WO2008102899A1 - Procédé pour la fabrication de feuilles d'acier pour boîtes métalliques - Google Patents
Procédé pour la fabrication de feuilles d'acier pour boîtes métalliques Download PDFInfo
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- WO2008102899A1 WO2008102899A1 PCT/JP2008/053125 JP2008053125W WO2008102899A1 WO 2008102899 A1 WO2008102899 A1 WO 2008102899A1 JP 2008053125 W JP2008053125 W JP 2008053125W WO 2008102899 A1 WO2008102899 A1 WO 2008102899A1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
- C21D8/0426—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
- C21D8/0436—Cold rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
- C21D8/0473—Final recrystallisation annealing
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
Definitions
- the present invention is a beverage canning (canned beverage) and food container of canned (caniied food) and ⁇ can or container) "I 2-piece DR Di ⁇ r used, two- piece drawn and redrawn can) and 3 arsenide 1
- the present invention relates to a method of manufacturing a tin steel plate for use in a three-piece welded can.
- a steel plate with a thickness of 0.16 mm when a steel plate with a thickness of 0.16 mm is used, at least the body of weld cans has a mouth cwell hardness (HR30T) of about 73 to 77 (at least 73 to 76, preferably 74-77), it is necessary to use a high-strength material with a bow I tensile strength (TS: tensile strength) of about 550 MPa to 620 MPa.
- DR method Double Reduce method
- the steel sheet is manufactured through a process of hot rolling, cold rolling and annealing, and secondary cold rolling.
- the steel sheet obtained by recrystallization annealing has low anisotropy and is suitable for drawn cans where earing should be suppressed as much as possible.
- steel sheets that do not require a small amount of anisotropy do not necessarily require recrystallization annealing after cold rolling.
- heat treatment at a low temperature is performed to relieve strain introduced in the cold rolling process and restore the ductility of the material to the minimum necessary range.
- recovery annealing can be applied instead of recrystallization annealing.
- Patent Document 3 the finishing temperature in hot rolling is set to the Ar3 transformation point or less, and the crystal grain size after hot rolling is reduced to 50 / X.
- the technology described above is disclosed.
- this technology after the above hot rolling, after cold rolling at a reduction rate of 85 to 90%, continuous annealing of 450 to 580 is performed. Steel plates for cans with E 1 (total elongation) force of 6-8% at 57kgf / mm 2 are obtained.
- the material used is Capped 0.05% to 06% Capped steel.
- Patent Document 4 After using copper containing REM as an essential component, the finishing temperature in hot rolling is below the Ar3 transformation point, and cold rolling is performed at a reduction rate of 85% or less.
- the technology for obtaining steel plates for cans with a YS (yield strength) of 640 MPa or more by heat treatment for 10 minutes or more in the range of 200 to 500: is disclosed.
- Japanese Patent Application Laid-Open No. 6-248338 discloses a stretchy yarn having a tempered grade of T 4 to T 6 by annealing at a recrystallization temperature of 400 or more after cold rolling.
- a technique for making a steel plate for containers without a stretcher strain is disclosed.
- a maximum of 72.9 is disclosed as the mouth-kwell hardness (HR30T) obtained with this technology.
- Patent Document 6 copper having the same composition as that of Patent Document 5 (C: 0.03% by weight or less, N: 0.005% by weight or less, etc.) is used at a temperature below the Ar3 transformation point. High-rigidity is achieved by performing hot rolling at least 50% and cold rolling at a reduction rate of 50% or more and then annealing at a recrystallization temperature of 400 or more. The technology to obtain steel plates for containers of the same level as the above is disclosed.
- the recrystallization temperature is defined as the temperature at which the recrystallization rate becomes a structure of less than 10%.
- finish rolling is performed by setting the total reduction ratio below the Ar3 transformation point to 40% or more during hot rolling, and cold rolling is performed at a reduction ratio of 50% or more.
- a technique for obtaining a steel having a YS of 54 to 70 kgf / mm 2 by performing low-temperature annealing at 350 to 6503 ⁇ 4 for a short time after rolling is disclosed. Disclosure of the invention
- Patent Document 3 Patent Document 4, Patent Document 6, and Patent Document 7, it is necessary to perform finish rolling below the Ar3 transformation point during hot rolling.
- the finish rolling is performed below the Ar3 transformation point, the ferrite grain size of the hot rolled steel sheet increases, and after hot rolling as shown in Fig. 3 of Patent Document 3.
- the strength of the steel decreases. Therefore, it is effective as a method of reducing the strength of copper itself to the extent that sufficient workability is ensured.
- finish rolling is performed below the Ar3 transformation point, the temperature in the finish rolling tends to be lower in the widthwise edge portion where the cooling rate is faster than the central portion in the width direction.
- Patent Document 4 the strain is recovered by annealing at 200 to 500 after cold rolling for 10 minutes or more to recover the strain. However, if annealing is performed for 10 minutes or more in a continuous annealing furnace, the line speed is lowered. It must significantly reduce productivity.
- Patent Document 5 and Patent Document 6 are characterized by annealing at 400 mm or more and below the recrystallization temperature, the Rockwell hardness of the obtained steel is less than 73.0, and the intended strength level in the present invention In order to obtain this copper, it is necessary to further lower the annealing temperature. As a result, the annealing temperature employed in the production of normal can materials will be removed, and a dedicated annealing cycle will need to be provided separately, reducing productivity.
- the present invention has been made in view of such circumstances, and an object of the present invention is to solve the above-described problems of the prior art and to propose a method for manufacturing a steel plate for cans with high strength. That is, the present invention is applied to a steel sheet for a can which is applied to a use where a small anisotropy is not required, such as a welded can, and which requires workability in addition to strength.
- An object of the present invention is to propose a method for producing a steel sheet for cans with high strength while ensuring the ductility, for example, the minimum ductility necessary for the flange workability of a welded can.
- Nb 0.001 ⁇ 0.05 ⁇ / ⁇
- ⁇ 0.0001 ⁇ 0.005 ⁇ / at least the o
- the recrystallization start temperature is a temperature at which the rate of change in strength greatly changes with temperature, as shown in Fig. 1 (Example: conditions will be described later). It is defined as the temperature at which a structure in which the recrystallized structure occupies 5% is obtained.
- FIG. 1 is a graph showing the relationship between annealing temperature (horizontal axis:), Ding S (vertical axis: MPa), and recrystallization start temperature in steel having the composition of the present invention.
- FIG. 2 is a graph showing the relationship between annealing temperature (horizontal axis: in), T S (vertical axis: MPa), and recrystallization start temperature in steels of another composition of the present invention.
- the steel plate for cans obtained by the method of the present invention can achieve a tensile strength of 550 to 650 MPa (see FIG. 1) and a total elongation of 5% or more.
- a tensile strength of 550 to 700 MPa see FIG. 2 in the example: conditions are described later
- a total elongation of 4% or more can be achieved.
- hot rolling is performed at a finishing temperature equal to or higher than the A ⁇ 3 transformation point, and a temperature of (recrystallization start temperature 1 200 t) to (recrystallization start temperature 1 20). It is characterized by annealing within the range.
- the component composition of the steel plate for cans of this invention is demonstrated.
- the steel plate for cans proposed in the present invention is intended to increase the strength by strain introduced by cold rolling (primary cold rolling). Therefore, strengthening elements are unnecessary, and they are reduced as much as possible from the viewpoint of ensuring ductility. If C is contained in an amount exceeding 0.003%, the local ductility necessary for molding into a can cannot be obtained sufficiently. Also, the amount of residual solute carbon increases, and there is a risk of cracking during stretch-flange forming of the seeding part, which is the final process of can making. An increase in the amount of solute carbon further increases the amount of work hardening, which may cause wrinkles during neck forming and flange processing. Based on the above, the C content is 0.003% or less.
- the C content is less than 0.0010%, the operability is lowered, for example, the annealing temperature for obtaining the target strength of the present invention is lowered, and the improvement in ductility is also reduced.
- the content is preferably 0.0010% or more.
- N 0.004% or less
- N is an impurity element inevitably mixed in copper.
- the N content increases, slab cracking tends to occur in the unbending zone during continuous casting. N forms precipitates and lowers the elongation, while if it remains in a solid solution, it hardens the steel.
- the N content is 0.004% or less.
- the N content is preferably 0.002% or less.
- Si is a strengthening element that increases the strength of steel by solid solution strengthening. If it is contained in a large amount, corrosion resistance is significantly impaired. Therefore, the Si content is 0.02% or less.
- Mn is a strengthening element that increases the strength of copper by solid solution strengthening. Mn is also an element that reduces the crystal grain size and increases the strength as it is further refined. In order not to cause the above effect, the upper limit of the Mn content is 0.5%. Preferably it is 0.3% or less.
- the lower limit of Mn is 0.05%.
- it is 0.10% or more.
- the P content is large, the strength of the steel is remarkably increased by solid solution strengthening, and the corrosion resistance is also deteriorated. Therefore, the P content is 0.02% or less.
- S exists as an inclusion in steel and is an element that is disadvantageous to the ductility and corrosion resistance of the steel sheet. Preferably it is 0.01% or less.
- A1 improves the cleanliness in steel as a deoxidizer. Also, it combines with solute N to form A1N, and has the effect of reducing the amount of solute N. Therefore, it is preferable to make it contain to some extent in copper. Add about 0.005% or more as the condition It is desirable to do. On the other hand, when the A1 content exceeds 0.1%, the effect of improving the cleanliness is saturated. In addition, problems such as an increase in manufacturing costs and an increased tendency to generate surface defects also arise. Therefore, the A1 content is 0.1% or less.
- Nb 0.001 to 0.05%
- B 0.001% to 0.005% force
- Nb is an element with high carbide-forming ability, and raises the recrystallization temperature of steel by pinning the grain boundary caused by the generated carbide. Therefore, the recrystallization temperature of steel can be changed by adding Nb or changing the amount of Nb added. In other words, the appropriate annealing temperature can be raised and lowered, and the target temperature can be adjusted as needed. As a result, it can be combined with other steel sheets for annealing, which is very efficient in terms of productivity.
- Nb is contained in excess of 0.05%, the recrystallization temperature becomes too high and the processing capability in CAL (continuous annealing line) decreases. Also, it becomes higher than the target strength due to precipitation strengthening of carbides. Therefore, the Nb content is 0.05% or less.
- Nb is preferably added from the viewpoint of annealing temperature, and if it is 0.05% or less, the Nb precipitation strengthening can be used by adjusting the addition amount.
- Nb addition is effective in preventing a decrease in weld strength by suppressing recrystallization during welding.
- a more preferable upper limit is 0.04%.
- Nb addition amount is set as the lower limit. More preferably, 0.005% or more is added. More preferably, it is 0.01% or more.
- B is an element that raises the recrystallization temperature. Therefore, B can be added for the same purpose as Nb. However, excessive addition inhibits recrystallization in the austenite region during hot rolling and increases the rolling load. Therefore, the B addition amount should be 0.005% or less. Preferably it is 0.002% or less. Also, since the effect of increasing the recrystallization temperature cannot be obtained at 0.0001% or less, when adding B for the purpose, 0.0001% is the lower limit. Preferably it is 0.0005% or more. More preferably, it is 0.0008% or more.
- B like Nb, can be made to have the desired strength by precipitation strengthening of B within the above range. It is also effective in preventing the welding strength from decreasing by suppressing recrystallization during welding.
- Nb and B may be added, or both may be added within the above ranges.
- the balance is Fe and inevitable impurities. Thickness: 0.18mm or less
- the plate thickness is an important factor. It is particularly meaningful to reduce the thickness to a tensile strength of 550 MPa or more in the range where the plate thickness is 0 ⁇ 18 mm or less.
- the annealing temperature is set to a recrystallization start temperature of ⁇ 20 ⁇ or less (usually 700 ⁇ : less than or equal to: refer to the examples described later), so even a sheet thickness of 0.18 mm or less can be easily produced. .
- the plate thickness is limited to 0.18 mm or less because the effect is large in the range of tensile strength of 550 MPa or more and the productivity improvement effect is remarkably exhibited by annealing in the low temperature region.
- Tensile strength 550 ⁇ 700MPa
- the steel plate for cans produced according to the present invention is one of the purposes that is currently applied to fields that use high-strength and ultra-thin steel plates such as DR materials, such as DRD cans and welded cans. It is said. In such a field, if the plate thickness of the steel sheet is 0.18 mm or less and the tensile strength is 550 MPa or less, the can body strength is insufficient, and there is a concern about the buckling of the can. To avoid this, the target tensile strength is 550 MPa or more. The On the other hand, when trying to obtain strength exceeding 700MPa (exceeding 650MPa when Nb and B are not used), it is necessary to add a large amount of strengthening elements, which may impair corrosion resistance.
- the tensile strength is controlled to the target value mainly by adjusting the steel plate composition, cold rolling rate, and annealing temperature.
- the cold rolling rate is set to 60% or more, and the tensile strength is controlled to 550 to 650 MPa by annealing at a soaking temperature: (at a recrystallization start temperature of 200 :) to (at a recrystallization start temperature of 20). ( Figure 1 ).
- C 0.003% or less
- N 0.004% or less
- Mn 0.05% to 0.5%
- P 0.02% or less
- Si 0.02% or less
- S 0.03% or less
- A1 0.1% or less.
- Nb 0.001% to 0.05%
- B Add at least one of 0.0001% to 0.005% to make the cold rolling rate 60% or more
- soaking temperature (Recrystallization start temperature 1 200) The tensile strength is controlled to 550-700MPa by annealing at a recrystallization start temperature of 20 (Fig. 2).
- the Rockwell hardness (HR30T) is about 74 to 77 when Nb and B are not added, and about 74 to 80 when at least one of Nb and B is added.
- the target for total growth is 4% or more. In order to improve the workability as much as possible, it is desirable to secure a total stretch of 5% or more.
- the total elongation is controlled to the target value mainly by adjusting the copper plate composition and the cooling rate after finishing during hot rolling. Next, the manufacturing method of the steel plate for cans of this invention is demonstrated.
- Molten steel adjusted to the above-mentioned chemical composition is produced by a generally known steel making method using a converter or the like, and then used for ordinary purposes such as continuous forging.
- Rolled material (steel ingots, especially slabs) is made by the forging method.
- a hot-rolled sheet is obtained by hot rolling using the rolled material obtained as described above.
- the rolled material Prior to hot rolling, the rolled material should be heated to 1250 or more. This is because the precipitates in the steel are completely dissolved to eliminate segregation and make the material homogeneous.
- the finishing temperature should be higher than the A r3 transformation point.
- scraping is performed at a scraping temperature of 600 to 750.
- the scale covering the surface of the steel plate is usually removed by pickling. Then, after performing cold rolling at a rolling reduction of 60 to 95%, annealing is performed at a temperature of (recrystallization start temperature—ZOOt) to (recrystallization start temperature—20T:).
- the hot rolling finishing temperature should be above the A r3 transformation point.
- finish rolling below the A r3 transformation point has the advantage of reducing the strength of the steel during recovery annealing, but finishes so that the center in the width direction of the slab is below the A r3 transformation point.
- the strain introduced in the finish rolling is less likely to be released by recrystallization or recovery in the widthwise wedge part, which has a faster cooling rate than the center part.
- the edge portion becomes hard, the difference in strength between the central portion and the edge portion becomes large, and a hot-rolled sheet having a non-uniform structure is easily obtained. Therefore, in order to obtain a hot-rolled sheet having a uniform structure, the finishing temperature should be higher than the Ar3 transformation point.
- the finishing temperature is more preferably set to Ar 3 transformation point + 5 or more.
- the finishing temperature is preferably 9503 ⁇ 4 or less from the viewpoint of avoiding scale defects.
- the Ar 3 transformation point is generally in the range of 840 to 910.
- the total elongation of the steel can be ensured only by hot rolling above the Ar3 transformation point, for the following reason.
- the ferrite grain size of the hot-rolled sheet is determined by hot rolling (which is a condition of the present invention). It is relatively small when raising temperature is higher than Ar3 transformation point, and is relatively large when hot rolling finish temperature is lower than Ar3 transformation point (which is a condition in the technology using conventional recovery annealing). . When both are cold-rolled, the strain energy accumulated in the cold-rolled sheet becomes higher when the ferrite grain size of the hot-rolled sheet is smaller.
- the conditions of the present invention are conditions that promote the progress of the recovery phenomenon. Due to the recovery phenomenon, the cold-rolled steel sheet decreases the strength. However, since the condition of the present invention is a state of high strain energy, the target high strength can be maintained even after recovery. In addition, since the ductility is improved by the recovery phenomenon, the desired appropriate ductility can be ensured. From the above mechanism, it is preferable to avoid hot-rolling high-temperature finishing and high-purity composition in which the particle size tends to grow.
- the cutting temperature In the hot rolling process, the cutting temperature must be 600 to 750. If it is less than 6003 ⁇ 4, the heat-retaining effect after scraping is not sufficient, and the ferritic grain size of the hot-rolled sheet becomes unnecessarily small, so that the strength tends to become excessively high. 7 This organization is not desirable because it is easy to make.
- the rolling reduction is 60-95%. If the rolling reduction is less than 60%, the desired strength is not achieved after cold rolling and heat treatment (recovery annealing). In addition, there is a problem that is considered to be caused by non-uniformity of the material, especially the non-uniformity in the direction of plate grinding. On the other hand, when the rolling reduction exceeds 95%, it becomes difficult to avoid deterioration of local ductility.
- a preferable rolling reduction is 80% or more.
- Recrystallization start temperature 1 200 or more, Recrystallization start temperature 1 20 or less The heat treatment (annealing) is performed in a temperature range where the recrystallization start temperature is at least 200 ⁇ and the recrystallization start temperature is _20 or less. Since the recrystallization temperature is changed by the composition, for example, addition of Nb, B, etc., the temperature range (soaking temperature range) is based on the recrystallization start temperature of each steel as _2003 ⁇ 4 to 120 Yes.
- the purpose of annealing (recovery annealing) in the present invention is to reduce the strength to the target strength by performing strain relief annealing from the state where the strength is increased by the strain introduced by cold rolling. If the recrystallization start temperature is less than 200, the strain is not sufficiently released, and the recrystallization start temperature is about 2003 ⁇ 4: as the lower limit because it is higher than the target strength and lower in ductility.
- a more preferable lower limit temperature from the viewpoint of ensuring ductility is a recrystallization start temperature of 150.
- Recrystallized grains and recovered grains can be distinguished by observation with an optical or electron microscope.
- a more preferable upper limit temperature from the viewpoint of securing the strength is the recrystallization start temperature-30.
- the recrystallization start temperature is generally in the range of 560 to 650: (Nb and B not added) or 620 to 780 (Nb and B added at least). .
- the soaking time during annealing is preferably set to 10 s or more and 90 s or less.
- a steel slab was obtained by melting copper containing the composition shown in Table 1 and the balance being inevitable impurities and Fe. After the obtained steel slab was reheated at each temperature shown in Table 2, hot rolling was started. The hot rolling was performed by changing the finish rolling temperature in the range of 800 to 950 and the cutting temperature in the range of 550 to 7003 ⁇ 4 (all shown in Table 2). Next, after pickling, cold rolling was performed at each reduction rate shown in Table 2 to produce a 0.15 mm thin steel plate (here, the thickness of the hot-rolled plate was adjusted according to the reduction rate).
- a tensile test and a ⁇ value measurement were performed on the plated steel sheet obtained as described above.
- the tensile test was performed using JIS5 size tensile test pieces (rolling direction), and the tensile strength and elongation (total elongation) were measured to evaluate the strength and ductility.
- the average r value was obtained by the natural vibration method specified in JIS Z2254.
- Table 3 shows that the inventive examples (steel plates 1 and 2 etc.) have a tensile strength of 550 to 600 MPa and a total elongation of 5% or more.
- the annealing temperature is below the range of the present invention, and the ductility is lowered because the recovery of strain in the steel is small.
- the comparative example (steel plate 4) is annealed. Since the temperature is higher than the range of the present invention and recrystallization starts locally, the strength is insufficient.
- TS: 550 to 650 MPa is obtained at an annealing temperature between the recrystallization start temperature -20 and 200. Note that when recrystallization start temperature is reduced to 403 ⁇ 4 or less, TS: 600 to 650MPa force S is obtained. On the other hand, to obtain a steel plate of 550 to 600MPa, recrystallization start temperature is approximately It can be seen that it is preferable to anneal with ⁇ -403 ⁇ 4 :).
- a steel slab was obtained by melting the steel containing the composition shown in Table 4 and the balance of inevitable impurities and Fe in an actual converter.
- the obtained steel slab was reheated at 1 150 to 1250, and hot rolling was started.
- the finishing rolling temperature was varied in the range of 880 to 900, and the milling temperature was 620 ⁇ .
- the steel sheet was cold-rolled at a rolling reduction of 80 to 90% to produce a thin steel plate having a thickness of 0.15 to 0.18 mm.
- the obtained thin steel sheet was annealed in a continuous annealing furnace at an annealing temperature of 300 700 and an annealing time of 30 s (recovery), and subjected to temper rolling so that the elongation was 1.5% or less.
- Tin-free steel was obtained by continuous chrome plating. Detailed manufacturing conditions are shown in Table 5.
- annealing temperature As a result of confirming the recrystallization behavior of steels 2-18, it was confirmed that recrystallization was completed at 620-720 as shown in Table 5.
- Fig. 2 shows the results of confirming the recrystallization behavior of steel 5 in Table 4 (manufactured under the conditions of steel plate 13 in Table 5 except for the annealing temperature).
- the tensile strength is 550 to 700 MPa and the total elongation is 4% or more.
- the annealing temperature is lower than the range of the present invention and the recovery of strain in the steel is small, so the strength is high and the ductility is low.
- the annealing temperature exceeds the range of the present invention and the recrystallization starts locally, so that the strength is insufficient.
- TS: 550 to 700 MPa is obtained at an annealing temperature between the recrystallization start temperature of 20 to 1 200 ⁇ . Recrystallization start temperature When TS is annealed at _40 or less, TS: 650 to 700 MPa is obtained. On the other hand, to obtain a steel plate with 550 to 650 MPa, annealing at a recrystallization start temperature of ⁇ 20 to 1-50 (preferably to 1 to 40) It can be seen that it is preferable.
- the strength is high and the ductility is lowered.
- the recrystallization behavior changes depending on the amount of Nb and B added, so that the applicable annealing temperature can be changed.
- the strength obtained can be changed by adding Nb and B. Therefore, the production method of the present invention can be annealed in the same cycle as other steel plates for cans, and can obtain a desired strength. .
- a steel plate for cans having a tensile strength of 550 to 650 MPa and a total elongation of 5% or more is obtained. Even when the DR process and the recrystallization annealing process are omitted, when Nb and B are added, a tensile strength of 550 to 700 MPa and an elongation of 4% or more can be obtained.
- a copper plate for high-strength cans can be manufactured and provided at a low cost without sacrificing corrosion resistance for cans that do not require small anisotropy. It becomes possible.
- the manufacturing method of the present invention is annealed in a low temperature region as compared with a normal method for manufacturing steel sheets for cans, it is possible to reduce energy costs. Also, by adding Nb and B, it is possible to anneal in the same temperature range as a normal steel plate for cans. In this case, there is no need to provide a separate annealing opportunity. As a result, it is possible to produce a steel sheet of T S 550 to 700 MPa class without hindering productivity. On the other hand, in the present invention, as shown in FIGS. 1 and 2, it is possible to perform annealing in a temperature range where the change in strength is small depending on the annealing temperature. Therefore, even if the annealing temperature varies, it is uniform in the width direction. A steel plate with an appropriate strength level can be obtained.
- the steel plate for cans produced by the production method of the present invention is a container for canned beverages and food cans. Most suitable as steel plate for cans, mainly 2-piece DRD cans and 3-piece welded cans.
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- Heat Treatment Of Sheet Steel (AREA)
Abstract
L'invention concerne une feuille d'acier haute résistance pour boîtes métalliques, qui a une résistance à la traction de 550 à 650 MPa et un allongement total de 5 % ou plus, qui est obtenue par la réalisation d'un laminage à chaud avec une température de finition de la température de transformation Ar3 ou plus, d'un laminage à froid, puis d'un recuit de restauration à une température de la température d'initiation de recristallisation moins 200°C à la température d'initialisation de recristallisation moins 20°C. En outre, l'addition de Nb : 0,001 à 0,05% et/ou de B : 0,0001 à 0,005% produit une feuille d'acier pour des boîtes métalliques qui a une résistance à la traction de 550 à 700 MPa et un allongement total de 4 % ou plus tout en permettant le recuit dans la même plage de température que celle des feuilles d'acier classiques pour boîtes métalliques.
Priority Applications (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP08711889.9A EP2123780B1 (fr) | 2007-02-21 | 2008-02-19 | Procédé pour la fabrication de feuilles d'acier pour boîtes métalliques |
CN200880001425.7A CN101578381B (zh) | 2007-02-21 | 2008-02-19 | 罐用钢板的制造方法 |
KR1020097010592A KR101128315B1 (ko) | 2007-02-21 | 2008-02-19 | 캔용 강판의 제조 방법 |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
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JP2007-041065 | 2007-02-21 | ||
JP2007041065A JP5076544B2 (ja) | 2007-02-21 | 2007-02-21 | 缶用鋼板の製造方法 |
Publications (1)
Publication Number | Publication Date |
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WO2008102899A1 true WO2008102899A1 (fr) | 2008-08-28 |
Family
ID=39710169
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2008/053125 WO2008102899A1 (fr) | 2007-02-21 | 2008-02-19 | Procédé pour la fabrication de feuilles d'acier pour boîtes métalliques |
Country Status (5)
Country | Link |
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EP (1) | EP2123780B1 (fr) |
JP (1) | JP5076544B2 (fr) |
KR (1) | KR101128315B1 (fr) |
CN (1) | CN101578381B (fr) |
WO (1) | WO2008102899A1 (fr) |
Families Citing this family (9)
Publication number | Priority date | Publication date | Assignee | Title |
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JP5076544B2 (ja) | 2007-02-21 | 2012-11-21 | Jfeスチール株式会社 | 缶用鋼板の製造方法 |
JP5655300B2 (ja) * | 2009-03-05 | 2015-01-21 | Jfeスチール株式会社 | 曲げ加工性に優れた冷延鋼板、その製造方法およびそれを用いた部材 |
JP5811686B2 (ja) * | 2010-10-18 | 2015-11-11 | Jfeスチール株式会社 | 高強度缶用鋼板およびその製造方法 |
JP5903884B2 (ja) * | 2011-12-27 | 2016-04-13 | Jfeスチール株式会社 | 耐腰折れ性に優れた高強度薄鋼板の製造方法 |
RS60571B1 (sr) * | 2012-03-30 | 2020-08-31 | Tata Steel Ijmuiden Bv | Postupak za proizvodnju obloženog rekristalizovanog žarenog čeličnog supstrata za izradu ambalaže i tako dobijeni čelični proizvod za izradu ambalaže |
DE102013003516A1 (de) * | 2013-03-04 | 2014-09-04 | Outokumpu Nirosta Gmbh | Verfahren zur Herstellung eines ultrahochfesten Werkstoffs mit hoher Dehnung |
CN106029926B (zh) * | 2014-02-25 | 2018-10-02 | 杰富意钢铁株式会社 | 瓶盖用钢板及其制造方法以及瓶盖 |
ES2770737T3 (es) | 2014-05-30 | 2020-07-02 | Jfe Steel Corp | Lámina de acero para latas y método de fabricación de las mismas |
JP6819838B1 (ja) * | 2019-03-29 | 2021-01-27 | Jfeスチール株式会社 | 缶用鋼板およびその製造方法 |
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2008
- 2008-02-19 CN CN200880001425.7A patent/CN101578381B/zh active Active
- 2008-02-19 WO PCT/JP2008/053125 patent/WO2008102899A1/fr active Application Filing
- 2008-02-19 KR KR1020097010592A patent/KR101128315B1/ko active IP Right Grant
- 2008-02-19 EP EP08711889.9A patent/EP2123780B1/fr active Active
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JPS62161938A (ja) * | 1986-01-09 | 1987-07-17 | Kawasaki Steel Corp | 化成処理性、加工性の良好な冷延鋼板とその製造方法 |
JPH02118026A (ja) * | 1988-10-28 | 1990-05-02 | Kawasaki Steel Corp | 缶用鋼板の製造方法 |
JPH02118024A (ja) * | 1988-10-28 | 1990-05-02 | Kawasaki Steel Corp | 缶用鋼板の製造方法 |
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JPH06248339A (ja) | 1993-02-26 | 1994-09-06 | Nippon Steel Corp | 高剛性容器用鋼板の製造方法 |
JPH0841549A (ja) | 1994-08-01 | 1996-02-13 | Kawasaki Steel Corp | 製缶用鋼板の製造方法 |
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JPH08269568A (ja) | 1995-03-30 | 1996-10-15 | Kawasaki Steel Corp | フランジ成形性に優れた製缶用鋼板の製造方法 |
JP2001107186A (ja) | 1999-08-05 | 2001-04-17 | Kawasaki Steel Corp | 高強度缶用鋼板およびその製造方法 |
JP2004285418A (ja) * | 2003-03-24 | 2004-10-14 | Nippon Steel Corp | 製缶性に優れた高時効硬化容器用鋼板及びその製造方法 |
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See also references of EP2123780A4 * |
Also Published As
Publication number | Publication date |
---|---|
CN101578381A (zh) | 2009-11-11 |
JP5076544B2 (ja) | 2012-11-21 |
EP2123780A4 (fr) | 2010-10-27 |
KR101128315B1 (ko) | 2012-04-12 |
JP2008202113A (ja) | 2008-09-04 |
KR20090084885A (ko) | 2009-08-05 |
EP2123780B1 (fr) | 2015-12-02 |
CN101578381B (zh) | 2013-06-19 |
EP2123780A1 (fr) | 2009-11-25 |
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