TW201000649A - High-strength steel sheet for container and process for production thereof - Google Patents

Abstract

Provided are a steel sheet for a container which has hardness of 500MPa or above and excellent workability, and a process for the production of the sheet. A high-strength steel sheet for containers which has a tensile strength of 500MPa or above and in which the proof stress difference between the sheet widthwise direction and the rolling direction is 20MPa or below can be obtained by subjecting a steel which contains by mass C: 0.01 to 0.05%, Si: 0.04% or less, Mn: 0.1 to 1.2%, S: 0.10% or less, Al: 0.001 to 0.100%, N: 0.10% or less, P: 0.0020 to 0.100% with the balance being Fe and unavoidable impurities to hot rolling at a finishing temperature not lower than the Ar3 transformation temperature minus 30 ( DEG C) and a coiling temperature of 400 to 750 DEG C, subjecting the rolled steel to pickling, cold rolling, and then continuous annealing including over-aging, and then subjecting the resulting sheet to second cold rolling with a draft of 20 to 50%.

Description

[Technical Field] The present invention relates to a steel sheet for two-piece processing suitable for shrinking or expanding processing of a crucible shape after three sheets of force, and a method for producing the same. ° High-strength container with material [Previous technology] ^Yearly, as a purpose of reducing costs, and reducing the use of materials or reducing the environment, we are developing materials for steel products (steel sheets). Further, if the thickness of the product is reduced, the rigidity is lowered, and in order to compensate for the "reduction", it is necessary to increase the strength of the steel. However, since the steel material is hardened when it is required to be strengthened, there is a problem that cracking occurs in the flange processing or the necking processing. In view of the above, various manufacturing methods are currently considered. For example, in the patent literature (the proposal is to manage the composition of the steel within a certain range and at (Αη metamorphic point ~3〇. 结束 〇 结束 热 热 热 结束 结束 , , , , , , , , , , , , , , 施 施 施 施 施 施 施 施 施 施 施 施And the second step of the second step is to set the P to 0.20% or less, and the second to be cold. The rolling reduction ratio of the rolling is set to 15 to 3 %, so that it is difficult to efficiently and efficiently process the thinner products, resulting in difficulty in production, and problems in which appearance is liable to occur. In addition, it also occurs in the surface layer of the steel slab. The rupture has caused the problem of the product yield of 098111997 201000649. It is difficult to carry out the manufacture and it is necessary to improve it. In addition, the manufacturing method of the steel plate for hard containers is proposed as follows: Appropriate choice of use (for example, non-patent literature U. Rate phase annealing (10)) - the second cold-like rate of thermal continuous annealing is called the second cold rolling (rolling ... and the upper 4 method towel g) for the lifting delay Various with high viscosity The oil is extended, because (4) due to the thickening of the rolling oil, the adhesion of the oil, etc., the problem of poor rolling of the blade is not caused. In addition, when the rate is 1^, the steel sheet is stretched by rolling. The difference in the endurance between the width direction of the steel sheet and the rolling direction is increased. In view of this, a method of reducing the rolling ratio at the time of the second cold rolling is considered, and it is difficult to obtain the necessary endurance when the rolling ratio is lowered.疋 Patent Document 1: Japanese Patent No. 3108615, Non-Patent Document 1: "Technical History of Surface Treated Steel Sheets for Cans in China", Sakamoto Steel Association, published on October 3, 2003, p i88 ^ Accordingly, when products are to be obtained When a steel plate for a container having a thin plate thickness is used, there is no yield strength, fine processing, and production in the current state. (4) The manufacturing method is satisfied. (4) The manufacturing method is satisfied. The present invention is completed in view of the facts, and the purpose is to provide tensile strength. In the present invention, the inventors of the present invention have solved the above-mentioned problems. The problem was obtained and the following findings were obtained. It was found that by adjusting the P content as a component composition and performing the second cold rolling at a rolling ratio of 20 to 50%, the strength is increased, and the continuous annealing is performed. By performing an aging treatment and uniformly depositing carbides, and using the carbides as voids for dispersing stress during processing, it is possible to reduce the appearance unsuitable, and it is possible to reduce the endurance difference in the width direction and the rolling direction, and to secure a high-strength material. Further, it has been found that a steel sheet for a container which is more excellent in workability can be obtained by standardizing the particle diameter, density, and ratio of the above-mentioned carbide. As described above, the present invention manages components by the above findings. The present invention has been completed based on the above findings, and the subject matter is as follows: [1] A steel sheet for a high-strength container, which is based on % by mass, contains: C: 0·01 ～0·05%, Si 0. 04%以下, Μη: 0. Bu 1. 2%, S: 0. 10% or less, Α1: 0.001 to 0. 100%, Ν: 0. 10% or less, Ρ: 0.0020~0. 100% , the rest consists of Fe and inevitable impurities, pulling The tensile strength TS is more than 500 MPa, and the difference in endurance between the width direction and the rolling direction is 20 MPa or less. [2] A steel sheet for high-strength containers, in terms of mass%, containing: C: 0. 0 Bu 0. 05%, Si: 0. 04% or less, Μη ·· 0. :1 〜1. 2% , S : 0. 10% to 989111997 5 201000649, A1 : 0. 001 ~ 〇. 100%, n: 〇. 10% or less, P: 0. 0020~0. 020%, the rest by Fe and inevitable The composition of the impurities is such that the tensile strength TS is 500 MPa or more, and the difference in the resistance between the sheet width direction and the rolling direction is 2 MPa or less. [3] The method for producing a steel sheet for high-strength containers is determined by mass%: C: 0. 0 Bu 0. 05%, Si: 〇 · 04% or less, Mn: 〇. Bu 1. 2% , S : 0· 10% or less, A1 : 〇. 〇〇卜〇. 1〇〇%, N: 10% or less, P: 0. 0020~0· 100%, and the rest consists of impurities avoided by Fe and the town. The steel, according to the finishing temperature: (Ar3 metamorphic point temperature -30) °C or more, coiling temperature: 400~750. The hot rolling is performed, and after pickling and cold rolling, continuous annealing with an overaging treatment is performed, and then the second cold rolling is performed according to the rolling rate: 20 to 5 %. [4] A method for producing a steel sheet for a high-strength container is contained in a mass%: C: 0. 01 〜0· 05%, Si: 0.45% or less, Μη: 〇·1~1. 2% , S : 0· 10% or less, Α 1 : 0. 〇〇 1 〇 100 100%, Ν : 〇. 1〇% or less, ρ: 0.0020 to 0.020% 'The remaining steel consisting of Fe and unavoidable impurities, According to the finishing rolling temperature: (An transformation point temperature -30) °C or more, coiling temperature: 400~750 ° (: performing hot rolling 'after pickling, cold rolling' and then performing continuous annealing with overaging treatment, Then, the second rolling cold rolling is carried out according to the rolling rate: 20 to 50%. In the present specification, the "%" of the steel component means "% by mass". In addition, in the present invention, "for high-strength containers" "Steel plate" refers to a steel sheet for a container having a tensile strength TS (hereinafter referred to as "TS") of 500 MPa or more. The steel sheet for a high-strength container of the present invention is intended for a container material or a can material, regardless of the presence or absence of a surface. Treatment, tin plating, nickel-plated tin, 098111997 6 201000649 chrome plating (so-called tin plating), or organic coating, etc., can be applied to the pole In addition, the relevant thickness is not particularly limited, but from the viewpoint of obtaining the maximum limit utilization effect of the present invention, the thickness is preferably 0.30 mm or less, more preferably 0.20 or less, and particularly preferably 0.10 mm or less. [Embodiment] The present invention will be described in detail below. f. The steel sheet for a container of the present invention has a TS of 500 MPa or more, and a steel sheet for a high-strength container having a difference in sheet width direction and a rolling direction of 20 MPa or less. In the invention, by adjusting the P content and setting the rolling ratio of the second cold rolling (hereinafter referred to as "secondary cold rolling") to 20 to 50%, it is possible to provide a high-strength steel sheet for containers. The composition of the steel sheet for a container according to the present invention will be described. C: 0. 01-0. 05% ί, if the C component is excessive, the steel sheet after the second cold rolling is hardened more than necessary, resulting in potability and The necking processability is deteriorated, and it is an element which is caused by the hardening of the welded portion and causes cracking of the crucible during the flange processing. If C. exceeds 0.05%, since the influence tends to be obvious, C is set to - 〇 _ 05% or less. Another When the C component is extremely low, it is necessary to perform secondary cold rolling at a high rolling ratio in order to maintain the strength of the container. Therefore, C is set to 0.01% or more, preferably 0.02% or more and 0.04% or less, more preferably 0.02% or more. 0. 03% or less. 098111997 7 201000649

Si: 0.04% or less When Si is added in a large amount, surface properties are deteriorated, corrosion resistance is deteriorated, and the like. Therefore, the 'Si system is set to 〇. 〇 4% or less.

Mn : G. 1 to 1. 2% Μ η is an effective element for preventing hot rolling cracking caused by S. By adding the amount of S, the effect of preventing cracking can be obtained. In addition, it also has the effect of refining crystal grains. In order to exert these effects, Μη must be added at least 0.1% or more. On the other hand, if it is added in a large amount, the corrosion resistance tends to deteriorate. The steel sheet is hardened more than necessary, and both the flange fixing property and the necking workability are deteriorated, and the upper limit is 丨 2%. It is preferably set below q•(10). P: 0. 0020-0. 100% P is a component which hardens steel. In the present invention, a predetermined enthalpy is contained in accordance with the required strength. If the right is less than 0. 0020%, 5 〇〇 Mpa or more cannot be obtained, so it is set to G. On the other hand, if the p component contains a necessary excess amount or more, the resistance is deteriorated. And the flange reinforcement and occupational processing are deteriorated. These cases tend to be more than 〇. 1〇〇% tend to be obvious, so the upper limit is set to 0·100%. When the right 3 is 0.0020 to 0.020%, it is preferable to obtain higher strength by the moderate strength caused by the addition of p and the effect of the first cold drying. S : 0. 10% or less The S system exists in the form of inclusions in steel, and is an element which reduces the ductility of the steel sheet and deteriorates the etchability. Therefore, it is set at 〇. 1〇% or less. Preferably 〇. 030% 098111997 8 201000649 Below. A1 : 0. 001 ~ 0. 100% A1 steel is necessary for deoxidation. If the content is less than 0.001%, the deoxidation is insufficient, and the workability of the flange is deteriorated and the necking workability is deteriorated due to inclusions. Therefore, it is set at 0.001% or more. On the other hand, although A1 is bonded to the N component to reduce the solid solution N, if the solid solution N is excessively decreased, the necessary strength cannot be obtained. Therefore, it is set to 0. 100% or less. 035〜0. 075%。 Preferably 0. 035~0. 075%. f N ·· 0· 10% or less N is an element that can effectively increase the strength without causing the hardness of the welded portion to increase. However, if the content is too large, the steel sheet is remarkably hardened, and the risk of occurrence of cracking defects in the rolled material (steel billet) is remarkably increased, which in turn causes deterioration in flange workability and necking workability. Therefore, N is set to be 0. 10% or less. Preferably it is 0.05% or less. 01%。 In addition, from the point of view of the rupture of the steel slab, the preferred setting is less than 0.01%.佳佳0. 005% or less. Accordingly, by reducing N, V can reduce the rupture of the billet, and the billet treatment is not required, which can improve the yield. The rest are Fe and inevitable impurities. Other than the above components are Fe and unavoidable impurities. In addition, _ an unavoidable impurity may allow, for example, Sn: 0.01% or less. The steel sheet for containers of the present invention has the above composition and has a TS of 500 MPa or more, and the difference in endurance between the sheet width direction and the rolling direction is 20 MPa or less. By having a TS of 500 MPa or more, the rigidity is not lowered even if the thickness is reduced. Furthermore, since the difference in the endurance between the width direction of the plate and the rolling direction is set to 09811997 9 201000649 20 MPa, the shape is 0 or less. 'When the flange processing and the necking are increased by 1, the crack does not occur. Then, the high strength is specified for the present invention. . In the method for producing a steel sheet for a device, the above-described composition is melted by a generally known method. Next, a commonly known casting material such as a continuous casting method is used. Hot-rolled steel billet extraction temperature: 1050~130 (rc (better condition) If the steel temperature is set to be t or more, the hot rolling end temperature can be ensured in the next-step hot rolling. On the other hand, If the extraction temperature is set below 130 °C, the surface properties of the final steel sheet will not deteriorate. Therefore, the steel billet drawing temperature is preferably 1〇5〇 or more and (10). C or less. End temperature): (An transformation temperature - 3 〇). The hot rolling end temperature is the same as the cold rolling property and product characteristics of the subsequent step, and it is necessary to set (A n metamorphic point _ 3 〇). If it is less than (A "3 metamorphic point -30" C, the metal structure of the final product is coarsened, and the skin is likely to be rough during the can making. Further, if the hot rolling end temperature is low, a ridge phenomenon occurs. Causes poor appearance after forming Therefore, the hot rolling end temperature is set to (An metamorphic point -30). (: Above.

Coiling temperature: 400 to 750 ° C If the coiling temperature is too low, the shape of the hot-rolled sheet deteriorates, and in the next step, acid 098111997 10 201000649 washes and colds 4, causing an obstacle, so it is set to 400C or more. On the other hand, if the surface is turned over, gasification will occur during the hot rolling of the mother plate, and sufficient solid solution N required for strengthening cannot be ensured. In addition, the hot-rolled mother sheet forms a structure in which carbides aggregate, and the uniform precipitation of carbides due to overaging as described later cannot be obtained, and the corrosion resistance of the steel sheet is also adversely affected. Further, the thickness of the scale generated on the surface of the steel sheet is increased to deteriorate the pickling property. In order to avoid such adverse conditions, it is necessary to set below 75 CTC. The hot rolled sheet thus obtained is subjected to pickling and cold rolling to form a cold rolled sheet. For the pickling system, the surface scale is removed by using an acid such as hydrochloric acid or sulfuric acid according to the usual method. The rolling rate of cold rolling after pickling (after pickling) is 80% or more (better conditions).

If the rolling ratio is less than m, it may not be possible to obtain sufficient granulation after annealing, and thus it is preferably _ or more. Further, the steel sheet of the material of the present invention is more preferably (10) or more in order to achieve a sufficiently fine film formation. In addition, there is no particular limitation on the upper limit of the relevant rolling rate, and it can be appropriately set after considering the capacity of the hot-drying and cold-rolling equipment. 7 degree: Recrystallization temperature below _°c (preferred condition) If there is a residual non-recrystallized structure in the steel sheet, it is good or bad in appearance. Therefore, it is necessary to use continuous retreat. 'If the annealing temperature is excessively increased, continuous annealing is performed. Will: raw = heat (heat buckle), plate breakage and other defects. Moreover, the risk of deterioration in appearance characteristics is also increased. 098111997 11 201000649 degrees are preferably carried out in a recrystallization temperature region of 800 ° C or less. Furthermore, if it is within the temperature range, it is not necessary to maintain a particular degree. From the viewpoint of the stability of the work, it is sufficient to set the heat for a period of 5 sec or more. When the soaking time of 5 s or more is used, it is preferable that the ruthenium of J is sufficient to precipitate carbides in the stress dispersion voids. Overaging treatment In order to more uniformly disperse the carbides precipitated by the above annealing, and to exert the effect of stress-dispersing voids, it is necessary to perform an overaging treatment. The obsolescence treatment is preferably carried out after the above annealing, and is cooled to a temperature range of 300 to 500 C at a cooling rate of 1 or more (rc/s), and is maintained at 300 to 5 Torr (the temperature is maintained in the rc temperature region. With HTC/s or higher The cooling rate is cooled to 3 〇〇 to 5 〇〇. In the 〇 temperature region, carbides are easily precipitated, and if it is kept in the temperature range of 300 〜5 〇〇〇 c for more than 5 s, uniform carbide precipitation can be ensured. By performing such an overaging treatment, even if the second cold rolling shown below is performed at a rolling ratio of 20 to 50%, the difference in the resistance between the sheet width direction and the rolling direction can be made 2 MPa or less. When the aging treatment is carried out under conditions, the carbide density and ratio of the particle diameter of 15/m or less and the particle diameter of more than 1.5//in and 3.0/im or less are preferably in the preferred range described later. The rolling of the second cold rolling Rate: 2〇~5〇% (preferably 2〇~3〇%) The second cold rolling after annealing (hereinafter referred to as "second cold rolling") is used to ensure the compression strength of the welding tank (ie The necessary step 4 of the steel plate fall strength) is to consider the use of the adjusted p content of the present invention, 2 times cold rolled 988111997 1 2 201000649 The rolling rate must be at least 20%. On the other hand, if the rolling rate exceeds 5〇%, the anisotropy of the material properties becomes larger, and the difference between the board width direction and the rolling (rolling) direction is poor. In addition, the flange workability and the necking workability of the new take-up method (the method of taking the steel sheet in the direction in which the rolling direction of the steel sheet is parallel to the axis of the can body) are remarkably deteriorated. Further, since the welding is performed at the time of canning, The amount of strain opening is increased, and the softening of the heat-affecting portion of the dazzling portion tends to be obvious, so that the flange crack is likely to occur. Therefore, it is set to 50% or less, preferably 20% or more and 30% or less, as long as the p content is contained, η and The strength of the target steel sheet can be appropriately selected. Specifically, when the ρ content exceeds 0. 020% and 0. 100% or less, it is preferable to set a lower rolling rate. In the present invention, '2 times' After cold rolling, a plating layer is formed on the surface (at least one side) of the cold-rolled steel sheet to form a steel sheet. The layer formed on the surface can be applied to a steel sheet for containers. The plating system can be exemplified. Such as: tin, chrome, nickel, nickel, chromium, etc. After the treatment, it may be applied by coating or attaching an organic resin film. V. [Examples] Steels containing the components shown in Table 1 and containing Fe and unavoidable impurities were melted in a converter. And the billet is formed by the continuous casting method. The billet is subjected to hot milk under the conditions that the billet extraction temperature is 1201TC, the hot rolling finishing temperature is 900°c, and the coiling temperature is 650X: The hot rolled sheet having a thickness of 2.0 mm is formed. Then, the hot rolled sheet is subjected to descaling treatment by pickling, and then cold rolling is performed at a rolling rate of 9% by weight to form a finish rolling thickness.冷.2〇mm cold-rolled sheet, followed by continuous tempering, overaging treatment and 2 cold rolling with a heat temperature of 098111997 13 201000649 of 750 ° C and a soaking time of 10 to 30 s. Rolled steel plate. Further, the overaging treatment conditions and the two-time cold rolling rolling ratio are shown in Tables 2 and 3. [Table 1] Steel mark steel composition (% by mass) TC Si Μη Ρ s A1 NA 0. 02 0. 015 0. 15 0. Oil 0. 004 0. 005 0. 0100 B 0. 02 0. 015 0. 15 0. 020 0. 004 0. 005 〇· oi〇(TC 0. 02 0. 015 0. 15 |〇^ 021 0. 004 0. 005 !〇. 0065 D 0. 02 0. 015 0. 15 L ο 019 0. 004 0. 005 0. 0043~'

Ara metamorphic point (°〇890 890 890 890 for the steel sheet obtained above) was observed by the following method, and the density and ratio of the carbide particle size were determined, and the following tests were performed to evaluate the characteristics. The cold-rolled steel sheet is buried in the phenolic resin, and the surface is polished. Then, the 'corrosion solution is a sodium sulphate solution prepared by blending bitter acid and sodium hydroxide' in an etching solution at 80 ° C for 60 seconds. The impregnation treatment was carried out. Next, the carbon crystals were observed under a 400-fold optical microscope for 3 fields (in the range of 0.175 mm×0.175 mm). In each field of view, the particle diameter was determined according to the visual observation. 1. The particle size exceeded i.5/ Zm, 3.0 / / m or less, more than 3.0 / / m of the number of carbides, and the density of the three fields of view and the ratio of the average 値. At this time 'the carbide particle size is set to the minimum diameter, for example, when the shape of the carbide When there are a rectangular or elliptical shape and a short axis and a long axis exist, the minimum diameter is set as the particle diameter in the present invention. (i) Tensile test 098111997 14 201000649 From the central portion in the width direction of the cold rolled steel sheets In the direction of extension (L), take the JIS No. 13-B tensile test The sheet is subjected to a tensile test according to the strain rate of the strain rate, and the tensile test is performed to measure the tensile strength TS and the tensile strength YS. The tensile test system is carried out within one day after the product is produced. The reason why the test piece is set to the 13-B test piece is to minimize the occurrence of cracking outside the punctuation. (ii) The difference in endurance between the plate width direction and the rolling direction is determined by the above-mentioned (i) tensile test. s, and the JIS No. 13-B tensile test piece taken in the width direction of the sheet depends on the difference between the YS measured in the same manner as (i).

Gii) Necking workability The cold-rolled steel sheets were subjected to a Sn plating treatment (% adhesion per one surface of 2. 8 g/m2) to form a plate. On the surface of the Lai steel plate, after applying the coating, printing, and money, the cup is subjected to the following conditions (4) without the pressure test (4), and the second re-stretching treatment is performed. Stretch into the material (10) times, and the incidence of Chen stretch seam. Deep drawing forming conditions. Bulk diameter: 200 mm Φ Lubricating conditions: No forging oil: Tensile ratio of the first stretching: 1.5. Stretching ratio of the second stretching: i2 Stretching ratio of the third stretching: 1. 2 098111997 15 201000649 The first to third stretch of the wrinkles to suppress the pressure: the best conditions of the flange processing: the stretch rate of 8% and then the stretch of the mold fillet radius: 0. 45mm processing speed: 0. 3m / s (iv) Flange fracture resistance In the deep drawing molding of (iii), the occurrence rate of the flange fracture was investigated. (v) Appearance The cold-rolled steel sheets were visually observed, and the portions in which the gloss or the hue was judged to be different were regarded as poor appearance. In the observed unit of l〇〇m, even if only one of the places had a poor appearance, the ΙΟΟη was regarded as a "defective appearance portion", and 10000 m was observed to obtain an appearance defect rate. (>1) Steel rupture The rupture of the slab on the surface of the slab after continuous casting was visually observed. In the observed lm unit, even if there is only one place where the rupture occurs, the lm is regarded as the "defective appearance part", the observation result is 〇m, and the result of the appearance defect rate is obtained. 3 in. 098111997 16 201000649 Steel billet breaking 1 < incidence. (%), LO m LO LO LO LO L LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO LO 〇ο r—H ο CZ5 <〇ζ=) τ—Η <3> CZ3 <=> Flange rupture rate (%) <=> C=5 or«H LO S Ο CP c =5 ο 1—<c=><Z5 CZ3 C3 C=5 CO CO Csj The incidence of neck wrinkling (%) Ο <3> LO Bu CZ3 Cl? CP ο C=5 CNI C? CD 〇> 〇οα LO CO OJ Dance·0 _ ◦ r—Η o 1"< LO C<1 Ο C5 LO LO O <z? 〇CO CO CD CO LO tensile strength TS (MPa) c? LO § s LO g CO <=5 LO CO <Ζ5 CO inch inch LO LO C=3 CNI CO C3> ι_η 〇>C^> g LO § LO Ο) inch C〇g LO s LO g The ratio of LO to total broken material B • 1 \〇U LO 〇〇LO 〇〇ΙΛ 00 LO OO LO 00 § § g § 〇〇〇0 CT5 OO Oi 00 03 OO CO 00 but 00 LO 00 particle size 1. 5//m or less (%) CD inch CD ^f1 a〇CD inch CO co LO CO LO CO LO CO LO CO LO CO LO CO LO LO LO LO LO LO CO s Carbide density (pieces / 10000W) More than 3. 0//m 1____ SSS LO CO οα CO OO <>3 Particle size exceeds 1. 5gm, 3. 0//m or less LO LO LO LO LO LO LO LO LO to inch C£5 co LO OO LO 〇〇c〇丨 particle size 1. 5 仁m following g § § § gsgss 1—^ g 1 ί grt S g S LO 00 § LO σ> Secondary cold rolling rolling rate (%) 0 1 1 LO LO C<J 〇rH LO S sor-H LQ i 1 another gss overaging treatment hold time (S) C=5 〇CZ3 o ◦ LT3 LO LO LO LO LO LO LO LO LO LO LO 1 Temperature CC) 1 1 1 1 1 g LO CZ5 gg LO g LO g LO g LO g LO g LO os ◦ S os 〇s C? o LO Cooling rate (°C/s) Derivation LO oa Another LO CO 1 <c: 0Q CO ca P〇CQ 0Q PQ PQ Classification Comparative Example Comparative Example j Comparative Example Comparative Example Compared with Vehicle Intersection Example Comparative Example Inventive Example Inventive Example Comparative Example of Present Invention Comparative Example 4 4 Inventive Example 4 In the example of the present invention, 4 CM CO LO CO 00 05 Ο i-H CM 1' t 〇〇 1 - Η LO r - H CO 1 · < 卜 ι ^ Η 1 1 1

On On 00 g 201000649

Steel plate characteristics and evaluation results Steel rupture occurrence rate (°/〇), 〇CD O 〇> CZ5 C5 <Z3 c=><=3 ο o 〇><〇C5 CZ3 CD C3 <〇 Appearance NPL ratio (°/〇) C3 C? C5 CZ5 LO <o Ο <〇C5 τ—Η C5 <33 ◦ <=> Q <3) o Flange rupture rate (°/〇) 〇> ◦ I1 < LO 1—^ s CD Ο o CI5 τ—Η <3> C5 C=5 oc=5 CO CO <>a Necking and knocking rate (%) <〇CD LO 卜 CZ5 o CD c G5 CN1 CD CZ5 (>α LO CO oa r-> I taste £ f ◦ ◦ LO C<1 another o (=) LO to 〇CO CO c^· CO LO tensile strength TS (MPa) <3> LQ 呀 g 呀 g LO g CO s co inch LO LO CD s § inch s LO g LO 〇> CD s LO S LO s LO ratio of total carbide B 〇 LO 00 LO OO LO OO LO OO LO 00 § § S § § CO OO CD 00 03 00 05 OO CO 00 inch CO LO OO ε U-^v • 1 \〇U CD CD CO CO CO LO CO LO CO LO CO LO CO LO CO LO CO LO LO LO LO Ln LO LO r < 呀 CD inch s Carbide density (pieces / 10000 _2) Particle size over 3.0 / / ms SSS Another LO CO C < I CO oo particle size exceeding 1. 5ym, 3. Ομπι below LO LO LO ΙΟ LO LO LO LO LO CO CO CO Ln oo LO oo CD particle size 1. 5 / / m The following § ggggs S r-H s T~H sr —HS 1—^ gssr—H s rH LO 00 g LO 05 Secondary cold rolling rolling rate (%) ◦ LO I < S LO CNI Another CZ5 LO 1' 1 S Another go 1—M LO , 丨 <宕 sss over-aging treatment hold time (S) 〇〇C3 o CZ5 LO LO LO LO LO Ln LO LO LO LO LO LO LO temperature CC) 1 1 1 1 g LO g LO Ο ssg LO g LO g LO osg LO g LO g LO 〇> sgm cooling rate (°C/s) write write write write LO C<l another LO CO 〇oo ◦ Ο ooooooo distinguish comparison example comparison example comparison example comparison example comparison example comparison example [Inventive Example 1] Inventive Example Comparative Example Comparative Example Inventive Example Inventive Example φ 4 4 4 Inventive Example 05 |丨1 OJ OJ CO C<1 (Μ LO c〇CJi c<i CO CO CO CO LO CO CD CO oo g 201000649 It is known from Table 2 and Table 3 that the ν〇. 8~ι〇, and 6 31 36 series of the present invention have sufficient strength and the width direction of the plate The difference in the direction of (4) is less than 2 GMPa, and it is sufficient to achieve, for example, the necessary properties of the three ϋ plus reading. The outer appearance is excellent, and the lion wrinkles and the flanges are not broken. In addition, the density and proportion of the stone anaesthetic are known. The good range, 13~15, 26~28, 31~33 will have more excellent processability. On the other hand, the comparative example N〇. 1, 2, 19, 20, which has not been subjected to the aging treatment, has a low rolling rate and cannot obtain strength. The rolling rate of the secondary cold rolling of the 3~5, 2b and 23 series is more than the above, and although the strength is improved, the difference in the endurance between the L direction and the C direction exceeds the occurrence of the sag of the neck and the rupture of the flange. obvious. In addition, it is prone to poor appearance. Further, the strength of the secondary cold rolling rolling reduction of less than 2% Na 6 , 7, u, 12, 24, 25, 29, 30 was not obtained. Furthermore, the density and ratio of the relevant carbides were found as follows. The steel sheet for the inter-strength barn of the present invention preferably has a carbide density of more than 1〇2/丨卯(10)#^2, and a particle diameter exceeding 1· from a viewpoint of workability. The carbide density below 5/m and 3. 0#m exceeds 63/10000/zm. Further, it is preferable that the ratio of the number of carbides having a particle diameter of 1⁄4 m or less to the total number of slaves exceeds 52%, and the number of carbides having a particle diameter of 3. 〇# m or less is relative to the total; The proportion of the number of chars exceeds 85%. The carbide density of the particle size of 1.5//m or less is more than 1 〇 2 / 10000 / zm, and the particle size is more than 1 · 5 # m, 3. 〇 # m below the carbide density of 098111997 19 201000649 degrees over 63 /l〇〇0 (W, it is possible to ensure a sufficient amount of carbide in the stress dispersion function during processing to form a more excellent workability. More preferably, the carbide density of the particle size of 1.5/zm or less is 13〇/ 1〇〇〇〇^2 or more, the granules are more than 1. 5 // m, 3. The carbide density below 〇// m is 8〇/10000 β m2 or more. Furthermore, if the particle size is 1.5_ or less When the ratio of the number of carbide phases to the total number of carbides exceeds 52%, and the ratio of the number of carbides having a particle diameter of 3·- or less to the total number of carbides exceeds 85%, the stress is further increased. The carbide effect of the political void function can further improve the workability. The ratio of the number of carbides with a particle diameter of 1.5 / m or less to the total number of carbides is 55/Q or more, and the particle diameter is 3.0. The ratio of the number of carbides below //m to the total number of carbides is more than 90%. Furthermore, the male, degree and proportion of the above-mentioned slaves are The rolled steel sheet can be controlled by performing annealing treatment under predetermined conditions. Specifically, in the continuous annealing step after cold rolling, the thermal history of the steel sheet is adjusted within a predetermined range and subjected to overaging treatment. The N content shown is 0. 0065%, 〇. 0043%, and is set to a preferred range: an embodiment less than 0.01%. It is known from Table 3 that n is contained below 0. 01 % 'The steel chain is not found to be broken at all, and the steel can be prevented from cracking. According to the present invention, TS having a width of 500 MPa or more can be obtained, and the difference in the direction between the width direction and the rolling direction is less than 20 MPa, and the flange processing and the neck are performed. In addition, in the present invention, by adjusting the P content, the rolling ratio of the second cold rolling is set to 20~. 50%, the high-strength, and can be used to solve the problem of the appearance of the rolling, and the difference in the direction of the width and the direction of the rolling. It can prevent the slab from rupturing and can inhibit the yield reduction of the product. INDUSTRIAL APPLICABILITY The steel sheet for containers of the present invention is excellent in strength because it does not break during necking and flange processing, and is therefore suitable for use in food containers such as cans and non-food products such as oil filters. Material for containers centered on electronic parts such as containers and batteries. 098311997 21

Claims (1)

201000649 VII. Patent application scope: 1 · A steel plate for high-strength containers, based on mass%, containing: c: 0' 01 ~ 0. 05%, Si: 0. 04% or less, Μη: 0. 1~1 2%, S: 10% or less, Α1: 0. 001 ~ 〇. 1〇〇%, ν: 〇. 1〇% or less, ρ: 〇. 0020-0. 100%, the rest by Fe and inevitable The composition of the impurities is such that the tensile strength TS is 5 〇〇 MPa or more, and the difference in the resistance between the sheet width direction and the rolling direction is 2 〇 Mpa or less. 2. 2%, S: 2%, S: 2%, S: 2%, S: 2. 〜1. 2%, S: 0. 10% or less, Α1: 0. 001 ～0. 1〇〇% ...1 ί w u. Ω Ων uzju/u The rest is composed of Fe and unavoidable impurities, and the tensile strength TS is 5_ or more. The difference in endurance between the direction and the rolling direction is 2 (10) pa or less. 3. The method for producing a steel sheet for high-strength containers is based on the mass%: C: 0. 0 Bu 0. 05%, Si: 〇·04% or less, Mn: oH 2%, S 0.10% or less , A1 : 1〇〇%, N: 〇·(10) or less, p 0·leakage~(). Lan's other steel consisting of Fe and unavoidable impurities, finishing rolling temperature: (An transformation temperature, t or more, Coiling temperature ·········································································································· . . . . . . . The following, A1: 〇·001~〇1〇〇%, N · 〇丄(10), °._'. The rest of the Fe and the inevitable impurities are two 980111997 22 201000649, finishing temperature: (Ar3 metamorphic temperature - 30) above °C, coiling temperature: 400~750 ° (3) hot rolling, after pickling, cold rolling, and then continuous annealing with overaging treatment, followed by rolling rate: 20~50% The second time Cold rolling. 098111997 23 201000649 IV. Designation of representative drawings: (1) The representative representative of the case is: No (2) Simple description of the symbol of the representative figure: No. 5. If there is a chemical formula in this case, please reveal the characteristics that can best show the invention. Chemical formula: none 098111997 2