EP3138936B1 - Hochfestes stahlblech und herstellungsverfahren dafür - Google Patents

Hochfestes stahlblech und herstellungsverfahren dafür Download PDF

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Publication number
EP3138936B1
EP3138936B1 EP15786615.3A EP15786615A EP3138936B1 EP 3138936 B1 EP3138936 B1 EP 3138936B1 EP 15786615 A EP15786615 A EP 15786615A EP 3138936 B1 EP3138936 B1 EP 3138936B1
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EP
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less
rolling
strength
steel sheet
steel sheets
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English (en)
French (fr)
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EP3138936A1 (de
EP3138936A4 (de
Inventor
Hayato Saito
Katsumi Kojima
Masaki Tada
Hiroki Nakamaru
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JFE Steel Corp
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JFE Steel Corp
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Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—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 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0268—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment between cold rolling steps
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite

Definitions

  • the present invention relates to high-strength steel sheets which are suited as can-making materials used in the production of food cans and beverage cans, and to methods for manufacturing such steel sheets.
  • the high-strength steel sheets of the invention exhibit highly excellent formability and can be suitably used for the manufacturing of easy-open-ends (EOEs) and welded can bodies.
  • EEEs easy-open-ends
  • DR double reduced steels
  • can-making steel sheets for the production of beverage cans and food cans and are formed into parts such as lids, bottoms and three-piece can bodies.
  • the steel sheets are cold rolled again after annealing.
  • the DR steels can be easily reduced in thickness while increasing hardness as compared to SR (single reduced) steels whose production involves only temper rolling with a small rolling reduction.
  • Patent Literatures 1 and 2 propose DR steels having improved formability.
  • WO2008018531 proposes DR steels characterized in that the steel contains, in mass%, C: 0.02% to 0.06%, Si: 0.03% or less, Mn: 0.05% to 0.5%, P: 0.02% or less, S: 0.02% or less, Al: 0.02% to 0.10% and N: 0.008% to 0.015%, the balance being Fe and inevitable impurities, the amount of solute N (Ntotal - NasAlN) in the steel sheet is 0.006% or more, the total elongation in the rolling direction after aging treatment is 10% or more, the total elongation in the sheet width direction after aging treatment is 5% or more, and the average Lankford value after aging treatment is 1.0 or less.
  • Patent Literature 2 proposes high-strength thin steel sheets with excellent flangeability for welded cans characterized in that the steel contains, in mass%, C: more than 0.04% and 0.08% or more, Si: 0.02% or less, Mn: 1.0% or less, P: 0.04% or less, S: 0.05% or less, Al: 0.1% or less and N: 0.005 to 0.02%, the total of solute C and solute N dissolved in the steel sheet satisfies 50 ppm ⁇ solute C + solute N ⁇ 200 ppm, the amount of solute C in the steel sheet is 50 ppm or more and the amount of solute N in the steel sheet is 50 ppm or more, the balance of the composition being Fe and inevitable impurities.
  • WO2013151085 discloses a high strength and high form ability steel sheet comprising, by mass: more than 0.020% and less than 0.040% C; 0.003% to 0.100% Si; 0.10% to 0.60% Mn; 0.001% to 0.100% P; 0.001 % to 0.020% S; 0.005% to 0.100% Al, and more than 0.0130% to 0.0170% of N, remainder Fe and inevitable impurities.
  • the steel sheet has a tensile strength in a rolling direction of not lower than 520 MPa; an Erichsen value of not less than 5.0 mm; and a resin film layer at least on a side to be an inner surface of a can.
  • the technique described in WO2008018531 does not necessarily realize good formability depending on conditions such as the number of steps in the formation of rivets in EOE cans. Further, the technique described in Patent Literature 1 does not attain sufficient workability such as flangeability for three-piece cans.
  • an object of the invention is to provide high-strength steel sheets having good formability (workability) and strength and methods for manufacturing such steel sheets.
  • the present inventors carried out extensive studies. As a result, the present inventors have found that the optimization of chemical composition of steel, hot rolling conditions, cold rolling conditions, annealing conditions and secondary cold rolling conditions (DR conditions) attains a tensile strength of 530 MPa or more and an elongation of 7% or more in the transverse direction after aging treatment. Further, the present inventors have found that the average ferrite grain size and the density of dislocations at 1/4 sheet thickness contribute to the satisfaction of the above tensile strength and elongation. The present invention has been completed based on the findings. Specifically, the invention resides in the following aspects.
  • the high-strength steel sheets of the invention have high formability as described above, and may be suitably used in applications in which the steel sheets are formed into rivets or are flanged.
  • the inventive high-strength steel sheets have a tensile strength of 530 MPa or more. This sufficient strength allows the sheets to form quality can bodies or lids even when the sheet thickness is reduced compared to the conventional materials. The reduction of sheet thickness saves resources and costs.
  • the high-strength steel sheets of the invention which are excellent in formability and strength, are not only used in various types of metal cans but are also expected to find use in a wide range of applications such as battery interior cases, various home appliance and electrical parts, and automobile parts.
  • the high-strength steel sheets of the invention have a specific chemical composition, and the average ferrite grain size and the density of dislocations at 1/4 sheet thickness are controlled to fall in the specific ranges.
  • the inventive high-strength steel sheets attain excellent formability while exhibiting high strength.
  • the chemical composition, the average ferrite grain size, the density of dislocations at 1/4 sheet thickness, the quality (high strength, high formability) of the high-strength steel sheets, and the methods for manufacturing the high-strength steel sheets will be sequentially described.
  • the high-strength steel sheet of the invention has a chemical composition including, in mass%, C: 0.010% to 0.080%, Si: 0.05% or less, Mn: 0.10% to 0.70%, P: 0.03% or less, S: 0.020% or less, Al: 0.005% to 0.070% and N: 0.0120% to 0.0180%, the balance being Fe and inevitable impurities.
  • N content in the steel 0.0100% or more is the content of solute nitrogen.
  • Carbon is an element that contributes to increasing the strength of the steel sheets.
  • the steel can attain a tensile strength of 530 MPa or more in the transverse direction after aging treatment. If the C content exceeds 0.080%, the elongation in the transverse direction after aging treatment falls to below 7% and the steel sheets exhibit poor flangeability or rivet formability. Thus, the C content needs to be limited to 0.080% or less. To ensure good flangeability and rivet formability, it is preferable that the C content be less than 0.040%. Because the average ferrite grain size is reduced with increasing C content, it is preferable that the C content be 0.020% or more in order to ensure that the steel sheets will exhibit high strength.
  • the element is enriched at the surface to cause a decrease in the surface treatment properties of the steel sheets. Consequently, the corrosion resistance of the steel sheets is reduced.
  • the Si content needs to be limited to 0.05% or less.
  • the Si content is preferably 0.03% or less.
  • Manganese has an effect of enhancing the hardness of the steel sheets by solution strengthening. Further, manganese forms MnS and thereby effectively prevents the decrease in hot ductility (casting properties) ascribed to sulfur present in the steel. To obtain these effects, the Mn content needs to be limited to 0.10% or more. Because manganese has an effect of reducing the grain size, it is preferable that the Mn content be 0.20% or more. Further, manganese decreases the rate of the diffusion of nitrogen and thereby inhibits the formation of AlN to ensure the presence of nitrogen as solute. Thus, the addition of manganese is effective particularly when the tensile strength is to be increased to 590 MPa or more.
  • the Mn content be more than 0.50%.
  • the Mn content is limited to 0.70% or less because any excessive addition of manganese not only results in the saturation of the above effects but also causes a marked decrease in elongation.
  • Abundant phosphorus causes a decrease in formability by excessive hardening or central segregation. Further, the presence of a large amount of phosphorus causes a decrease in corrosion resistance. Thus, the P content is limited to 0.03% or less. The P content is preferably 0.02% or less.
  • the S content is limited to 0.020% or less.
  • the S content is preferably 0.015% or less.
  • Aluminum is an element added as a deoxidizer. To obtain this effect, the Al content needs to be limited to not less than 0.005%. Aluminum decreases the amount of solute nitrogen in the steel by forming AlN with nitrogen. The decrease in the amount of solute nitrogen results in a decrease in the strength of the steel sheets. Thus, the Al content is limited to 0.070% or less. To ensure that the amount of solute nitrogen will be stably 0.0100% or more, it is preferable that the Al content be 0.020% or less, and more preferably 0.018% or less.
  • Nitrogen present in the form of solute nitrogen contributes to increasing the strength of the steel sheets.
  • solute nitrogen is present in 0.0100% or more, the introduction of dislocations during secondary cold rolling is facilitated and consequently the balance between high strength and formability is enhanced.
  • the content of nitrogen in the form of solute nitrogen needs to be limited to 0.0100% or more.
  • the solute N content is more preferably 0.0120% or more.
  • the N content needs to be limited to 0.0120% or more.
  • the N content is preferably more than 0.0130%.
  • the formation of AlN during the manufacturing steps be suppressed by one or a combination of any of (1) controlling the Mn content to more than 0.50%, (2) controlling the coiling temperature during hot rolling to 640°C or less, preferably 600°C or less, and more preferably 580°C or less, and (3) controlling the annealing temperature to 690°C or less, and more preferably less than 680°C.
  • the tensile strength is increased to 600 MPa or more in order to further increase the strength or to further reduce the thickness of cans, it is preferable that all the above three conditions be combined so that the steel will exhibit high formability with the elongation being 10% or more.
  • the N content is limited to 0.0180% or less.
  • the N content is preferably 0.0170% or less. With the N content being in the above range, the content of nitrogen in the form of solute nitrogen is 0.0180% or less.
  • the balance between high strength and formability is enhanced by reducing the size of ferrite grains so that the average ferrite grain size will be 7.0 ⁇ m or less. Further, the reduction in average ferrite grain size provides another advantage that the roughening of skin after working is prevented. In view of this, the average ferrite grain size is preferably 6.5 ⁇ m or less.
  • the average ferrite grain size is a value measured by the method described in EXAMPLES. With the size of ferrite grains after annealing being finer, the introduction of dislocations during secondary cold rolling is facilitated more efficiently and consequently high strength is obtained even with a smaller rolling reduction.
  • the average ferrite grain size after secondary cold rolling is reduced compared to that after annealing (before the secondary cold rolling). In view of this fact, it is more preferable that the average ferrite grain size after the secondary cold rolling be 6.0 ⁇ m or less in order to obtain the above effects.
  • the lower limit of the average ferrite grain size is not particularly limited. If, however, the grains are excessively fine, the balance between high strength and formability is decreased. For this reason, the average grain size is preferably 1.0 ⁇ m or more.
  • the microstructure of the inventive steel is based on ferrite and the ferrite phase represents 98 vol% or more.
  • the control of the density of dislocations in the steel sheets is important in order to satisfy the strength and formability of the steel sheets at the same time.
  • the density of dislocations at a depth of 1/4 sheet thickness needs to be controlled to 4.0 ⁇ 10 14 m -2 or more in order to attain an increase in strength.
  • Dislocations present in an excessively high density induce the occurrence of voids during forming and thus cause a decrease in the formability of the steel sheets.
  • the dislocation density needs to be controlled to 2.0 ⁇ 10 15 m -2 or less.
  • the solute N content be controlled to 0.0100% or more or preferably 0.0120% or more, and the average ferrite grain size be controlled to 7.0 ⁇ m or less, preferably 6.5 ⁇ m or less or more preferably 6.0 ⁇ m or less.
  • the density of dislocations at 1/4 sheet thickness is a value measured by the method described in EXAMPLES.
  • the high-strength steel sheets of the present invention achieve high formability while having high strength by virtue of having the chemical composition described hereinabove and also because of the average ferrite grain size and the density of dislocations at 1/4 sheet thickness being controlled to 7.0 ⁇ m or less and from 4.0 ⁇ 10 14 m -2 to 2.0 ⁇ 10 15 m -2 .
  • the term "thin" means that the thickness is not more than 0.26 mm. According to the present invention, the sheet thickness can be reduced to 0.12 mm while still ensuring that high strength and high formability can be satisfied at the same time.
  • high strength means that the tensile strength in the transverse direction perpendicular to the rolling direction after aging treatment is not less than 530 MPa. With the tensile strength being not less than 530 MPa, sufficient strength of cans may be ensured when the steel sheets are formed into can lids or can bodies.
  • the tensile strength is preferably 550 MPa or more, and more preferably 590 MPa or more. With the tensile strength being 550 MPa or more, high strength and high formability can be satisfied simultaneously even when the sheets are extremely thin.
  • extremely thin means that the thickness is 0.18 mm or less.
  • high formability it is meant that the elongation in the transverse direction perpendicular to the rolling direction after aging treatment is 7% or more. With the elongation being 7% or more, the high-strength steel sheets of the invention applied to can bodies or EOE cans exhibit sufficient flangeability required for the production of can bodies or rivet formability demanded in the manufacturing of EOE cans. Higher formability is necessary when the tensile strength is as high as 550 MPa or more, and in this case it is preferable that the elongation in the transverse direction after aging treatment be 10% or more.
  • the high-strength steel sheets of the invention may be produced by a method including a hot rolling step, a primary cold rolling step, an annealing step and a secondary cold rolling step. These steps will be described below.
  • a slab having the aforementioned chemical composition except the solute N content (the solute N content may be satisfied or not satisfied) is heated at a heating temperature of 1180°C or more, rolled with the hot rolling finish temperature being 820 to 900°C, and coiled at a coiling temperature of 640°C or less.
  • the heating temperature is limited to 1180°C or more.
  • the heating temperature is preferably 1200°C or more. While the upper limit of the heating temperature is not particularly limited, an excessively high heating temperature may give rise to the occurrence of excessive scales, resulting in defects on the product surface. Thus, the heating temperature is preferably 1300°C or less.
  • the hot rolling finish temperature is more than 900°C, the grains in the hot-rolled sheet are coarsened and consequently the grain size in the annealed sheet is increased and the hardness of the steel sheet is decreased. Thus, the hot rolling finish temperature is limited to 900°C or less. If the hot rolling finish temperature is less than 820°C, the rolling takes place at or below the Ar3 transformation point, and consequently the formability is decreased due to the formation of coarse grains and the remaining of deformation microstructure. Thus, the hot rolling finish temperature is limited to 820°C or more.
  • the hot rolling finish temperature is preferably 840°C or more.
  • the coiling temperature is more than 640°C, a large amount of AlN is formed during the coiling and consequently the amount of solute nitrogen is reduced. Further, coiling at more than 640°C results in the coarsening of the grains in the hot-rolled sheet and thus causes the grain size after annealing to be increased.
  • the coiling temperature is limited to 640°C or less.
  • the coiling temperature is preferably 600°C or less, and more preferably 580°C or less.
  • the lower limit of the coiling temperature is not particularly limited. If, however, the coiling temperature is excessively low, a great variation in temperature is caused during cooling possibly to give rise to wide variations in tensile strength and elongation. In view of this, the coiling temperature is preferably 500°C or more.
  • the hot-rolled steel sheet is pickled and primarily cold rolled with a rolling reduction of 85% or more.
  • the pickling conditions are not particularly limited as long as skin scales can be removed. Usual pickling methods may be used.
  • the grain size after annealing may be reduced and the balance between tensile strength and elongation may be enhanced by appropriately controlling the rolling reduction during the primary cold rolling.
  • the rolling reduction is limited to 85% or more. Rolling with an excessively large reduction causes tensile strength and elongation to be widely anisotropic in plane, resulting in a decrease in formability.
  • the rolling reduction in this step is preferably less than 91.5%.
  • the cold-rolled sheet is annealed at an annealing temperature of 620°C or more and 690°C or less.
  • the microstructure should be sufficiently recrystallized during annealing.
  • the annealing temperature needs to be limited to 620°C or more. If the annealing temperature is excessively high, the average ferrite grain size is increased and the balance between tensile strength and elongation is lowered. In view of this, the annealing temperature is limited to 690°C or less. At high annealing temperatures, AlN tends to be formed to cause a decrease in the amount of solute nitrogen. Thus, it is preferable that the annealing temperature be 680°C or less.
  • the annealing method is not particularly limited. From the point of view of quality uniformity, a continuous annealing method is preferable.
  • the holding time in the annealing step is not particularly limited but is preferably not less than 5 seconds from the point of view of the uniformity in steel sheet temperature, and is preferably 90 seconds or less in order to prevent the increase in average ferrite grain size.
  • the annealed sheet is secondarily cold rolled with a rolling reduction of 8 to 20%.
  • the annealed steel sheet is strengthened by being subjected to the secondary rolling. Further, the thickness of the steel sheet is reduced by the secondary rolling.
  • the rolling reduction (the DR ratio) in the secondary cold rolling is limited to 8% or more. If the DR ratio is too high, the dislocation density is excessively increased and the formability is decreased. In view of this, the DR ratio is limited to 20% or less. When formability is particularly required, the DR ratio is preferably controlled to 15% or less.
  • the high-strength steel sheets of the invention are obtained in the manner described hereinabove.
  • the advantageous effects of the invention may be still attained even when the steel sheets obtained are subjected to surface treatments such as plating and chemical conversion.
  • the amount of solute nitrogen was determined by subtracting the amount of nitrogen as AlN measured by extraction analysis with 10% Br methanol, from the total amount of nitrogen.
  • JIS No. 5 tensile test piece was sampled in the transverse direction and was tested in accordance with JIS Z 2241 to evaluate the tensile strength and the elongation (total elongation).
  • a cross section in the rolling direction was buried, polished, and etched with Nital to expose the grain boundaries.
  • the average crystal grain sizes were measured by a linear intercept method. The average ferrite grain size was thus evaluated.
  • a rivet for the attachment of an EOE tab was formed to evaluate the rivet formability.
  • the rivet was formed by 3-step pressing.
  • the steel sheet was bulged and was thereafter shrunk (reduced in diameter) to form a cylindrical rivet 4.0 mm in diameter and 2.5 mm in height.
  • the rivet formability was evaluated as " ⁇ " when wrinkles or cracks had occurred on the rivet surface, and as " ⁇ " when the surface was free from wrinkles or cracks.
  • the steel sheet was seam welded to form a can body 52.8 mm in outer diameter.
  • the end portions were necked in to an outer diameter of 50.4 mm and were thereafter flanged to an outer diameter of 55.4 mm.
  • the presence or absence of flange cracks was evaluated.
  • the can body formed was of 190 g beverage can size.
  • the welding was performed along the steel sheet rolling direction.
  • the necking-in was carried out by a die-necking process, and the flanging by a spin-flanging process.
  • the flangeability was evaluated as "x" when the flanged portions had been cracked, and as "O" when there was no cracks.
  • Cans were fabricated by sealing lids to those samples which had been successfully necked-in and flanged.
  • the strength of the cans was measured by a dent test. An indenter having a tip radius of 10 mm and a length of 42 mm was pressed against the center of the can body opposite to the weld, and the load which caused the can body to be buckled was measured. The strength of the cans was evaluated as good " ⁇ " when the load was 70 N or more, and as " ⁇ " when the load was less than 70 N.
  • the hyphens "-" indicate that the steel sheet had been cracked during the flanging and the fabrication of a can failed.

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

Claims (2)

  1. Hochfestes Stahlblech mit einer chemischen Zusammensetzung, die in Masse-%, 0,010% bis 0,080% C, 0,05% oder weniger Si, mehr als 0,50% bis 0,70% Mn, 0,03% oder weniger P, 0,020% oder weniger S, 0,005% bis 0,070% Al sowie 0,0120% bis 0,0180% N umfasst, wobei der Rest Eisen und unvermeidbare Verunreinigungen sind,
    Stickstoff, der als gelöster Stickstoff vorliegt, einen Gehalt von 0,0120% oder mehr in dem N-Gehalt hat,
    eine durchschnittliche Ferrit-Korngröße 7,0 µm oder weniger beträgt,
    eine Dichte von Versetzungen in einer Tiefe von 1/4 Blechdicke von der Oberfläche 4,0 × 1014 m-2 bis 2,0 × 1015 m-2 beträgt, wobei die Versetzungs-Dichte (m-2) basierend auf ρ = 14,4ε2/(0,25 x 10-9)2 bewertet wird und ε eine Verformung ist,
    eine Zugfestigkeit und eine Dehnung in der Querrichtung senkrecht zu der Walzrichtung nach Alterungsbehandlung 600 MPa oder mehr und 10% oder mehr betragen.
  2. Verfahren zum Herstellen des hochfesten Stahlblechs nach Anspruch 1, das umfasst:
    einen Warmwalzschritt, in dem eine Bramme auf eine Erwärmungstemperatur von 1180°C oder darüber erhitzt wird, die Bramme mit einer Warmwalz-Endtemperatur von 820 bis 900°C gewalzt wird und das Blech bei einer Wickeltemperatur von 640°C oder darunter gewickelt wird,
    einen primären Kaltwalzschritt, in dem das warmgewalzte Stahlblech gebeizt wird und das Blech mit einer Walzreduktion von 85% oder mehr kaltgewalzt wird,
    einen Glühschritt, in dem das primärem Kaltwalzen unterzogene Stahlblech bei 620°C bis 690°C geglüht wird, sowie
    einen sekundären Kaltwalzschritt, in dem das geglühte Stahlblech sekundärem Kaltwalzen mit einer Walzreduktion von 8 bis 20% unterzogen wird.
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BR112016025118A2 (pt) 2017-08-15
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CN106460125B (zh) 2019-11-08
BR112016025118B1 (pt) 2021-02-17
PH12016501833B1 (en) 2017-01-09
PH12016501833A1 (en) 2017-01-09
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