WO2016157878A1 - Steel sheet for cans and method for manufacturing steel sheet for cans - Google Patents
Steel sheet for cans and method for manufacturing steel sheet for cans Download PDFInfo
- 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
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- less
- cans
- amount
- depth position
- steel plate
- Prior art date
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—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.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
210℃、20分の熱処理後における、上降伏強度が480~700MPa、全伸びが12%以上であり、
板厚方向に表面~1/8深さ位置までの領域における固溶N量と、表面から3/8深さ位置~4/8深さ位置までの領域における固溶N量の比が、下記の式1を満たす、缶用鋼板。
(板厚方向に表面~1/8深さ位置までの領域における固溶N量)/(板厚方向に表面から3/8深さ位置~4/8深さ位置までの領域における固溶N量)≦0.96・・・(式1)
[2]前記フェライト相が再結晶組織である、[1]に記載の缶用鋼板。 [1] 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: 0.007% or more, and 0.0. 100% or less, S: 0.03% or less, Al: 0.0010% or more and 0.10% or less, N: 0.0120% to 0.020% or less, and Nb: 0.010% or more and 0 .050% or less, Ti: 0.010% or more and 0.050% or less, B: One or two or more selected from 0.0010% or more and 0.010% or less, with the balance being iron and inevitable impurities Having a component composition, the structure has a ferrite phase, the area ratio of the ferrite phase is 50% or more,
The upper yield strength after heat treatment at 210 ° C. for 20 minutes is 480 to 700 MPa, and the total elongation is 12% or more.
The ratio of the amount of solute N in the region from the surface to 1/8 depth position in the sheet thickness direction and the amount of solute N in the region from the surface to 3/8 depth position to 4/8 depth position is as follows. A steel plate for cans that satisfies Equation 1 below.
(Solution N amount in region from surface to 1/8 depth position in plate thickness direction) / (Solution N in region from surface to 3/8 depth position to 4/8 depth position in plate thickness direction) Amount) ≦ 0.96 (Formula 1)
[2] The steel plate for cans according to [1], wherein the ferrite phase has a recrystallized structure.
鋼を、仕上げ圧延温度がAr3変態点以上で圧延し、巻き取り温度が500~620℃で巻き取り、巻取り後に冷却速度が10℃/hr以下で冷却する熱間圧延工程と、
前記熱間圧延工程後に、圧下率が80%以上で圧延する1次冷間圧延工程と、
前記1次冷間圧延工程後に、均熱温度が660~800℃、均熱時間が55s以下で連続焼鈍する焼鈍工程と、
前記焼鈍工程後に、圧下率が1~19%で圧延する2次冷間圧延工程と、を有する、缶用鋼板の製造方法。 [4] 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.
本発明の缶用鋼板においては、所定以上の上降伏強度(480~700MPa)を達成すると同時に12%以上の全伸びを有することが必須である。そのためにはNb添加で生成するNbCによる析出強化、Ti添加で生成するTiCによる析出強化、B添加で生成するBNによる析出強化を利用することが重要となる。NbC、TiCによる析出強化を利用するためには、缶用鋼板のC含有量が重要となる。具体的には、C含有量の下限を0.020%とすることが必要である。好ましくは、C含有量の下限は0.030%である。一方、C含有量が0.130%を超えると、鋼の溶製中冷却過程の中で亜包晶割れを起こす。このため、C含有量の上限は0.130%とする。好ましくは、C含有量の上限は0.080%である。 C: 0.020% or more and 0.130% or less In 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. For that purpose, it is important to use precipitation strengthening by NbC produced by addition of Nb, precipitation strengthening by TiC produced by addition of Ti, and precipitation strengthening by BN produced by addition of B. In order to utilize precipitation strengthening by NbC and TiC, 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%. Preferably, the lower limit for the C content is 0.030%. On the other hand, if the C content exceeds 0.130%, subperitectic cracking occurs during the cooling process during steel melting. For this reason, the upper limit of the C content is 0.130%. Preferably, the upper limit of the C content is 0.080%.
Siは固溶強化により鋼板を高強度化させる元素である。しかし、Si含有量が0.04%を超えると耐食性が著しく損なわれる。よって、Si含有量は0.04%以下とする。好ましくは、Si含有量は0.02%以下である。なお、本発明ではSi以外の元素や製造条件の調整により上降伏強度を高めることが可能であるため、Siによる固溶強化を利用する必要はない。このため、本発明においてはSiを含まなくてもよい。Si含有量について、あえて下限側の好ましい例をあげるなら、0.001%以上である。 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は固溶強化により鋼板の強度を増加させ、フェライト平均結晶粒径も小さくする。フェライト平均結晶粒径を小さくする効果が顕著に生じるのはMn含有量が0.10%以上である。また、目標の上降伏強度を確保するにはMn含有量を0.10%以上にする必要がある。よって、Mn含有量の下限を0.10%とする。好ましくは、Mn含有量の下限は0.20%である。一方、Mn含有量が1.2%を超えると耐食性、表面特性が劣る。よって、Mn含有量の上限を1.2%とする。好ましくは、Mn含有量の上限は0.80%である。 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. Moreover, 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%. Preferably, the lower limit of the Mn content is 0.20%. On the other hand, if the Mn content exceeds 1.2%, the corrosion resistance and surface properties are inferior. Therefore, the upper limit of the Mn content is 1.2%. Preferably, the upper limit of Mn content is 0.80%.
Pは固溶強化能が大きい元素ではある。しかし、Pの含有量が0.100%を超えると耐食性が劣る。このため、P含有量は0.100%以下とする。P含有量は好ましくは0.080%以下であり、より好ましくは0.030%以下である。また、P含有量を0.007%未満とするには脱りん時間が大幅に上昇する。このため、P含有量は0.007%以上とする。 P: 0.007% or more and 0.100% or less P is an element having a large solid solution strengthening ability. However, if 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. Moreover, in order to make P content less than 0.007%, dephosphorization time rises significantly. For this reason, the P content is set to 0.007% or more.
本発明の缶用鋼板はC、N含有量が高く、また、スラブ割れの原因となる析出物を形成するNb、Ti、Bから選ばれる一種または二種以上を含むため、連続鋳造時矯正帯でスラブエッジが割れやすくなる。スラブ割れを防止する点からS含有量は0.03%以下にする。好ましくはS含有量は0.02%以下である。より好ましくは、S含有量は0.01%以下である。 S: 0.03% or less 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. In view of preventing slab cracking, the S content is set to 0.03% or less. Preferably, the S content is 0.02% or less. More preferably, the S content is 0.01% or less.
Al含有量を増加すると、再結晶温度の上昇がもたらされるため、Al含有量の増加分だけ焼鈍温度を高く設定する必要がある。本発明においては、上降伏強度を増加させるために添加する他の元素の影響で再結晶温度が上昇し、焼鈍温度を高く設定しなければならない。そこで、Alによる再結晶温度の上昇を極力回避することが必要であり、Al含有量を0.10%以下とする。Al含有量は好ましくは0.070%以下である。一方、固溶Nを完全に除去するのは困難であるため、介在物制御の観点から、Al含有量を0.0010%以上とする。なお、Alは脱酸剤として添加することが好ましく、この効果を得るためにはAl含有量を0.010%以上とすることが好ましい。 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. In the present invention, 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. On the other hand, since it is difficult to completely remove the solid solution N, 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は固溶強化を増加させるために必要な元素である。固溶強化の効果を発揮させるためには、N含有量を0.0120%超えとする必要がある。一方、N含有量が多すぎると、連続鋳造時の温度が低下する下部矯正帯でスラブ割れが生じやすくなる。よって、N含有量は0.020%以下とする。 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は炭化物生成能の高い元素であり、微細な炭化物を析出させる。これにより、上降伏強度が上昇する。本発明では、Nb含有量によって上降伏強度を調整することができる。Nb含有量が0.010%以上のときにこの効果が生じるため、Nb含有量の下限は0.010%に限定する。好ましくは、下限は0.015%である。一方、Nbは再結晶温度の上昇をもたらすので、Nb含有量が0.050%を超えると、660~800℃の焼鈍温度、55s以下の均熱時間での連続焼鈍では未再結晶組織が多量に残存するなど、焼鈍し難くなる。このため、Nb含有量の上限を0.050%に限定する。 Nb: 0.010% or more and 0.050% or less Nb is an element having a high carbide generating ability and precipitates fine carbides. As a result, the upper yield strength increases. In the present invention, 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%. On the other hand, 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についてもNbと同様の理由で上降伏強度、降伏伸びを得ることを目的として添加する。0.010%以上含有するときにこの効果が生じるので、下限を0.010%とする。好ましくは下限は0.015%である。上限についてもNbと同様に、再結晶温度の観点から0.050%とする。好ましくは上限は0.030%である。 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はフェライト粒内のB系析出物を核としてセメンタイト析出を促進させるため、降伏伸びを小さくする効果を示す。0.0010%以上含有するときにこの効果が生じるので、下限を0.0010%とする。好ましくは下限は0.0012%である。上限については再結晶温度の観点から0.010%とする。好ましくは上限は0.0050%である。 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%.
本発明の缶用鋼板はフェライト相を有する。強度と延性確保の観点から、本発明の缶用鋼板ではフェライト相の面積率が50%以上である。好ましくはフェライト相の面積率が70%以上であり、より好ましくは100%である。フェライト相の面積率は圧延方向に平行な断面を研摩後にナイタル液で腐食して撮影した組織写真より、板厚方向に鋼板表面から4/8深さ位置の視野において圧延加工組織とフェライト相を分別して、フェライト相の面積を全面積で割算することで求める。 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.
板厚方向に表面から3/8深さ位置~4/8深さ位置までの領域の固溶N量を増やして上降伏強度をより上昇させることができる。一方、板厚方向に表面~1/8深さ位置までの領域では固溶N量を減らして軟質とし良好な全伸びを得ることができる。これらより、板厚方向に表面~1/8深さ位置までの領域における固溶N量と、板厚方向に表面から3/8深さ位置~4/8深さ位置までの領域における固溶N量の比を0.96以下とする。板厚方向で材質差をつけることで、良好な耐食性を保ちつつ、延性と強度を極めて優れた状態で両立させることができると考えられる。材質差は大きいほど延性と強度のバランスに優れ、高強度でかつ高延性を両立することができる。このため、板厚方向に表面~1/8深さ位置までの領域における固溶N量と、板厚方向に表面から3/8深さ位置~4/8深さ位置までの領域における固溶N量の比は、好ましくは0.93以下であり、より好ましくは0.91以下であり、さらにより好ましくは0.89以下である。板厚方向に表面~1/8深さ位置までの領域における固溶N量は、熱延の巻き取り温度を低くすれば大きな値になり、熱延の巻き取り温度を高くすれば小さな値になる。また、巻き取り後の冷却速度を小さくすれば、板厚方向に表面~1/8深さ位置までの領域における固溶N量は小さな値になる。 (Solution N amount in region from surface to 1/8 depth position in plate thickness direction) / (Solution N in region from surface to 3/8 depth position to 4/8 depth position in plate thickness direction) Amount) ≤ 0.96
The upper yield strength can be further increased by increasing 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. On the other hand, in the region from the surface to the 1 / 8th depth position in the plate thickness direction, the amount of dissolved N can be reduced to make it soft and to obtain good total elongation. From these, the solid solution N amount 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 3/8 depth position to 4/8 depth position in the plate thickness direction. 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.
上降伏強度:480~700MPa
0.19mm程度の板厚材について、溶接缶のデント強度、2ピース缶の耐圧強度を確保するために、上降伏強度を480MPa以上とする。上降伏強度は、好ましくは500MPa以上である。一方、700MPa超えの上降伏強度を得ようとすると多量の元素添加が必要となる。多量の元素添加は本発明の缶用鋼板の耐食性を阻害するおそれがある。そこで、上降伏強度は700MPa以下とする。上記成分組成を採用するとともに、例えば後述する製造条件を採用することで、缶用鋼板の上降伏強度を480~700MPaに制御することができる。 In the present invention, the upper yield strength and the total elongation after heat treatment at 210 ° C. for 20 minutes are defined.
Upper yield strength: 480 to 700 MPa
In order to ensure the dent strength of the welding can and the pressure strength of the two-piece can, 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. On the other hand, in order to obtain an upper yield strength exceeding 700 MPa, a large amount of element needs to be added. Addition of a large amount of element may hinder the corrosion resistance of the steel plate for cans of the present invention. Therefore, 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.
缶用鋼板の全伸びが12%を下回ると、例えば、拡缶加工のような缶胴加工により成形される缶の製造においてクラックなどの割れ発生等の不具合が発生するおそれがある。また、全伸びが12%を下回ると、缶のフランジ加工時にクラックが発生するおそれがある。従って、全伸びの下限は12%とする。全伸びは好ましくは13%以上であり、より好ましくは14%以上である。例えば、再結晶組織であるフェライト相の量を特定の範囲とした後、焼鈍後の2次冷間圧延の圧下率を特定の範囲にすることにより全伸び12%以上に制御することができる。2次冷間圧延の圧下率制御で製造する場合に得られる全伸びは、好ましくは35%以下であり、より好ましくは25%以下である。 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. For example, 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.
熱間圧延工程とは、鋼を、仕上げ圧延温度がAr3変態点以上で圧延し、巻き取り温度が500~620℃で巻き取り、巻取り後に冷却速度が10℃/hr以下で冷却する工程である。 Hot rolling process The 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.
1次冷間圧延工程は、熱間圧延工程後に、圧下率が80%以上で冷間圧延する工程である。なお、熱間圧延工程後1次冷間圧延工程前に適宜他の工程が含まれても良いし、熱間圧延工程の直後に1次冷間圧延工程を行っても良い。 Primary cold rolling step The primary cold rolling step is a step of cold rolling at a rolling reduction of 80% or more after the hot rolling step. In addition, 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.
焼鈍工程とは、1次冷間圧延工程後に、均熱温度が660~800℃、均熱時間が55s以下で連続焼鈍する工程である。ここで、単位「s」は「秒」を意味する。なお、1次冷間圧延工程後焼鈍工程前に適宜他の工程が含まれても良いし、1次冷間圧延工程の直後に焼鈍工程を行っても良い。 Annealing Step 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. Here, the unit “s” means “second”. In addition, 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.
2次冷間圧延工程とは、上記焼鈍工程後に、圧下率が1~19%で冷間圧延する工程である。なお、焼鈍工程後2次冷間圧延工程前に適宜他の工程が含まれても良いし、焼鈍工程の直後に2次冷間圧延工程を行っても良い。 Secondary cold rolling step The secondary cold rolling step is a step of cold rolling at a rolling reduction of 1 to 19% after the annealing step. In addition, 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.
本発明の製造方法では、2次冷間圧延後においても、種々の工程を行いうる。例えば、めっき工程、塗装焼付け処理工程、フィルムラミネート等の工程を行ってもよい。 After the secondary cold rolling process In the production method of the present invention, various processes can be performed even after the secondary cold rolling process. For example, you may perform processes, such as a plating process, a paint baking process, and a film lamination.
Claims (4)
- 質量%で、C:0.020%以上0.130%以下、Si:0.04%以下、Mn:0.10%以上1.2%以下、P:0.007%以上0.100%以下、S:0.03%以下、Al:0.0010%以上0.10%以下、N:0.0120%超え0.020%以下を含有し、さらにNb:0.010%以上0.050%以下、Ti:0.010%以上0.050%以下、B:0.0010%以上0.010%以下から選ばれる一種または二種以上を含み、残部が鉄および不可避的不純物からなる成分組成を有し、
組織はフェライト相を有し、該フェライト相の面積率が50%以上であり、
210℃、20分の熱処理後における、上降伏強度が480~700MPa、全伸びが12%以上であり、
板厚方向に表面~1/8深さ位置までの領域における固溶N量と、表面から3/8深さ位置~4/8深さ位置までの領域における固溶N量の比が、下記の式1を満たす、缶用鋼板。
(板厚方向に表面~1/8深さ位置までの領域における固溶N量)/(板厚方向に表面から3/8深さ位置~4/8深さ位置までの領域における固溶N量)≦0.96・・・(式1) In 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: 0.007% or more and 0.100% or less S: 0.03% or less, Al: 0.0010% or more and 0.10% or less, N: 0.0120% or more and 0.020% or less, and Nb: 0.010% or more and 0.050% Hereinafter, a component composition comprising Ti: 0.010% or more and 0.050% or less, B: one or more selected from 0.0010% or more and 0.010% or less, with the balance being iron and inevitable impurities. Have
The structure has a ferrite phase, the area ratio of the ferrite phase is 50% or more,
The upper yield strength after heat treatment at 210 ° C. for 20 minutes is 480 to 700 MPa, and the total elongation is 12% or more.
The ratio of the amount of solute N in the region from the surface to 1/8 depth position in the sheet thickness direction and the amount of solute N in the region from the surface to 3/8 depth position to 4/8 depth position is as follows. A steel plate for cans that satisfies Equation 1 below.
(Solution N amount in region from surface to 1/8 depth position in plate thickness direction) / (Solution N in region from surface to 3/8 depth position to 4/8 depth position in plate thickness direction) Amount) ≦ 0.96 (Formula 1) - 前記フェライト相が再結晶組織である、請求項1に記載の缶用鋼板。 The steel plate for cans according to claim 1, wherein the ferrite phase has a recrystallized structure.
- 前記フェライト相の面積率が70%以上である、請求項1又は2に記載の缶用鋼板。 The steel plate for cans according to claim 1 or 2, wherein the area ratio of the ferrite phase is 70% or more.
- 請求項1~3のいずれかに記載の缶用鋼板の製造方法であって、
鋼を、仕上げ圧延温度がAr3変態点以上で圧延し、巻き取り温度が500~620℃で巻き取り、巻取り後に冷却速度が10℃/hr以下で冷却する熱間圧延工程と、
前記熱間圧延工程後に、圧下率が80%以上で圧延する1次冷間圧延工程と、
前記1次冷間圧延工程後に、均熱温度が660~800℃、均熱時間が55s以下で連続焼鈍する焼鈍工程と、
前記焼鈍工程後に、圧下率が1~19%で圧延する2次冷間圧延工程と、を有する、缶用鋼板の製造方法。 A method for producing a steel plate for cans according to any one of claims 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.
Priority Applications (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2016544875A JP6028884B1 (en) | 2015-03-31 | 2016-03-28 | Steel plate for cans and method for producing steel plate for cans |
KR1020177027622A KR101994914B1 (en) | 2015-03-31 | 2016-03-28 | Steel sheet for can and method for manufacturing the same |
CN201680019401.9A CN107429360B (en) | 2015-03-31 | 2016-03-28 | The manufacturing method of steel plate for tanks and steel plate for tanks |
CONC2017/0009718A CO2017009718A2 (en) | 2015-03-31 | 2017-09-27 | Steel sheet for a can and method of manufacturing it |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2015-071649 | 2015-03-31 | ||
JP2015071649 | 2015-03-31 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2016157878A1 true WO2016157878A1 (en) | 2016-10-06 |
Family
ID=57005566
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2016/001774 WO2016157878A1 (en) | 2015-03-31 | 2016-03-28 | Steel sheet for cans and method for manufacturing steel sheet for cans |
Country Status (7)
Country | Link |
---|---|
JP (1) | JP6028884B1 (en) |
KR (1) | KR101994914B1 (en) |
CN (1) | CN107429360B (en) |
CO (1) | CO2017009718A2 (en) |
MY (1) | MY173780A (en) |
TW (1) | TWI617677B (en) |
WO (1) | WO2016157878A1 (en) |
Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2018059196A (en) * | 2016-10-04 | 2018-04-12 | Jfeスチール株式会社 | High strength ultrathin steel sheet and manufacturing method therefor |
WO2019088044A1 (en) * | 2017-10-31 | 2019-05-09 | Jfeスチール株式会社 | High-strength steel sheet and method for producing same |
WO2020261965A1 (en) * | 2019-06-24 | 2020-12-30 | Jfeスチール株式会社 | Steel sheet for can, and method for manufacturing same |
CN113242909A (en) * | 2018-12-20 | 2021-08-10 | 杰富意钢铁株式会社 | Steel sheet for can and method for producing same |
JPWO2021167023A1 (en) * | 2020-02-21 | 2021-08-26 | ||
CN113748220A (en) * | 2019-03-29 | 2021-12-03 | 杰富意钢铁株式会社 | Steel sheet for can and method for producing same |
EP3845678A4 (en) * | 2018-08-30 | 2022-01-19 | JFE Steel Corporation | Steel sheet for can, and method for producing same |
Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2005350737A (en) * | 2004-06-11 | 2005-12-22 | Nippon Steel Corp | Thin steel sheet for can provided with strong can body strength and press workability and its production method |
JP2008214658A (en) * | 2007-02-28 | 2008-09-18 | Jfe Steel Kk | Steel sheet for can, hot rolled steel sheet used for base material therefor, and their manufacturing method |
JP2009007607A (en) * | 2007-06-27 | 2009-01-15 | Nippon Steel Corp | Steel sheet for extrathin vessel |
JP2013028842A (en) * | 2011-07-29 | 2013-02-07 | Jfe Steel Corp | Steel plate for high strength high workability can and method for manufacturing the same |
Family Cites Families (15)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH08246060A (en) * | 1995-03-10 | 1996-09-24 | Kawasaki Steel Corp | Production of steel sheet for can |
JPH08325670A (en) | 1995-03-29 | 1996-12-10 | Kawasaki Steel Corp | Steel sheet for can making excellent in deep drawability and flanging workability at the time of can making and surface property after can making and having sufficient can strength and its production |
JP3769914B2 (en) | 1998-01-06 | 2006-04-26 | Jfeスチール株式会社 | Steel plate for cans with excellent aging resistance and bake hardenability |
JP4051778B2 (en) | 1998-10-08 | 2008-02-27 | Jfeスチール株式会社 | Steel plate for cans suitable for 3-piece cans with good surface properties |
JP4244486B2 (en) | 1999-08-05 | 2009-03-25 | Jfeスチール株式会社 | Steel plate for high-strength can and manufacturing method thereof |
JP3887009B2 (en) | 2002-12-05 | 2007-02-28 | 東洋鋼鈑株式会社 | Steel plate for thinned deep-drawn ironing can and manufacturing method thereof |
JP5526483B2 (en) * | 2008-03-19 | 2014-06-18 | Jfeスチール株式会社 | Steel plate for high-strength can and manufacturing method thereof |
CN101983251A (en) * | 2008-04-03 | 2011-03-02 | 杰富意钢铁株式会社 | High-strength steel plate for a can and method for manufacturing said high-strength steel plate |
EP2395120B1 (en) * | 2009-01-30 | 2015-07-15 | JFE Steel Corporation | Corrosion resistant steel for crude oil tank, manufacturing method therefor, and crude oil tank |
CN103014483B (en) * | 2011-09-26 | 2015-12-02 | 宝山钢铁股份有限公司 | The secondary cold-rolling plate of high extension and manufacture method thereof |
MY185149A (en) * | 2012-04-06 | 2021-04-30 | Jfe Steel Corp | High strength and high formability steel sheet and manufacturing method thereof |
KR101645840B1 (en) * | 2012-06-06 | 2016-08-04 | 제이에프이 스틸 가부시키가이샤 | Three-piece can and method for producing same |
KR101989712B1 (en) * | 2014-10-28 | 2019-06-14 | 제이에프이 스틸 가부시키가이샤 | Steel sheet for two-piece can and manufacturing method therefor |
EP3187612B1 (en) * | 2014-11-12 | 2019-06-19 | JFE Steel Corporation | Steel sheet for cans and method for manufacturing steel sheet for cans |
CN107406944B (en) * | 2015-03-27 | 2019-05-10 | 杰富意钢铁株式会社 | Steel plate for tanks and its manufacturing method |
-
2016
- 2016-03-28 WO PCT/JP2016/001774 patent/WO2016157878A1/en active Application Filing
- 2016-03-28 KR KR1020177027622A patent/KR101994914B1/en active IP Right Grant
- 2016-03-28 JP JP2016544875A patent/JP6028884B1/en active Active
- 2016-03-28 CN CN201680019401.9A patent/CN107429360B/en active Active
- 2016-03-28 MY MYPI2017703401A patent/MY173780A/en unknown
- 2016-03-31 TW TW105110311A patent/TWI617677B/en active
-
2017
- 2017-09-27 CO CONC2017/0009718A patent/CO2017009718A2/en unknown
Patent Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2005350737A (en) * | 2004-06-11 | 2005-12-22 | Nippon Steel Corp | Thin steel sheet for can provided with strong can body strength and press workability and its production method |
JP2008214658A (en) * | 2007-02-28 | 2008-09-18 | Jfe Steel Kk | Steel sheet for can, hot rolled steel sheet used for base material therefor, and their manufacturing method |
JP2009007607A (en) * | 2007-06-27 | 2009-01-15 | Nippon Steel Corp | Steel sheet for extrathin vessel |
JP2013028842A (en) * | 2011-07-29 | 2013-02-07 | Jfe Steel Corp | Steel plate for high strength high workability can and method for manufacturing the same |
Cited By (16)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2018059196A (en) * | 2016-10-04 | 2018-04-12 | Jfeスチール株式会社 | High strength ultrathin steel sheet and manufacturing method therefor |
WO2019088044A1 (en) * | 2017-10-31 | 2019-05-09 | Jfeスチール株式会社 | High-strength steel sheet and method for producing same |
JP6569840B1 (en) * | 2017-10-31 | 2019-09-04 | Jfeスチール株式会社 | High strength steel plate and manufacturing method thereof |
TWI672383B (en) * | 2017-10-31 | 2019-09-21 | 日商杰富意鋼鐵股份有限公司 | High-strength steel plate and manufacturing method thereof |
US11913087B2 (en) | 2017-10-31 | 2024-02-27 | Jfe Steel Corporation | High-strength steel sheet and method for producing same |
EP3845678A4 (en) * | 2018-08-30 | 2022-01-19 | JFE Steel Corporation | Steel sheet for can, and method for producing same |
EP3901300A4 (en) * | 2018-12-20 | 2022-04-27 | JFE Steel Corporation | Steel plate for can and method for producing same |
CN115821158B (en) * | 2018-12-20 | 2024-08-20 | 杰富意钢铁株式会社 | Steel sheet for cans and method for producing same |
CN113242909A (en) * | 2018-12-20 | 2021-08-10 | 杰富意钢铁株式会社 | Steel sheet for can and method for producing same |
CN115821158A (en) * | 2018-12-20 | 2023-03-21 | 杰富意钢铁株式会社 | Steel sheet for can and method for producing same |
CN113748220A (en) * | 2019-03-29 | 2021-12-03 | 杰富意钢铁株式会社 | Steel sheet for can and method for producing same |
WO2020261965A1 (en) * | 2019-06-24 | 2020-12-30 | Jfeスチール株式会社 | Steel sheet for can, and method for manufacturing same |
JP6881696B1 (en) * | 2019-06-24 | 2021-06-02 | Jfeスチール株式会社 | Steel sheet for cans and its manufacturing method |
JP7014341B2 (en) | 2020-02-21 | 2022-02-01 | Jfeスチール株式会社 | Steel plate and steel plate manufacturing method |
WO2021167023A1 (en) * | 2020-02-21 | 2021-08-26 | Jfeスチール株式会社 | Sheet steel and method for manufacturing sheet steel |
JPWO2021167023A1 (en) * | 2020-02-21 | 2021-08-26 |
Also Published As
Publication number | Publication date |
---|---|
JPWO2016157878A1 (en) | 2017-04-27 |
KR20170121277A (en) | 2017-11-01 |
CN107429360B (en) | 2019-06-25 |
CN107429360A (en) | 2017-12-01 |
KR101994914B1 (en) | 2019-07-01 |
MY173780A (en) | 2020-02-20 |
TW201702404A (en) | 2017-01-16 |
CO2017009718A2 (en) | 2018-02-28 |
JP6028884B1 (en) | 2016-11-24 |
TWI617677B (en) | 2018-03-11 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP6028884B1 (en) | Steel plate for cans and method for producing steel plate for cans | |
JP5135868B2 (en) | Steel plate for can and manufacturing method thereof | |
JP5712479B2 (en) | Steel plate for cans excellent in rough skin resistance and method for producing the same | |
TWI643964B (en) | Two-piece can steel plate and manufacturing method thereof | |
JP2009263789A (en) | High strength steel sheet for vessel, and method for producing the same | |
JP5939368B1 (en) | Steel plate for can and manufacturing method thereof | |
JP6540769B2 (en) | High strength ultra thin steel plate and method of manufacturing the same | |
JP2010150571A (en) | Method for manufacturing steel sheet for can-making | |
TWI721696B (en) | Steel plate for tank and manufacturing method thereof | |
JP6699310B2 (en) | Cold rolled steel sheet for squeezer and method for manufacturing the same | |
JP6191807B1 (en) | Steel plate for can and manufacturing method thereof | |
JP6421773B2 (en) | Steel plate for can and manufacturing method thereof | |
JP2005350737A (en) | Thin steel sheet for can provided with strong can body strength and press workability and its production method | |
JP6361553B2 (en) | Steel plate for high workability and high strength can and manufacturing method thereof | |
JP6881696B1 (en) | Steel sheet for cans and its manufacturing method |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
ENP | Entry into the national phase |
Ref document number: 2016544875 Country of ref document: JP Kind code of ref document: A |
|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 16771766 Country of ref document: EP Kind code of ref document: A1 |
|
WWE | Wipo information: entry into national phase |
Ref document number: NC2017/0009718 Country of ref document: CO |
|
ENP | Entry into the national phase |
Ref document number: 20177027622 Country of ref document: KR Kind code of ref document: A |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
122 | Ep: pct application non-entry in european phase |
Ref document number: 16771766 Country of ref document: EP Kind code of ref document: A1 |