WO2016157878A1 - Tôle d'acier pour canettes et procédé de fabrication d'une feuille d'acier pour boîtes canettes - Google Patents

Tôle d'acier pour canettes et procédé de fabrication d'une feuille d'acier pour boîtes canettes Download PDF

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Publication number
WO2016157878A1
WO2016157878A1 PCT/JP2016/001774 JP2016001774W WO2016157878A1 WO 2016157878 A1 WO2016157878 A1 WO 2016157878A1 JP 2016001774 W JP2016001774 W JP 2016001774W WO 2016157878 A1 WO2016157878 A1 WO 2016157878A1
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less
cans
amount
depth position
steel plate
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PCT/JP2016/001774
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English (en)
Japanese (ja)
Inventor
多田　雅毅
克己 小島
裕樹 中丸
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Ｊｆｅスチール株式会社
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Application filed by Ｊｆｅスチール株式会社 filed Critical Ｊｆｅスチール株式会社
Priority to KR1020177027622A priority Critical patent/KR101994914B1/ko
Priority to CN201680019401.9A priority patent/CN107429360B/zh
Priority to JP2016544875A priority patent/JP6028884B1/ja
Publication of WO2016157878A1 publication Critical patent/WO2016157878A1/fr
Priority to CONC2017/0009718A priority patent/CO2017009718A2/es

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—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
    • C21D8/0221—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
    • C21D8/0268—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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • 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
    • 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
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite

Definitions

  • the present invention relates to a steel plate for cans and a method for producing a steel plate for cans.
  • the present invention relates to a steel plate for a can used as a raw material for a three-piece can formed by high-working can body processing, a two-piece can requiring pressure strength, and a method for manufacturing the same.
  • Measures to reduce the can manufacturing cost include reducing the cost of the material.
  • 2-piece cans formed by drawing even 3-piece cans mainly made of simple cylindrical molding are being used to reduce the thickness of the steel sheets used.
  • ultra-thin and hard steel plates for cans are manufactured by the Double Reduce method (hereinafter referred to as DR method) in which secondary cold rolling with a reduction rate of 20% or more is performed after annealing.
  • DR method Double Reduce method
  • a steel plate manufactured by using the DR method (hereinafter also referred to as a DR material) has a high strength, but has a feature that the total elongation is small.
  • a DR material having poor ductility as a can material formed by can body processing with a strong working degree, such as a deformed can.
  • Patent Document 1 proposes a technique for obtaining a steel sheet for high-strength cans by adding a large amount of C and N and baking and hardening.
  • the steel sheet for cans described in Patent Document 1 has a high yield stress of 550 MPa or more after the paint baking process.
  • Patent Document 2 As in Patent Document 1, high strength of about +50 MPa is realized by post-coating baking treatment.
  • Patent Document 3 proposes a steel plate that balances strength and ductility by combining precipitation strengthening with Nb carbide and refinement strengthening with Nb, Ti, and B carbonitrides.
  • Patent Document 4 proposes a method for increasing the strength by using solid solution strengthening such as Mn, P, and N.
  • Patent Document 5 the tensile strength is less than 540 MPa using precipitation strengthening by Nb, Ti, and B carbonitrides, and the deformability due to inclusions and precipitates is controlled by controlling the particle diameter of oxide inclusions.
  • Steel plates for cans that prevent deterioration and improve the formability of welds have been proposed.
  • JP 2001-107186 A Japanese Patent Laid-Open No. 11-199991 JP-A-8-325670 JP 2004-183074 A JP 2001-89828 A
  • the above-described conventional technology can produce a steel sheet that satisfies any of the strength, ductility, and corrosion resistance, but cannot produce a steel sheet that satisfies all of the requirements.
  • the method of adding a large amount of C and N described in Patent Documents 1 and 2 and increasing the strength by bake hardenability is an effective method for increasing the strength, but the solid solution C and N amount in steel Since there are many, yield elongation becomes large. And since yield elongation becomes large, the surface appearance is spoiled by generating wrinkles called stretcher strain during processing. Therefore, there is room for improvement in the techniques described in Patent Documents 1 and 2.
  • Patent Document 3 realizes high strength by precipitation strengthening and proposes a steel with a balance between strength and ductility, but does not describe the yield elongation that impairs the surface appearance. The yield elongation targeted by the invention cannot be obtained.
  • Patent Document 4 proposes an increase in strength by solid solution strengthening, but P and Mn, which are generally known as elements that inhibit corrosion resistance, are excessively added, so that there is a high risk of inhibiting corrosion resistance.
  • Patent Document 5 target strength is obtained by using precipitation and refinement strengthening of Nb, Ti and the like.
  • Patent Document 5 requires the addition of not only Ti but also Ca and REM.
  • the yield of the Ti alloy is poor as compared with the conventional method of deoxidizing with Al.
  • the present invention has been made in view of such circumstances, and provides a steel plate for cans having high strength, excellent ductility, and good corrosion resistance even for highly corrosive contents and a method for producing the same. With the goal.
  • the present inventors have conducted intensive research to solve the above problems. As a result, the following knowledge was obtained.
  • the strength can be increased without inferior in ductility by achieving solid solution strengthening with N and precipitation strengthening with Nb, Ti, and B.
  • composition of the original plate with the addition amount of elements within the range that does not affect the corrosion resistance, it shows good corrosion resistance even for highly corrosive contents.
  • the coiling temperature in the hot rolling process and the cooling rate after coiling can be adjusted appropriately to increase the strength without reducing the total elongation.
  • the present invention has been made based on the above findings, and the gist thereof is as follows.
  • a method for producing a steel plate for cans according to any one of [1] to [3], A hot rolling step in which the steel is rolled at a finish rolling temperature of Ar3 transformation point or higher, wound at a winding temperature of 500 to 620 ° C., and cooled at a cooling rate of 10 ° C./hr or lower after winding; After the hot rolling step, a primary cold rolling step of rolling at a rolling reduction of 80% or more, After the primary cold rolling step, an annealing step of continuous annealing at a soaking temperature of 660 to 800 ° C. and a soaking time of 55 s or less; And a secondary cold rolling step of rolling at a rolling reduction of 1 to 19% after the annealing step.
  • the present invention by increasing the strength of the steel sheet, it is possible to ensure a high strength of the can even if the welded can is made thinner. Further, due to the excellent ductility, it is possible to perform strong can barrel processing and flange processing such as can expansion processing used in welded cans.
  • the component composition is set so that the corrosion resistance is not hindered.
  • the steel plate for cans of the present invention is excellent in any of strength, ductility, and corrosion resistance.
  • the steel plate for cans according to the present invention has an excellent yield strength (hereinafter sometimes referred to as U-YP) after heat treatment at 210 ° C. for 20 minutes and a total elongation of 12% or more. Has corrosion resistance. Moreover, in the steel plate for cans of this invention, aging can also be made small.
  • U-YP yield strength
  • the upper yield strength is 480 to 700 MPa as described above, the total elongation is 12% or more, and A steel plate for cans having excellent corrosion resistance is obtained.
  • the steel plate for cans of the present invention is, by mass%, C: 0.020% or more and 0.130% or less, Si: 0.04% or less, Mn: 0.10% or more and 1.2% or less, P: 0.00.
  • the steel sheet for cans of the present invention it is essential that the upper yield strength (480 to 700 MPa) is achieved at a predetermined level or more and the total elongation is 12% or more.
  • the C content of the steel plate for cans is important. Specifically, it is necessary to set the lower limit of the C content to 0.020%.
  • the lower limit for the C content is 0.030%.
  • the upper limit of the C content is 0.130%.
  • the upper limit of the C content is 0.080%.
  • Si 0.04% or less Si is an element that increases the strength of a steel sheet by solid solution strengthening. However, if the Si content exceeds 0.04%, the corrosion resistance is significantly impaired. Therefore, the Si content is set to 0.04% or less. Preferably, the Si content is 0.02% or less. In the present invention, since it is possible to increase the upper yield strength by adjusting elements other than Si and manufacturing conditions, it is not necessary to use solid solution strengthening by Si. For this reason, in this invention, it is not necessary to contain Si. If a preferable example on the lower limit side is given about Si content, it is 0.001% or more.
  • Mn 0.10% or more and 1.2% or less Mn increases the strength of the steel sheet by solid solution strengthening and also reduces the average ferrite grain size.
  • the effect of reducing the average ferrite grain size is noticeably produced when the Mn content is 0.10% or more.
  • the Mn content in order to ensure the target upper yield strength, the Mn content must be 0.10% or more. Therefore, the lower limit of the Mn content is 0.10%.
  • the lower limit of the Mn content is 0.20%.
  • the upper limit of the Mn content is 1.2%.
  • the upper limit of Mn content is 0.80%.
  • P 0.007% or more and 0.100% or less
  • P is an element having a large solid solution strengthening ability.
  • the P content exceeds 0.100%, the corrosion resistance is poor. For this reason, the P content is 0.100% or less.
  • the P content is preferably 0.080% or less, more preferably 0.030% or less.
  • the P content is set to 0.007% or more.
  • the steel plate for cans of the present invention has a high C and N content, and includes one or more selected from Nb, Ti, and B that form precipitates that cause slab cracking. For this reason, the slab edge tends to break in the straightening zone during continuous casting.
  • the S content is set to 0.03% or less.
  • the S content is 0.02% or less. More preferably, the S content is 0.01% or less.
  • Al 0.0010% or more and 0.10% or less
  • Increasing the Al content results in an increase in the recrystallization temperature. Therefore, it is necessary to set the annealing temperature as high as the increase in the Al content.
  • the recrystallization temperature rises due to the influence of other elements added to increase the upper yield strength, and the annealing temperature must be set high. Therefore, it is necessary to avoid the increase in the recrystallization temperature due to Al as much as possible, and the Al content is set to 0.10% or less.
  • the Al content is preferably 0.070% or less.
  • the Al content is set to 0.0010% or more from the viewpoint of inclusion control.
  • Al is preferably added as a deoxidizer, and in order to obtain this effect, the Al content is preferably 0.010% or more.
  • N 0.0120% to 0.020% or less
  • N is an element necessary for increasing solid solution strengthening. In order to exert the effect of solid solution strengthening, the N content needs to be over 0.0120%. On the other hand, when there is too much N content, it will become easy to produce a slab crack in the lower correction zone where the temperature at the time of continuous casting falls. Therefore, the N content is 0.020% or less.
  • Nb 0.010% or more and 0.050% or less
  • Nb is an element having a high carbide generating ability and precipitates fine carbides.
  • the upper yield strength increases.
  • the upper yield strength can be adjusted by the Nb content. Since this effect occurs when the Nb content is 0.010% or more, the lower limit of the Nb content is limited to 0.010%. Preferably, the lower limit is 0.015%.
  • Nb brings about an increase in recrystallization temperature. Therefore, if the Nb content exceeds 0.050%, a large amount of unrecrystallized structure is caused by continuous annealing at an annealing temperature of 660 to 800 ° C. and a soaking time of 55 s or less. It remains difficult to anneal. For this reason, the upper limit of Nb content is limited to 0.050%.
  • Ti 0.010% or more and 0.050% or less Ti is also added for the purpose of obtaining upper yield strength and yield elongation for the same reason as Nb. Since this effect occurs when the content is 0.010% or more, the lower limit is made 0.010%. Preferably the lower limit is 0.015%.
  • the upper limit is also set to 0.050% from the viewpoint of the recrystallization temperature, similarly to Nb. Preferably the upper limit is 0.030%.
  • B 0.0010% or more and 0.010% or less B has the effect of reducing yield elongation because it promotes cementite precipitation using B-based precipitates in ferrite grains as nuclei. Since this effect occurs when the content is 0.0010% or more, the lower limit is made 0.0010%. Preferably the lower limit is 0.0012%. The upper limit is made 0.010% from the viewpoint of the recrystallization temperature. Preferably the upper limit is 0.0050%.
  • the remainder other than the above components is Fe and inevitable impurities.
  • the structure has a ferrite phase, and the area ratio of the ferrite phase is 50% or more.
  • the steel plate for cans of the present invention has a ferrite phase. From the viewpoint of securing strength and ductility, the steel plate for cans of the present invention has an area ratio of ferrite phase of 50% or more.
  • the area ratio of the ferrite phase is preferably 70% or more, and more preferably 100%.
  • the area ratio of the ferrite phase is determined from the structure photograph taken by grinding a cross section parallel to the rolling direction and then corroding with a nital liquid, in the field of view at a depth of 4/8 from the steel sheet surface in the thickness direction. It is determined by dividing and dividing the area of the ferrite phase by the total area.
  • the ferrite phase of the present invention preferably has a recrystallized structure.
  • the present invention may include a rolled structure that is a high-strength non-recrystallized structure.
  • the rolled structure which is an unrecrystallized structure, appears to be black due to corrosion because the crystal grains are crushed by rolling, and the recrystallized structure is ferrite.
  • the crystal grains since the crystal grains are grown by recrystallization, the crystal grains look white without being corroded.
  • the ratio of N amount is set to 0.96 or less. It is considered that by making the material difference in the plate thickness direction, it is possible to achieve both excellent ductility and strength while maintaining good corrosion resistance. The greater the material difference, the better the balance between ductility and strength, and both high strength and high ductility can be achieved. Therefore, the amount of dissolved N in the region from the surface to 1/8 depth position in the plate thickness direction and the solid solution in the region from the surface to 3/8 depth position to 4/8 depth position in the plate thickness direction.
  • the ratio of N amount is preferably 0.93 or less, more preferably 0.91 or less, and even more preferably 0.89 or less.
  • the amount of solute N in the region from the surface to the depth of 1/8 in the plate thickness direction increases as the hot rolling coiling temperature decreases, and decreases as the hot rolling coiling temperature increases. Become. Further, if the cooling rate after winding is reduced, the amount of solute N in the region from the surface to the 1/8 depth position in the plate thickness direction becomes a small value.
  • the amount of solute N in the region from the surface to the 1/8 depth position in the plate thickness direction is preferably 0.0114 to 0.0190 mass%.
  • the amount of solute N in the region from the surface to the 3/8 depth position to the 4/8 depth position in the thickness direction is preferably 0.0118 to 0.0198 mass%.
  • the amount of solute N between the surface in the plate thickness direction and the depth of 1/8 of the plate thickness is extracted with 10% Br methanol to a depth of 1/8 of the plate thickness, and precipitated as AlN, BN, etc.
  • the amount of N present is analyzed, and then the amount of N deposited as AlN, BN, etc. is subtracted from the total amount of N.
  • the amount of solute N between the depth position of 3/8 and the depth position of 4/8 from the surface in the plate thickness direction is obtained after oxalic acid polishing to the depth position of 3/8 of the plate thickness. Extracted and washed, extracted with 10% Br methanol, analyzed the amount of N deposited as AlN, BN, etc., and then calculated by subtracting the amount of N deposited as AlN, BN, etc. from the total N amount To do. The total N amount is expressed by mass%, and the sample is continuously included from the surface to the depth position of 4/8 that is the center in the plate thickness direction, and 4/8 that is the center in the plate thickness direction from the surface. The average N mass% up to the depth position was calculated.
  • the upper yield strength and the total elongation after heat treatment at 210 ° C. for 20 minutes are defined.
  • the upper yield strength is set to 480 MPa or more for the plate thickness of about 0.19 mm.
  • the upper yield strength is preferably 500 MPa or more.
  • the upper yield strength is 700 MPa or less.
  • the upper yield strength of the steel plate for cans can be controlled to 480 to 700 MPa by employing the above component composition and, for example, the production conditions described later.
  • Total elongation 12% or more If the total elongation of the steel plate for cans is less than 12%, there is a risk that defects such as cracks may occur in the production of cans formed by can body processing such as can expansion processing. There is. On the other hand, if the total elongation is less than 12%, cracks may occur during flange processing of the can. Therefore, the lower limit of total elongation is 12%.
  • the total elongation is preferably 13% or more, more preferably 14% or more.
  • the total elongation can be controlled to 12% or more by setting the amount of ferrite phase as a recrystallized structure in a specific range and then setting the rolling reduction ratio of secondary cold rolling after annealing in a specific range.
  • the total elongation obtained when producing by controlling the reduction ratio of secondary cold rolling is preferably 35% or less, more preferably 25% or less.
  • the plate thickness of the steel plate for cans of the present invention is not particularly limited, but may be 0.4 mm or less, 0.3 mm or less, or 0.2 mm or less.
  • the steel plate for cans of the present invention may further be provided with a plating layer.
  • the plating layer include an Sn plating layer, a Cr plating layer such as tin-free, an Ni plating layer, and an Sn—Ni plating layer.
  • the manufacturing method of the steel plate for cans of the present invention will be described. It is preferable that the steel plate for cans of this invention is manufactured with the manufacturing method which has a hot rolling process, a primary cold rolling process, an annealing process, and a secondary cold rolling process. Hereinafter, each manufacturing process will be described.
  • Hot rolling process is a process in which steel is rolled at a finish rolling temperature of Ar3 transformation point or higher, wound at a winding temperature of 500 to 620 ° C, and cooled at a cooling rate of 10 ° C / hr or lower after winding. It is the process of cooling.
  • Steel is obtained by melting molten steel adjusted to the above-described component composition by a known melting method using a converter or the like, and then forming a rolled material by a commonly used casting method such as a continuous casting method. It is done.
  • Hot rolled steel sheet is manufactured by hot rolling the steel obtained as described above. At the start of hot rolling, the temperature of the steel is preferably 1200 ° C. or higher.
  • the finish rolling temperature in hot rolling is set to the Ar3 transformation point or higher.
  • the Ar3 transformation point is determined at a temperature at which the volume of the sample expands due to the ⁇ ⁇ ⁇ transformation in the process of heating the sample to 1200 ° C. and then slowly cooling it with a processing for master.
  • the finish rolling temperature in the hot rolling is an important condition for securing the upper yield strength.
  • the finish rolling temperature in the hot rolling is limited to the Ar3 transformation point or higher.
  • finish rolling temperature in hot rolling is preferably in the range of Ar3 transformation point to Ar3 transformation point + 20 ° C.
  • the upper limit of finish rolling temperature is not specifically limited, It is preferable to make 980 degreeC into an upper limit for the reason of suppressing scale generation.
  • the coiling temperature in the hot rolling process is an important condition for controlling the upper yield strength and the total elongation, which are important in the present invention.
  • the minimum of coiling temperature shall be 500 degreeC.
  • the lower limit of the winding temperature is 550 ° C.
  • the upper limit of coiling temperature shall be 620 degreeC.
  • the upper limit of the coiling temperature is 600 ° C.
  • a cooling rate of 10 ° C./hr or less after winding in the hot rolling process is an important condition.
  • the cooling rate after winding exceeds 10 ° C./hr, the surface layer is rapidly cooled, so that the precipitation of AlN on the surface layer decreases, the amount of solute N increases, and the total elongation decreases.
  • the lower limit of the cooling rate is not particularly limited, but is preferably 2 ° C./hr or more from the viewpoint of the production efficiency of the steel sheet.
  • the primary cold rolling step is a step of cold rolling at a rolling reduction of 80% or more after the hot rolling step.
  • another process may be suitably included after the hot rolling process and before the primary cold rolling process, or the primary cold rolling process may be performed immediately after the hot rolling process.
  • the surface layer scale formed in the hot rolling process it is preferable to remove the surface layer scale formed in the hot rolling process.
  • the method for removing the surface scale is not particularly limited, and various methods such as chemical removal such as pickling and physical removal can be applied.
  • the rolling reduction in the primary cold rolling process is one of the important conditions in the present invention. If the rolling reduction in the primary cold rolling process is less than 80%, it is difficult to produce a steel sheet having an upper yield strength of 480 MPa or more. Furthermore, when the reduction ratio in this process is less than 80%, in order to obtain a plate thickness (about 0.17 mm) similar to that of a conventional DR material in which the reduction ratio in the secondary cold rolling process is 20% or more At least the thickness of the hot rolled sheet needs to be 0.9 mm or less. However, in operation, it is difficult to set the thickness of the hot rolled sheet to 0.9 mm or less. Therefore, the rolling reduction in this step is 80% or more.
  • the upper limit of the rolling reduction in the primary cold rolling step is not particularly limited, but a rolling reduction of 95% or less is preferable from the viewpoint of suppressing surface defects.
  • An annealing step is a step of performing continuous annealing after the primary cold rolling step at a soaking temperature of 660 to 800 ° C. and a soaking time of 55 seconds or less.
  • the unit “s” means “second”.
  • another process may be appropriately included before the annealing process after the primary cold rolling process, or the annealing process may be performed immediately after the primary cold rolling process.
  • a continuous annealing device is used for annealing.
  • the soaking temperature is set to 660 ° C. or higher.
  • the soaking temperature is set in the range of 660 to 800 ° C.
  • the soaking temperature is preferably 660 to 710 ° C, more preferably 660 to 705 ° C.
  • the soaking time is 55 s or less.
  • the soaking time is preferably 40 s or less.
  • the lower limit of the soaking time is not particularly limited, but in order to shorten the soaking time, it is necessary to increase the transport speed, so that it is difficult to stably transport without meandering. It is preferable that
  • the secondary cold rolling step is a step of cold rolling at a rolling reduction of 1 to 19% after the annealing step.
  • another process may be appropriately included before the secondary cold rolling process after the annealing process, or the secondary cold rolling process may be performed immediately after the annealing process.
  • the reduction ratio in the secondary cold rolling after annealing is the same as the normal DR material production conditions (20% or more), the strain introduced during processing increases, so the total elongation decreases.
  • the reduction ratio in the secondary cold rolling is set to 19% or less.
  • secondary cold rolling has a role of imparting surface roughness of the steel sheet, and in order to uniformly impart surface roughness to the steel sheet, the reduction ratio of secondary cold rolling needs to be 1% or more.
  • the rolling reduction in the secondary cold rolling process may be 8 to 19%.
  • the tensile test was performed using a JIS No. 5 size tensile test piece, the upper yield strength (U-YP) was measured according to JIS Z 2241, and the total elongation (El) was measured according to JIS Z 2241. The obtained results are shown in Table 3.
  • the steel plate for cans of the invention example had an area ratio of the ferrite phase of 50% or more.
  • the ferrite phase had a recrystallized structure.
  • the solute N amount in the region from the surface to 1/8 depth position in the plate thickness direction, and the solute N amount in the region from the surface 3/8 depth position to 4/8 depth position are nitrided from the total N amount It measured by the method of reducing N amount of a thing.
  • the measurement results are shown in Table 4.
  • Compressive strength After roll form, welding, neck forming, and flange forming using steel plates, a lid was wound and a blank can sample was prepared, placed in a chamber, and the pressure at which the sample was buckled after being pressurized with compressed air was measured. A buckling pressure of 0.2 MPa or more was rated as ⁇ , 0.14 to 0.13 MPa as ⁇ , and less than 0.13 MPa as x (failed).
  • Formability Wrinkles at the time of neck forming when roll forming, welding, and neck forming using a steel plate were observed. The case where there was no visual wrinkle was rated as ⁇ , the case where one fine wrinkle was seen visually was marked as ⁇ , and the case where two or more fine wrinkles were seen visually was marked as x (failed).
  • Corrosion resistance It was evaluated using an alloy tin couple (ATC) test facility used for evaluating the corrosion resistance of electroplated tin. What ATC value is less than 0.05 ⁇ A / cm 2 ⁇ , those 0.05 ⁇ 0.12 ⁇ A / cm 2 ⁇ , and a ⁇ (fail) those exceeding 0.12 ⁇ A / cm 2.
  • the present invention it is possible to obtain a steel plate for cans having high strength, excellent ductility, and good corrosion resistance even for highly corrosive contents.
  • the present invention is most suitable as a steel plate for cans centering on a three-piece can with a high degree of can body processing and a two-piece can whose bottom portion is processed by several percent.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
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Abstract

La présente invention concerne une tôle d'acier pour canettes et un procédé de fabrication de la tôle d'acier pour canettes. La tôle d'acier pour canettes possède une composition de composants contenant, sur une base de pourcentage en masse : 0,020 à 0,130 % de C ; pas plus de 0,04 % de Si ; 0,10 % à 1,2 % de Mn ; 0,007 à 0,100 % de P ; pas plus de 0,03 % de S ; 0,0010 à 0,10 % de Al, 0,0120 à 0,020 % de N ; un ou plusieurs éléments sélectionnés parmi 0,010 à 0,050 % de Nb, 0,010 à 0,050 % de Ti et 0,0010 à 0,010 % de B ; le reste étant du fer et des impuretés inévitables. La tôle d'acier pour canettes possède une structure comprenant une phase de ferrite dans laquelle le rapport surfacique de la phase de ferrite n'est pas inférieur à 50 %. La tôle d'acier pour canettes possède une limite d'élasticité supérieure de 480 à 700 MPa après un traitement thermique à 210 °C pendant 20 minutes, et un allongement total non inférieur à 12 %. Le rapport entre la teneur en soluté N dans une région s'étendant de la surface à une profondeur de 1/8, dans le sens de l'épaisseur et la teneur en soluté N dans une région s'étendant à partir d'une profondeur de 3/8 à partir de la surface jusqu'à une profondeur de 4/8, satisfait la formule 1. (quantité de soluté N dans la région s'étendant à partir de la surface jusqu'à la profondeur de 1/8 dans le sens de l'épaisseur)/(quantité de soluté N dans la région s'étendant à partir de la profondeur de 3/8 à partir de la surface jusqu'à la profondeur de 4/8) ≤ 0,96 (formule 1)
PCT/JP2016/001774 2015-03-31 2016-03-28 Tôle d'acier pour canettes et procédé de fabrication d'une feuille d'acier pour boîtes canettes WO2016157878A1 (fr)

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CN201680019401.9A CN107429360B (zh) 2015-03-31 2016-03-28 罐用钢板及罐用钢板的制造方法
JP2016544875A JP6028884B1 (ja) 2015-03-31 2016-03-28 缶用鋼板及び缶用鋼板の製造方法
CONC2017/0009718A CO2017009718A2 (es) 2015-03-31 2017-09-27 Hoja de acero para una lata y método para fabricarla

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WO2019088044A1 (fr) * 2017-10-31 2019-05-09 Ｊｆｅスチール株式会社 Tôle d'acier à haute résistance, et procédé de fabrication de celle-ci
WO2020261965A1 (fr) * 2019-06-24 2020-12-30 Ｊｆｅスチール株式会社 Tôle d'acier pour canette et son procédé de fabrication
CN113242909A (zh) * 2018-12-20 2021-08-10 杰富意钢铁株式会社 罐用钢板及其制造方法
JPWO2021167023A1 (fr) * 2020-02-21 2021-08-26
CN113748220A (zh) * 2019-03-29 2021-12-03 杰富意钢铁株式会社 罐用钢板和其制造方法
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JP6028884B1 (ja) 2016-11-24
KR20170121277A (ko) 2017-11-01
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