invention has been completed by further considering the workability, etc. of a two-piece can annealed at a relatively low temperature for restraining heat-buckle during annealing process.
    Based on the finding that the anti-wrinkling property is influenced by the amount and size of AlN and MnS, the inventors have further studied in detail and obtained the result that the anti-wrinkling property can be evaluated by restricting the ratio of N existing as Al nitrides to N content or the size distribution of AlN and MnS. That is, according to the present invention, a steel sheet for a two-piece can with a thickness of 0.19mm or less and having excellent neck wrinkling resistance and anti-earing property can be produced on condition that AlN and MnS satisfy the following requirements:
  • 1. (N existing as AlN)/(N content)>0.5,
  • 2. the ratio of the number of AlN with a diameter of 0.01µm or less to the number of AlN with a diameter of at least 0.005µm is 10% or less (RA),
  • 3. the average diameter of AlN with a diameter of at least 0.005µm is 0.01 to 0.10µm (DA),
  • 4. the ratio of the number of MnS with a diameter of 0.03µm or less to the number of MnS with a diameter of at least 0.005µm is 50% or less (RM),
  • 5. the average diameter of MnS with a diameter of at least 0.005µm is 0.03 to 0.40µm (DM).
    • BRIEF DESCRIPTION OF THE DRAWING
  • Figure 1 is a graph showing the relationship between the average diameter of MnS, hot-rolling conditions (slab heating temperature and coiling temperature) and a critical diameter reduction ratio.
    • BEST MODES FOR CARRYING OUT THE INVENTION
    The present invention will be explained in detail hereafter.
    Firstly, the chemical compositions of the steel, hereafter in weight percent, will be explained.
    C forms cementite in steel when the content is high. When coarse cementite is exposed on a surface, it may cause the deterioration of the plating properties of a steel sheet. Further, the coarse cementite could be a starting points cracks during ironing, stretching or flange forming in the process for manufacturing a can. It is desirable, therefore, that the upper limit of C content is set to 0.08%.
    When a material with good ductility during ironing, stretching and flange forming is required, in particular, the properties can be markedly improved by setting the upper limit of C to 0.06% or less. However, a reduction of the carbon content of less than 0.008% for controlling aging property, it is not desirable from the aspect of insufficient can strength and the increase of decarburization cost because of the existence of C in solid solution. From these aspects, it is desirable to set C content to at least 0.008%. Further, to obtain a soft material with high ductility desirable for a two-piece can at a low cost without using a vacuum degassing process, it is desirable to limit the C content within the range between 0.02 and 0.04%.
    N is an important element that controls the formation of nitrides. Too much N generates many nitrides, and hence the object of the present invention is hard to achieve. It is desirable, therefore, the upper limit of N be set to 0.0040%. If N is reduced to 0.0020% or less by sufficiently applying a vacuum degassing treatment, it is further desirable because the amount of nitrides generated is decreased and hence the target properties are improved.
    Since a high Si content causes hardening of the material and deterioration of workability, it is desirable that the Si content is set to 0.05% or less. Further, more desirably, it should be set to 0.029% or less.
    Since a high Mn content causes hardening of the material and deterioration of workability and an excessive reduction of Mn leads to a high cost, it is desirable that the Mn content is set within the range between 0.04 and 0.4%. Further, more desirably, it should be set within the range between 0.15 and 0.25%.
    Since a high P content causes hardening of the material and deterioration of workability, it is desirable that the P content is set to 0.04% or less. Further, more desirably, it should be set to 0.010% or less.
    Since a high S content generates many MnS precipitates and causes hardening of the material and deterioration of workability, it is desirable that the S content is set to 0.04% or less. Further, more desirably, it should be set to 0.020% or less.
    Al is, like N, an important element that controls nitrides, which is an important requirement of the present invention. From this aspect, it is desirable that the Al content is set within the range between 0.02 and 0.10%. Further, more desirably, it should be set within the range between 0.050 and 0.080%.
    An important requirement of the present invention is to control the amount of nitrides. The present invention mainly utilizes Al nitrides as precipitates and does not mainly utilize compounds of B, Ti and V, etc. Therefore, B, Ti and V, etc. are not added intentionally.
    Nitrides are mainly composed of AlN and hence the following relation must be satisfied;
    (N existing as AlN)/(N content)> 0.5.
    Here, N existing as AlN (N as AlN) is a value obtained by converting the total amount of AlN into the amount of N, wherein the amount of Al in residuals when a steel sheet is dissolved in an iodine alcohol solution is analyzed and that total amount is regarded as composing AlN.
    The size distributions of AlN and MnS are important factors for improving neck wrinkling resistance. The present invention is preferable that, for AlN, the ratio of the number of AlN with a diameter of 0.10µm or less to the number of AlN with a diameter of at least 0.005µm is 10% or less and the average diameter of AlN is 0.01 to 0.10µm, and that, for MnS, the ratio of the number of MnS with a diameter of 0.03µm or less to the number of MnS with a diameter of at least 0.005µm is 50% or less and the average diameter of MnS is 0.03 to 0.40µm.
    These are the values obtained by observing replicas extracted from steel sheets by the SPEED method with an electron microscope and by measuring the diameter and number of precipitates within the visual field with possibly no maldistribution.
    As described above, by controlling precipitates, the crystal structure and the crystalline texture, etc. can be controlled and hence the neck wrinkling resistance of a thin sheet with a thickness of 0.19mm or less can be improved.
    The size distribution can also be obtained by photographing the visual field and carrying out image analysis, etc. As described above, to improve neck wrinkling resistance, work hardening behavior of a material, including the Bauschinger Effect, should be considered. It is generally thought that fine precipitates greatly influence the work hardening behavior of a material. However, the quantitative and qualitative analyses of fine precipitates are not regarded as perfect even with the latest technologies and could cause large errors. Therefore, the present invention specifies the claims in relation to coarse precipitates in which measuring errors are expected to be reduced.
    MnS of an elongated shape can occasionally be observed, and for MnS with anisotropic shape, the average of the longest diameter and the shortest diameter is defined as the diameter of the precipitate.
    For controlling nitrides and sulfides, the heat history over the overall manufacturing processes is important. In the heat history, the influence of slab heating temperature and coiling temperature is large, and therefore it is necessary to control the slab reheating temperature to within a predetermined range.
    A slab reheating temperature (SRT) is determined in combination with a coiling temperature (CT). When a slab reheating temperature is in the range between 1150 and 1250°C, the coiling temperature must be limited to the range between 690 and 750°C. The reason is not clear, but it is thought that changing the size distribution of AlN precipitates in a steel sheet by keeping it particularly within the temperature range specified above influences the work hardening behavior of a material after recrystallization at cold rolling. Generally speaking, it is thought that reducing the number of fine precipitates directly influences the work hardening behavior of a material, coarsens crystal grain size by promoting crystal grain growth during recrystallization at cold rolling and, in addition, restrains work hardening also through the change of crystal orientation (crystalline texture).
    When a slab reheating temperature is in the prescribed range between 1000 and 1150°C which is lower than the above case, a steel sheet according to the present invention can be obtained without specifying the coiling temperature. The reason is not clear, but it is thought that the precipitation of MnS during slab heating proceeds by setting a slab reheating temperature at a low temperature of 1150°C or less, the amount of fine MnS, which precipitates with a temperature drop during hot-rolling, is reduced, and thus the same effect as the above-mentioned AlN can be obtained. Further, in this case, it is thought that the coiling temperature need not be specified because the precipitation of AlN is also promoted during slab heating.
    Cold-rolling reduction ratio (CR) is in the range between 82 and 94%. The figure is defined considering the productivity in producing a thin steel sheet and the suppression of in-plane anisotropy from the aspect of material quality. When the cold-rolling reduction ratio is low, the productivity of hot rolling goes down and in-plane anisotropy increases because the thickness of a hot band is required to be thinner. On the other hand, when the cold-rolling reduction ratio is high, the burden on the cold-rolling process becomes heavy and in-plane anisotropy also increases.
    Annealing temperature (AT) is in the range between the recrystallization temperature and 720°C. The reason is that securing recrystallization is necessary for obtaining good ductility and the deterioration of productivity in the annealing process is of concern at a temperature exceeding 720°C. Further, more desirably, the temperature should be in the range between 650 and 670°C.
    It is desirable that re-cold-rolling reduction ratio (RCR) after annealing is in the range between 1 and 10%. This is because the effect of re-cold-rolling is obtained at a re-cold-rolling reduction ratio of at least 1%, while too high re-cold-rolling reduction ratio causes the deterioration of workability due to the hardening of a material. Further, more desirably, the re-cold-rolling reduction ratio is in the range between 1 and 2%.
    Further, the effect of the present invention does not disappear even if strengthening elements such as Si, Mn and P, etc. are added in a large quantities, instead of employing 2CR, to increase the strength of a steel sheet.
    Further, a steel sheet according to the present invention is also used as a substrate for a surface treated steel sheet. However, the surface treatment does not hurt the effect of the present invention at all.
    A steel sheet according to the present invention, when it is used as a surface treated steel sheet for a can, is usually coated with tin or chromium (tin-free), etc. Further, a steel sheet according to the present invention is also used as a substrate for a laminated steel sheet, which is coated with organic film and has been in use recently, without hurting the effect of the present invention.
    EXAMPLES
    Steel sheets with a thickness of 0.180mm were produced under the manufacturing conditions shown in Table 2 using steel materials with the chemical compositions shown in Table 1, and then the effect of the present invention was evaluated.
    Cups were formed by drawing in a predetermined condition, and the earing property was evaluated by the earing ratio calculated from the maximum and minimum values of cup wall height using the following equation (1); earing ratio = (maximum value - minimum value)/(minimum value)
    Cans with a thickness of 125µm at the portion where neck-forming is to be performed were produced while maintaining the drawing ratio and ironing ratio constant and the same multi-stage diameter reduction as is applied to conventional actual can manufacturing was applied to the cans and neck wrinkling resistance was evaluated by the value of a critical diameter reduction ratio calculated by the following equation (2) as a threshold of generating wrinkle. Since the allowance of material quality in actual operation becomes larger as the critical diameter reduction ratio becomes higher, wrinkle generation can be suppressed. Critical diameter reduction ratio = (initial diameter - diameter at the time of wrinkle generation)/(initial diameter)
    Heat-buckle was evaluated by the occurrence of heat-buckle when a steel sheet was processed in a continuous annealing line at the temperature of recrystallization temperature + 40°C.
    As is apparent from Table 2, steel sheets produced under conditions within the range specified by the present invention have excellent properties in all of anti-earing property, neck wrinkling resistance and heat-buckle resistance.
    (Chemical composition: wt%)
    Steel C Si Mn P S Al N
    a 0.021 0.02 0.24 0.007 0.009 0.066 0.0028
    b 0.035 0.01 0.07 0.008 0.009 0.059 0.0016
    c 0.035 0.03 0.24 0.015 0.009 0.014 0.0035
    d 0.064 0.02 0.20 0.010 0.010 0.068 0.0027
    e 0.002 0.02 0.15 0.013 0.010 0.053 0.0018
    f 0.083 0.02 0.15 0.006 0.010 0.067 0.0022
    Figure 00120001
    Figure 1 shows the relationship between the size distribution of MnS and neck wrinkling resistance for steel sheets with 0.03% of C in weight percent. Steel sheets having MnS size distribution within the range specified by the present invention have good neck wrinkling resistance. In Figure 1, the effects of MnS size distribution are separately shown by each slab reheating temperature category. The neck diameter reduction property is improved when slab reheating temperature is 1250°C or less and coiling temperature is at least 690°C even though the size distribution of MnS is almost the same.
    INDUSTRIAL APPLICABILITY
    According to the present invention, the rate of wrinkle generation during neck diameter reduction can be reduced. Further, since a steel according to the present invention shows good properties even with an annealing temperature lower than the temperature for a conventional steel, the generation of heat-buckle can be avoided and highly efficient production of a material for an ultra-thin can is made possible.

    Claims (6)

    1. A steel sheet for a two-piece can having excellent neck wrinkling resistance and anti-earing properties characterized by:
      the average diameter of AlN with a diameter of at least 0.005µm being 0.01 to 0.10µm,
      the ratio of the number of AlN with a diameter of 0.01µm or less to the number of AlN with a diameter of at least 0.005µm being 10% or less,
      the average diameter of MnS with a diameter of at least 0.005µm being 0.03 to 0.40µm,
      the ratio of the number of MnS with a diameter of 0.03µm or less to the number of MnS with a diameter of at least 0.005µm being 50% or less,
      the following equation being satisfied,
      (N existing as AlN)/(N content)>0.5, and
      the thickness of said steel sheet being 0.19mm or less.
    2. A steel sheet for a two-piece can having excellent neck wrinkling resistance and anti-earing properties characterized by:
      said steel sheet containing, in weight percent,
      C: 0.08% or less,
      Si: 0.05% or less,
      Mn: 0.04 - 0.4%,
      P: 0.04% or less,
      S: 0.04% or less,
      Al: 0.02 - 0.10%, and
      N: 40ppm or less; and
      the average diameter of AlN with a diameter of at least 0.005µm being 0.01 to 0.10µm,
      the ratio of the number of AlN with a diameter of 0.01µm or less to the number of AlN with a diameter of at least 0.005µm being 10% or less,
      the average diameter of MnS with a diameter of at least 0.005µm being 0.03 to 0.40µm,
      the ratio of the number of MnS with a diameter of 0.03µm or less to the number of MnS with a diameter of at least 0.005µm being 50% or less,
      the following equation being satisfied,
      (N existing as AlN)/(N content)>0.5, and
      the thickness of said steel sheet being 0.19mm or less.
    3. A steel sheet for a two-piece can having excellent neck wrinkling resistance and anti-earing properties characterized by:
      said steel sheet containing, in weight percent,
      C: 0.02 - 0.04%,
      Si: 0.029% or less,
      Mn: 0.15 - 0.25%,
      P: 0.010% or less,
      S: 0.020% or less,
      Al: 0.050 - 0.080%, and
      N: 40ppm or less; and
      the average diameter of AlN with a diameter of at least 0.005µm being 0.01 to 0.10µm,
      the ratio of the number of AlN with a diameter of 0.01µm or less to the number of AlN with a diameter of at least 0.005µm being 10% or less,
      the average diameter of MnS with a diameter of at least 0.005µm being 0.03 to 0.40µm,
      the ratio of the number of MnS with a diameter of 0.03µm or less to the number of MnS with a diameter of at least 0.005µm being 50% or less,
      the following equation being satisfied,
      (N existing as AlN)/(N content)>0.5, and
      the thickness of said steel sheet being 0.19mm or less.
    4. A method for producing a steel sheet for a two-piece can having excellent neck wrinkling resistance and anti-earing properties characterized by:
      said steel sheet containing, in weight percent,
      C: 0.08% or less,
      Si: 0.05% or less,
      Mn: 0.04 - 0.4%,
      P: 0.04% or less,
      S: 0.04% or less,
      Al: 0.02 - 0.10%, and
      N: 40ppm or less; and
      carrying out hot rolling at a slab reheating temperature in the range of 1150 - 1250°C and at a hot-rolling coiling temperature in the range of 690 - 750°C, cold-rolling with a cold-rolling reduction ratio in the range of 82 - 94%, annealing at a temperature between the recrystallization temperature and 720°C, and re-cold-rolling with a re-cold-rolling reduction ratio in the range of 1 - 10%; and
      the average diameter of AlN with a diameter of at least 0.005µm being 0.01 to 0.10µm,
      the ratio of the number of AlN with a diameter of 0.01µm or less to the number of AlN with a diameter of at least 0.005µm being 10% or less,
      the average diameter of MnS with a diameter of at least 0.005µm being 0.03 to 0.40µm,
      the ratio of the number of MnS with a diameter of 0.03µm or less to the number of MnS with a diameter of at least 0.005µm being 50% or less,
      the following equation being satisfied,
      (N existing as AlN)/(N content)>0.5, and
      the thickness of said steel sheet being 0.19mm or less.
    5. A method for producing a steel sheet for a two-piece can having excellent neck wrinkling resistance and anti-earing properties characterized by:
      said steel sheet containing, in weight percent,
      C: 0.08% or less,
      Si: 0.05% or less,
      Mn: 0.04 - 0.4%,
      P: 0.04% or less,
      S: 0.04% or less,
      Al: 0.02 - 0.10%, and
      N: 40ppm or less; and
      carrying out hot rolling at a slab reheating temperature in the range of 1000 - 1150°C, cold-rolling with a cold-rolling reduction ratio in the range of 82 - 94%, annealing at a temperature between the recrystallization temperature and 720°C, and re-cold-rolling with a re-cold-rolling reduction ratio in the range of 1 - 10%; and
      the average diameter of AlN with a diameter of at least 0.005µm being 0.01 to 0.10µm,
      the ratio of the number of AlN with a diameter of 0.01µm or less to the number of AlN with a diameter of at least 0.005µm being 10% or less,
      the average diameter of MnS with a diameter of at least 0.005µm being 0.03 to 0.40µm,
      the ratio of the number of MnS with a diameter of 0.03µm or less to the number of MnS with a diameter of at least 0.005µm being 50% or less,
      the following equation being satisfied,
      (N existing as AlN)/(N content)>0.5, and
      the thickness of said steel sheet being 0.19mm or less.
    6. A method for producing a steel sheet for a two-piece can having excellent neck wrinkling resistance and anti-earing properties characterized by:
      said steel sheet containing, in weight percent,
      C: 0.02 - 0.04%,
      Si: 0.029% or less,
      Mn: 0.15 - 0.25%,
      P: 0.010% or less,
      S: 0.020% or less,
      Al: 0.050 - 0.080%, and
      N: 40ppm or less; and
      carrying out hot rolling at a slab reheating temperature in the range of 1150 - 1250°C and at a hot-rolling coiling temperature in the range of 690 - 750°C, cold-rolling with a cold-rolling reduction ratio in the range of 82 - 94%, annealing at a recrystallization temperature in the range of 650 - 670°C, and re-cold-rolling with a re-cold-rolling reduction ratio in the range of 1 - 2%; and
      the average diameter of AlN with a diameter of at least 0.005µm being 0.01 to 0.10µm,
      the ratio of the number of AlN with a diameter of 0.01µm or less to the number of AlN with a diameter of at least 0.005µm being 10% or less,
      the average diameter of MnS with a diameter of at least 0.005µm being 0.03 to 0.40µm,
      the ratio of the number of MnS with a diameter of 0.03µm or less to the number of MnS with a diameter of at least 0.005µm being 50% or less,
      the following equation being satisfied,
      (N existing as AlN)/(N content)>0.5, and
      the thickness of said steel sheet being 0.19mm or less.
    EP00915519.3A 1999-04-20 2000-04-13 Steel sheet for ultra-thin two-piece cans having excellent anti-wrinkling properties and method for producing thereof Expired - Lifetime EP1088905B2 (en)

    Applications Claiming Priority (3)

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    JP11285299 1999-04-20
    JP11285299 1999-04-20
    PCT/JP2000/002426 WO2000063453A1 (en) 1999-04-20 2000-04-13 Very thin 2-piece container steel sheet excellent in pucker resistance at neck diameter reduction and in earing and production method therefor

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    Cited By (1)

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    EP1347071A1 (en) * 2002-03-21 2003-09-24 Usinor Cold worked aluminium killed steel sheet and process for manufacturing packaging from this metal sheet

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    JP2689148B2 (en) * 1988-11-19 1997-12-10 新日本製鐵株式会社 Manufacturing method of steel plate for squeeze can with small ear generation
    JPH0480345A (en) * 1990-07-19 1992-03-13 Nippon Steel Corp Cold rolled steel sheet excellent in workability, roughening property and earing property and its manufacture
    FR2678641B1 (en) † 1991-07-04 1998-11-20 Lorraine Laminage IMPROVED STAMPING STEEL AND METHOD FOR MANUFACTURING SHEETS FOR STAMPING.
    JP3103268B2 (en) * 1994-04-22 2000-10-30 新日本製鐵株式会社 Method for producing steel sheet for containers with excellent fluting resistance
    JPH08253820A (en) * 1995-03-16 1996-10-01 Nisshin Steel Co Ltd Production of thin steel sheet for can, excellent in aging resistance, by continuous annealing
    JP3975488B2 (en) * 1995-10-06 2007-09-12 Ｊｆｅスチール株式会社 Manufacturing method of thin steel sheet with excellent material uniformity
    JP3224732B2 (en) * 1996-03-28 2001-11-05 川崎製鉄株式会社 Cold rolled steel sheet having good aging resistance and method for producing the same
    JP3593235B2 (en) * 1997-02-26 2004-11-24 新日本製鐵株式会社 Method of manufacturing high strength ultra-thin welded steel sheet with excellent formability
    JP3740779B2 (en) * 1997-03-12 2006-02-01 Ｊｆｅスチール株式会社 Steel plate for easy open can lid excellent in openability and rivet formability, manufacturing method thereof, and easy open can lid
    JP3421942B2 (en) * 1997-07-18 2003-06-30 Ｊｆｅエンジニアリング株式会社 Slab for producing cold-rolled steel sheet for cans

    Cited By (3)

    * Cited by examiner, † Cited by third party
    Publication number Priority date Publication date Assignee Title
    EP1347071A1 (en) * 2002-03-21 2003-09-24 Usinor Cold worked aluminium killed steel sheet and process for manufacturing packaging from this metal sheet
    FR2837500A1 (en) * 2002-03-21 2003-09-26 Usinor NUT SHEET IN CALM ALUMINUM STEEL AND METHOD OF MANUFACTURING A PACKAGE FROM THIS SHEET
    US9039846B2 (en) 2002-03-21 2015-05-26 Usinor Cold-rolled aluminum killed steel sheet and method of manufacturing packaging from said sheet

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    EP1088905A4 (en) 2004-12-01
    EP1088905B1 (en) 2009-10-07
    DE60043087D1 (en) 2009-11-19
    JP4213870B2 (en) 2009-01-21
    EP1088905B2 (en) 2019-06-05

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