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WO2016031234A1 - Tôle d'acier pour canettes et son procédé de production - Google Patents

Tôle d'acier pour canettes et son procédé de production Download PDF

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Publication number
WO2016031234A1
WO2016031234A1 PCT/JP2015/004269 JP2015004269W WO2016031234A1 WO 2016031234 A1 WO2016031234 A1 WO 2016031234A1 JP 2015004269 W JP2015004269 W JP 2015004269W WO 2016031234 A1 WO2016031234 A1 WO 2016031234A1
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WO
WIPO (PCT)
Prior art keywords
less
cans
strength
amount
rolling
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/JP2015/004269
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English (en)
Japanese (ja)
Inventor
多田　雅毅
克己 小島
裕樹 中丸
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
JFE Steel Corp
Original Assignee
JFE Steel Corp
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by JFE Steel Corp filed Critical JFE Steel Corp
Priority to CN201580045669.5A priority Critical patent/CN106605006B/zh
Priority to MYPI2017700598A priority patent/MY177004A/en
Priority to KR1020177005192A priority patent/KR101923839B1/ko
Priority to JP2016501260A priority patent/JP5939368B1/ja
Publication of WO2016031234A1 publication Critical patent/WO2016031234A1/fr
Priority to PH12017500200A priority patent/PH12017500200A1/en
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0268—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
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations
    • 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 a can used as a raw material for a three-piece can formed by high-working can body processing, a two-piece can that requires pressure strength, and a method for manufacturing the same.
  • the present invention relates to a steel plate for cans having a large total elongation and excellent upper yield strength, and a method for producing the same.
  • Measures to reduce can manufacturing costs include cost reduction of materials.
  • 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 sheet manufactured using the DR method has a high strength but a small total elongation.
  • a DR material with poor ductility as a material for a can formed by can body processing with a strong working degree such as a deformed can that has recently been put on the market.
  • the DR material has a higher manufacturing cost because the number of manufacturing steps is increased as compared with a steel sheet that is subjected to temper rolling after normal annealing.
  • Patent Document 1 in mass%, C: 0.02% or less, Si: 0.10% or less, Mn: 1.5% or less, P: 0.20% or less, S: 0.01% or less, Al: 0.01% or less, N: 0.0050 to 0.0250%, and (Solution C + Solution N) 0.0050% or more, with the balance being Fe and inevitable impurities , Having a structure having a recrystallization rate of 90% or more, bake hardening amount (BH amount): 100 MPa or more, increase amount of tensile strength by paint baking treatment ⁇ TS: 30 MPa or more, yield stress after painting / baking treatment: An ultra-thin cold-rolled steel sheet for high-strength cans having a sheet thickness of 0.3 mm or less, characterized by having 550 MPa or more is disclosed.
  • BH amount bake hardening amount
  • ⁇ TS increase amount of tensile strength by paint baking treatment
  • ⁇ TS 30 MPa or more
  • yield stress after painting / baking treatment An ultra
  • Patent Document 1 adjusts hot rolling conditions and cooling conditions, rapidly cools to a low temperature range after continuous annealing, and effectively uses the effect of solid solution C amount + solid solution N amount to use the age hardening phenomenon. By doing so, a technique for obtaining a steel plate for a high-strength can similar to a DR material has been proposed.
  • 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 by weight ratio, C: 0.020 to 0.150%, Si: 0.05% or less, Mn: 1.00% or less, P: 0.050% or less, S: 0.010 %, N: 0.0100% or less, Al: 0.100% or less, Nb: 0.005 to 0.025%, and the balance consists of inevitable impurities and iron, and a substantial ferrite single phase structure
  • the yield strength is 40 kgf / mm 2 or more
  • the average crystal grain size is 10 ⁇ m or less
  • the plate thickness is 0.300 mm or less.
  • Patent Document 2 proposes a steel plate having a balance between strength and ductility by combining precipitation strengthening with Nb carbide and refinement strengthening with Nb, Ti, and B carbonitrides.
  • Patent Document 3 C: 0.001 to 0.010 wt%, Si: ⁇ 0.05 wt%, Mn: ⁇ 0.9 wt%, P: 0.131 to 0.200 wt%, S: ⁇ 0.04 wt%, Al: 0.
  • a steel plate for a thinned deep-drawn ironing can characterized by comprising a low-carbon steel plate containing 006 to 0.08 wt%, N: 0.0010 to 0.015 wt%, the balance Fe and inevitable impurities.
  • a method of increasing the strength by using solid solution strengthening such as Mn, P, and N has been proposed.
  • the above-described conventional technology can produce a steel sheet that satisfies any of the strength, ductility (total elongation), and corrosion resistance, but cannot produce a steel sheet that satisfies all of the above characteristics.
  • Patent Document 1 Although the method described in Patent Document 1 is an effective method for increasing the strength, since the amount of solute C and solute N in the steel is large, the yield elongation increases. Yield elongation occurs because solute C or solute N adheres to dislocations, thereby reducing movable dislocations. In a strain region where the yield elongation is large, a local yield phenomenon occurs, causing uneven deformation, and thus wrinkles called stretcher strains may occur, thereby impairing the appearance.
  • Patent Document 2 high strength is realized by precipitation strengthening, and steel with a balance between strength and ductility is proposed, but yield elongation is not taken into consideration, and the manufacturing method described in Patent Document 2 is The yield elongation value targeted by the invention cannot be obtained.
  • Patent Document 3 proposes high strength by solid solution strengthening.
  • P and Mn which are generally known as elements that inhibit corrosion resistance, are added in excess, there is a high risk of inhibiting corrosion resistance.
  • the present invention has been made in view of such circumstances, and has an upper yield strength of 450 to 600 MPa after coating and baking, a total elongation of 13% or more, and good corrosion resistance even for highly corrosive contents.
  • An object of the present invention is to provide a steel sheet for cans with high workability and high strength and a method for producing the same.
  • the present inventors have conducted intensive research to solve the above problems. As a result, the following knowledge was obtained.
  • the balance between precipitation strengthening and solid solution strengthening can increase the strength without impairing the elongation.
  • the reduction rate in the secondary cold rolling is set to 1 to 19%, and the work strength at a reduction rate lower than that in the conventional secondary cold rolling can enhance the strength without reducing the total elongation.
  • composition of the original plate with the element addition amount in a range that does not affect the corrosion resistance, it shows good corrosion resistance even for highly corrosive contents.
  • the present invention has completed the high-workability and high-strength steel plate and its manufacturing method by comprehensively managing the components and the manufacturing method based on the above findings.
  • the present invention has been made based on the above findings, and the gist thereof is as follows.
  • a high workability high strength steel sheet having an upper yield strength of 450 to 630 MPa and a total elongation of 13% or more can be obtained. More specifically, in the present invention, precipitation strengthening by Nb, solid solution strengthening by N, and work strengthening by performing secondary cold rolling at a low pressure reduction rate of 1 to 19% after annealing are harmful to other characteristics. Strengthening the composite without increasing the strength. As a result, the final yield is 450 to 630 MPa in the final product while the total elongation is 13% or more.
  • the present invention by increasing the strength of the original plate, it is possible to ensure high strength of the can even if the welded can is made thinner (thinned). Even if the high workability high strength steel sheet of the present invention is applied to a two-piece can application that requires the pressure resistance of the bottom portion, it is possible to obtain a high pressure resistance with the current gauge. In addition, by increasing 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 sheet for high workability and high strength can of the present invention is excellent in any of strength, workability and corrosion resistance.
  • the steel sheet for high workability and high strength can of the present invention has an excellent yield resistance with an upper yield strength (hereinafter sometimes referred to as U-YP) of 450 to 630 MPa and a total elongation of 13% or more. Moreover, in the high workability high strength steel plate for cans of the present invention, aging can be reduced.
  • U-YP upper yield strength
  • Nb is added as a precipitation strengthening element
  • N is added as a solid solution strengthening element
  • the upper yield strength is increased by work strengthening by performing secondary cold rolling with a rolling reduction of 1 to 19% after annealing. It can be made into a range. Furthermore, if the upper yield strength is increased by the above-described method in a specific component system, the total elongation is also high. Having excellent upper yield strength and high overall elongation is a feature of the present invention and is the most important requirement.
  • the upper yield strength is 450 to 630 MPa, A steel with high workability and high strength cans having an elongation of 13% or more is obtained.
  • the steel sheet for high workability and high strength can of the present invention is in mass%, C: more than 0.020% and 0.130% or less, Si: 0.04% or less, Mn: 0.10 to 1.20%, P : 0.100% or less, S: 0.030% or less, Al: 0.10% or less, N: more than 0.0120% and 0.020% or less, Nb: 0.004 to 0.040%,
  • the balance has a composition composed of iron and inevitable impurities.
  • % in the description of the component composition means “% by mass”.
  • the upper yield strength (450 to 630 MPa) is not less than a predetermined value after continuous annealing and at the same time the total elongation is 13% or more. It is.
  • the C content of the steel plate for cans is important. Specifically, the C content needs to exceed 0.020%.
  • the C content exceeds 0.040%, the strength of the hot-rolled sheet increases and the deformation resistance during cold rolling increases, so that surface defects may easily occur after rolling. Moreover, in order to reduce this defect, it is necessary to make rolling speed small.
  • the C content is preferably 0.070% or more.
  • 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%.
  • the C content is preferably more than 0.020% to 0.040% from the viewpoint of ease of manufacture.
  • Si 0.04% or less Si is an element that increases the strength of steel 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. In the present invention, since the upper yield strength is increased 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.
  • Mn 0.10 to 1.20% Mn increases the strength of the steel by solid solution strengthening and also reduces the ferrite average crystal 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%. On the other hand, if the Mn content exceeds 1.20%, the corrosion resistance and surface characteristics are inferior. Therefore, the upper limit of the Mn content is 1.20%.
  • P 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 steel plate for high workability and high strength cans of the present invention may not contain S, it is preferable to set S to 0.030% or less when implementing this patent. . Since the steel plate for cans of the present invention has a high Nb, C, and N content, the slab edge tends to break in the straightening zone during continuous casting. From the viewpoint of preventing slab cracking, the S content is preferably 0.030% or less. Preferably, the S content is 0.020% or less. More preferably, the S content is 0.010% or less.
  • Al 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. Therefore, the Al content is set to 0.10% or less. 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.
  • the N content is 0.020% or less.
  • the N content needs to be over 0.0120%.
  • Nb 0.004 to 0.040%
  • Nb is an important additive element in the present invention.
  • Nb is an element having a high carbide generating ability and precipitates fine carbides.
  • the upper yield strength and surface properties can be adjusted by the Nb content. Since this effect occurs when the Nb content is 0.004% or more, the lower limit of the Nb content is limited to 0.004%.
  • Nb increases the recrystallization temperature. Therefore, if the Nb content exceeds 0.040%, non-recrystallization is not achieved in continuous annealing at an annealing temperature of 650 to 780 ° C. and a soaking time of 10 to 55 seconds. It becomes difficult to anneal, such as remaining part. For this reason, the upper limit of Nb content is limited to 0.040%.
  • the Nb content is preferably 0.004 to 0.020% from the viewpoint of suppressing an increase in deformation resistance during cold rolling.
  • the remainder other than the above essential components and optional components is Fe and inevitable impurities.
  • the structure of the steel sheet for cans of the present invention is a ferrite single-phase structure.
  • the average ferrite grain size affects not only the upper yield strength but also the surface properties during drawing. If the ferrite average crystal grain size of the final product exceeds 7.0 ⁇ m, after the drawing process, a rough skin phenomenon occurs in part and the beauty of the surface appearance is lost. Therefore, the ferrite average crystal grain size is set to 7.0 ⁇ m or less.
  • the element that forms fine precipitates that suppress the grain growth of ferrite crystals by reducing the soaking temperature during continuous annealing or pin the grain boundary migration.
  • the ferrite average crystal grain size is preferably 5.0 ⁇ m or more because the production cost is increased because it is necessary to add a large amount of.
  • the ferrite average crystal grain size may be in the above range after coating baking, but since the ferrite average crystal grain size does not change before and after the coating baking process, it may be measured either before or after the coating baking process.
  • the coating baking process is a process corresponding to heating during coating baking and laminating, and specifically refers to heat treatment in the range of 170 to 265 ° C. for 12 seconds to 30 minutes. In the examples described later, heat treatment is performed at 210 ° C. for 20 minutes as a standard condition.
  • the ferrite average crystal grain size is controlled by the component composition, the cold rolling reduction ratio, and the annealing temperature. Specifically, the ferrite average crystal grain size of 7.0 ⁇ m or less can be obtained by adopting the above component composition and adopting the production conditions described later. Increasing the soaking temperature in continuous annealing increases the average ferrite grain size, and decreasing the soaking temperature decreases the average ferrite grain size.
  • Precipitation Nb amount / Total Nb amount ⁇ 0.30
  • the ratio of the precipitated Nb amount to the total Nb amount (precipitated Nb amount / total Nb amount) is preferably 0.30 or more, the target upper yield strength of 450 to 630 MPa can be realized while improving the total elongation and corrosion resistance.
  • the amount of precipitated Nb / total Nb amount is preferably 0.9 or less because the particle size of the precipitated Nb becomes coarse when the amount of precipitated Nb increases.
  • the deposited Nb amount / total Nb amount may be within the above range after baking. Since the deposited Nb amount / total Nb amount does not change before and after the paint baking process, it may be measured before or after the paint baking process. Since the paint baking process is the same as described above, the description thereof is omitted.
  • the amount of precipitated Nb can be increased by increasing the soaking temperature during continuous annealing.
  • Average particle size of Nb precipitates 20 nm or less
  • the average particle size of Nb precipitates is set to 20 nm or less.
  • the value measured by the method as described in an Example is employ
  • the Nb precipitate average particle diameter may be within the above range after the coating baking. Since the average particle size of Nb precipitates does not change before and after the paint baking process, it may be measured before or after the paint baking process. Since the paint baking process is the same as described above, the description thereof is omitted.
  • the soaking time of continuous annealing may be shortened to suppress the growth of Nb precipitates.
  • the ratio of the volume ratio means that the ratio of the volume ratio is in the above range after baking. Since the paint baking process is the same as described above, the description thereof is omitted.
  • the volume ratio of Nb precipitates in the region from the surface to the 1 / 8th depth position in the plate thickness direction can be obtained by, for example, lowering the temperature of the final finish rolling in hot rolling to roughen the surface layer, If adjusted by a method of promoting Nb precipitation, the value becomes large, and if the temperature of the final finish rolling is increased to refine the surface layer and suppress Nb precipitation in the crystal grains of the surface layer, the value becomes small.
  • the volume fraction of Nb precipitates in the region from the 3/8 depth position to the 4/8 depth position from the surface becomes large if, for example, the Nb precipitate is grown by increasing the coiling temperature of hot rolling.
  • the coiling temperature of hot rolling is lowered to suppress the growth of Nb precipitates, the value becomes small.
  • Upper yield strength 450-630MPa
  • the upper yield strength is set to 450 MPa or more in order to ensure the paneling strength and dent strength of the welded can and the pressure strength of the two-piece can.
  • the upper yield strength is 630 MPa or less.
  • the upper yield strength can be controlled to a target value by employing the above component composition and employing the manufacturing conditions described later. In the present invention, it means that the upper yield strength is in the above range after baking. Since the paint baking process is the same as described above, the description thereof is omitted.
  • Total elongation 13% or more
  • the total elongation is controlled to a target value by setting the component composition in a specific range and setting the rolling reduction ratio of secondary cold rolling after annealing in a specific range.
  • the total elongation after baking is in the above range. Since the paint baking process is the same as described above, the description thereof is omitted.
  • the total elongation is usually 35% or less.
  • the steel plate for cans of this invention is manufactured by the method which has a hot rolling process, a primary cold rolling process, an annealing process, and a secondary cold rolling process.
  • a hot rolling process a hot rolling process
  • a primary cold rolling process a primary cold rolling process
  • an annealing process a secondary cold rolling process
  • Hot rolling process is a process in which steel (for example, slab) is hot-rolled under conditions where the finishing temperature is Ar3 transformation point or higher and 990 ° C or lower, and the winding temperature is 400 ° C or higher and lower than 600 ° C. This is a winding process.
  • the steel used as a raw material will be described. Steel is obtained by melting molten steel adjusted to the above-described component composition by a generally known melting method using a converter or the like, and then using a casting method such as a continuous casting method as a rolling material. It is done.
  • the rolling material means steel as a raw material.
  • the hot rolled sheet is manufactured by subjecting the rolled material obtained as described above to hot rolling.
  • the temperature of the rolled material is preferably set to 1230 ° C. or higher.
  • the finishing temperature in the hot rolling is not less than the Ar3 transformation point.
  • the finish rolling temperature in hot rolling is an important factor in securing the upper yield strength.
  • the hot rolling finishing temperature is limited to the Ar3 transformation point or higher.
  • the finish rolling temperature is higher than 990 ° C., the total elongation is insufficient and the formability deteriorates.
  • the finish rolling temperature is 990 ° C. as the upper limit.
  • the coiling temperature in the hot rolling process is an important factor in controlling the upper yield strength and the total elongation, which are important in the present invention, to the target values.
  • the coiling temperature is set to 600 ° C. or higher, N added for solid solution strengthening is precipitated as AlN, so that the amount of solid solution N decreases, and as a result, the upper yield strength decreases. For this reason, the coiling temperature was set to less than 600 ° C. Further, when the winding temperature is less than 400 ° C., the total elongation is lowered and the moldability is deteriorated, so the winding temperature is set to 400 ° C. or more.
  • the cooling rate after winding is preferably slow cooling, preferably cooling at 11.5 ° C./hour or less, and further cooling at 6.3 ° C./hour or less.
  • cooling at 1.7 ° C./hour or less is more preferable.
  • the primary cold rolling step is a step of pickling a steel plate (hot-rolled plate) after the hot rolling step and rolling under a condition where the rolling reduction is 80% or more.
  • Pickling is not particularly limited as long as the surface scale can be removed. Pickling can be performed by a commonly performed method.
  • the rolling reduction in primary cold rolling is one of the important conditions in the present invention. If the rolling reduction in primary cold rolling is less than 80%, it is difficult to produce a steel sheet having an upper yield strength of 450 MPa or more. Further, when the reduction ratio in this step is less than 80%, at least the thickness of the hot-rolled plate needs to be 1 mm or less in order to obtain a plate thickness (about 0.17 mm) comparable to that of the DR material. However, in operation, it is difficult to set the thickness of the hot-rolled sheet to 1 mm or less. Therefore, the rolling reduction in this step is 80% or more.
  • An annealing step is a step in which a steel plate (cold rolled plate) is continuously annealed after the primary cold rolling step under conditions of a soaking temperature of 650 to 780 ° C. and a soaking time of 10 s to 55 s.
  • the soaking temperature needs to be equal to or higher than the recrystallization temperature of the steel sheet in order to ensure good workability, and in order to make the structure more uniform and ensure the total elongation, the soaking temperature is 650 ° C. or more. Limited to.
  • the soaking temperature exceeds 780 ° C., the ferrite crystal grain size is increased, the upper yield strength is lowered, and the pressure resistance is insufficient.
  • the soaking temperature is set to a range of 650 to 780 ° C.
  • the soaking time is 55 s or less.
  • the soaking time is 10 s or more.
  • the secondary cold rolling step is a step of rolling the steel plate (annealed plate) under the condition of a rolling reduction of 1 to 19% after the annealing step.
  • the rolling reduction in the secondary cold rolling after annealing is made the same as the normal DR material manufacturing conditions, so the strain introduced at the time of processing increases, so the total elongation decreases.
  • the reduction ratio in the secondary cold rolling is set to 19% or less.
  • the rolling reduction of the secondary cold rolling needs to be 1% or more because the unevenness of the roll is transferred to the steel sheet.
  • the rolling reduction in secondary cold rolling is preferably 4 to 12% from the viewpoint of preventing slippage of the steel sheet and roll during rolling and ensuring the total elongation.
  • the plated steel plate obtained above is subjected to a heat treatment corresponding to a coating baking process at 210 ° C. for 20 minutes, and then subjected to a tensile test to measure the upper yield strength and the total elongation.
  • the texture and average crystal grain size were also investigated.
  • the survey method is as follows.
  • the tensile test was performed using a JIS No. 5 size tensile test piece, and the upper yield strength (U-YP) and total elongation (El) were measured to evaluate the strength, ductility and aging. Aging was evaluated by the yield elongation that contributes to the generation of stretcher strain during processing. If the yield elongation is 4% or less, the occurrence of stretcher strain during processing can be suppressed. The obtained results are shown in Table 3.
  • the crystal structure was observed with an optical microscope by polishing the sample, corroding the crystal grain boundary with nital.
  • the ferrite average crystal grain size was measured using the cutting method of JIS G5503 for the crystal structure observed as described above. The obtained results are shown in Table 3.
  • the amount of precipitated Nb was 10% acetylacetone-1% tetramethylammonium chloride-methanol solution, electrolytically extracted and then dissolved in acid, and Nb was quantified by ICP measurement. The total Nb amount was measured by ICP after directly dissolving the sample in acid. Moreover, the Nb precipitate average particle diameter was measured by TEM. The obtained results are shown in Table 3.
  • a 0.26mm thick plate (plated steel plate) is molded into a 63mm ⁇ lid, and then wrapped around a 63mm ⁇ welded can body, compressed air is introduced into the can, and the can lid is deformed.
  • the pressure when measured was measured.
  • the case where the can lid was not deformed even when the internal pressure was 0.20 MPa was designated as “ ⁇ ”, and the case where the can lid was deformed at less than 0.20 MPa was designated as “x”.
  • Table 4 The results are shown in Table 4.
  • the example of the present invention has an average crystal grain size of 7.0 ⁇ m or less and a fine ferrite structure, and therefore has a high upper yield strength and is excellent in both strength and ductility. Moreover, in this invention, since it is adjusted to the component composition in Table 1, corrosion resistance is also excellent.
  • any of the conditions in the claims of the present application is out of order, so that the desired characteristics of the present application cannot be obtained.
  • a steel sheet having excellent strength, ductility, and corrosion resistance can be obtained, a three-piece can with a high degree of processing can body processing, and a two-piece can with a bottom portion of several percent processed. It is most suitable as a steel plate for cans.

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

Abstract

Cette invention concerne : une tôle d'acier à haute résistance hautement usinable pour des canettes, qui a une limite élastique supérieure de 450 à 600 MPa après cuisson de son revêtement, une caractéristique d'allongement total supérieure ou égale à 13 % et une bonne résistance à la corrosion d'un contenu même hautement corrosif ; et un procédé de fabrication de cette dernière. La tôle d'acier à haute résistance hautement usinable pour des canettes est caractérisée en ce qu'elle a une composition des constituants comprenant, en % en masse, plus de 0,020 % et jusqu'à 0,130 % de C, 0,04 % ou moins de Si, 0,10 à 1,20 % de Mn, 0,100 % ou moins de P, 0,030 % ou moins de S, 0,10 % ou moins d'Al, plus de 0,0120 % et jusqu'à 0,020 % de N et 0,004 à 0,040 % de Nb, le reste comprenant du fer et des impuretés inévitables. La tôle d'acier à haute résistance hautement usinable pour des canettes est en outre caractérisée en ce que : le rapport d'une quantité de Nb précipité à une quantité totale de Nb représenté par (quantité de Nb précipité)/(quantité totale de Nb) est ≥ 0,30 ; la taille moyenne des particules de Nb précipité est inférieure ou égale à 20 nm ; la taille moyenne de grains de ferrite est inférieure ou égale à 7,0 µm ; la limite élastique supérieure après cuisson de son revêtement est de 450 à 630 MPa ; et l'allongement total est supérieur ou égal à 13 %.
PCT/JP2015/004269 2014-08-29 2015-08-25 Tôle d'acier pour canettes et son procédé de production Ceased WO2016031234A1 (fr)

Priority Applications (5)

Application Number Priority Date Filing Date Title
CN201580045669.5A CN106605006B (zh) 2014-08-29 2015-08-25 罐用钢板及其制造方法
MYPI2017700598A MY177004A (en) 2014-08-29 2015-08-25 Steel sheets for cans and methods for manufacturing the same
KR1020177005192A KR101923839B1 (ko) 2014-08-29 2015-08-25 캔용 강판 및 그 제조 방법
JP2016501260A JP5939368B1 (ja) 2014-08-29 2015-08-25 缶用鋼板及びその製造方法
PH12017500200A PH12017500200A1 (en) 2014-08-29 2017-02-02 Steel sheets for cans and methods for manufacturing the same

Applications Claiming Priority (2)

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JP2014175303 2014-08-29
JP2014-175303 2014-08-29

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WO2016031234A1 true WO2016031234A1 (fr) 2016-03-03

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KR (1) KR101923839B1 (fr)
CN (1) CN106605006B (fr)
MY (1) MY177004A (fr)
PH (1) PH12017500200A1 (fr)
TW (1) TWI593811B (fr)
WO (1) WO2016031234A1 (fr)

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JP2018059196A (ja) * 2016-10-04 2018-04-12 Ｊｆｅスチール株式会社 高強度極薄鋼板およびその製造方法
CN110494581A (zh) * 2017-03-27 2019-11-22 杰富意钢铁株式会社 两片罐用钢板及其制造方法
WO2020045449A1 (fr) * 2018-08-30 2020-03-05 Ｊｆｅスチール株式会社 Tôle d'acier de canette et son procédé de production
CN113166835A (zh) * 2018-11-21 2021-07-23 杰富意钢铁株式会社 罐用钢板及其制造方法
EP3875611A1 (fr) * 2020-03-06 2021-09-08 ThyssenKrupp Rasselstein GmbH Produit en acier laminé à froid pour emballages

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KR102533809B1 (ko) 2018-12-20 2023-05-17 제이에프이 스틸 가부시키가이샤 캔용 강판 및 그 제조 방법
CN119061330B (zh) * 2024-08-27 2025-03-14 重庆数元道科技有限公司 基于高碳设计的低碳基体2000MPa抗氢脆热成形钢及其制备方法

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JPH0734194A (ja) * 1993-07-14 1995-02-03 Toyo Kohan Co Ltd 薄肉化深絞り缶用途に適した鋼板およびその製造法
JPH08325670A (ja) * 1995-03-29 1996-12-10 Kawasaki Steel Corp 製缶時の深絞り性及びフランジ加工性と、製缶後の表面性状とに優れ、十分な缶強度を有する製缶用鋼板及びその製造方法
WO2005103316A1 (fr) * 2004-04-27 2005-11-03 Jfe Steel Corporation Feuille d'acier pour boîte et sa méthode de production
WO2008105524A1 (fr) * 2007-02-28 2008-09-04 Jfe Steel Corporation Tôle d'acier pour boîtes de conserve, tôle d'acier laminé à chaud à utiliser comme métal de base et procédés de fabrication des deux types de tôle
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Publication number Priority date Publication date Assignee Title
JP2018059196A (ja) * 2016-10-04 2018-04-12 Ｊｆｅスチール株式会社 高強度極薄鋼板およびその製造方法
CN110494581A (zh) * 2017-03-27 2019-11-22 杰富意钢铁株式会社 两片罐用钢板及其制造方法
CN110494581B (zh) * 2017-03-27 2021-07-09 杰富意钢铁株式会社 两片罐用钢板及其制造方法
US11486018B2 (en) 2017-03-27 2022-11-01 Jfe Steel Corporation Steel sheet for two-piece can and manufacturing method therefor
WO2020045449A1 (fr) * 2018-08-30 2020-03-05 Ｊｆｅスチール株式会社 Tôle d'acier de canette et son procédé de production
JPWO2020045449A1 (ja) * 2018-08-30 2020-09-03 Ｊｆｅスチール株式会社 缶用鋼板およびその製造方法
CN113166835A (zh) * 2018-11-21 2021-07-23 杰富意钢铁株式会社 罐用钢板及其制造方法
CN113166835B (zh) * 2018-11-21 2023-08-18 杰富意钢铁株式会社 罐用钢板及其制造方法
EP3875611A1 (fr) * 2020-03-06 2021-09-08 ThyssenKrupp Rasselstein GmbH Produit en acier laminé à froid pour emballages
WO2021175562A1 (fr) * 2020-03-06 2021-09-10 Thyssenkrupp Rasselstein Gmbh Produit plat en acier laminé à froid pour emballage

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MY177004A (en) 2020-09-01
CN106605006B (zh) 2018-11-06
KR20170029635A (ko) 2017-03-15
CN106605006A (zh) 2017-04-26
TW201610180A (zh) 2016-03-16
KR101923839B1 (ko) 2018-11-29
JPWO2016031234A1 (ja) 2017-04-27
JP5939368B1 (ja) 2016-06-22
PH12017500200B1 (en) 2017-07-10
PH12017500200A1 (en) 2017-07-10
TWI593811B (zh) 2017-08-01

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