US20150064448A1

US20150064448A1 - High strength and high formability steel sheet and manufacturing method thereof

Info

Publication number: US20150064448A1
Application number: US14/382,363
Authority: US
Inventors: Takumi Tanaka; Katsumi Kojima; Yoichi Tobiyama
Original assignee: JFE Steel Corp
Current assignee: JFE Steel Corp
Priority date: 2012-04-06
Filing date: 2013-04-03
Publication date: 2015-03-05
Also published as: TW201410879A; CN104245985B; EP2835438A4; CN104245985A; TWI473889B; EP2835438A1; CO7061066A2; WO2013151085A1; JPWO2013151085A1; MY185149A; KR20140117602A; EP2835438B1; JP5804195B2

Abstract

A high strength and high formability steel sheet contains, by mass % of the steel sheet: greater than 0.020% and less than 0.040% of C; not less than 0.003% and not greater than 0.100% of Si; not less than 0.10% and not greater than 0.60% of Mn; not less than 0.001% and not greater than 0.100% of P; not less than 0.001% and not greater than 0.020% of S; not less than 0.005% and not greater than 0.100% of Al; and greater than 0.0130% and not greater than 0.0170% of N, wherein a remainder is Fe and inevitable impurities, and the steel sheet has: a tensile strength in a rolling direction of not lower than 520 MPa; an Erichsen value of not less than 5.0 mm; and a resin film layer at least on a side to be an inner surface of a can.

Description

TECHNICAL FIELD

This disclosure relates to a high strength and high formability steel sheet suitable for application to a steel sheet for easy open ends, and a manufacturing method thereof.

BACKGROUND

Among steel sheets used for beverage cans or food cans, a steel sheet referred to as a double reduced (DR) material may be used for lids, bottoms, bodies of three-pieced cans, drawn cans, or the like. With the DR material manufactured by a DR method of performing cold rolling again after annealing, sheet thickness can be made thin more easily than with a single reduced (SR) material manufactured only by temper rolling after annealing at a small reduction ratio. Thus, it is possible, using the DR material, to reduce costs of manufacturing cans. In the DR method, the cold rolling performed again after annealing causes work hardening. Thus, although a thin and hard steel sheet can be manufactured, its formability is less than the SR material.
As lids of beverage cans and food cans, easy open ends (EOEs) that can be opened easily are widely used. In manufacturing an EOE, it is necessary to form, by bulging, a rivet to attach a tab with which a finger is engaged. Steel sheets as materials for manufacturing cans are required to have strengths according to sheet thicknesses and, as for the DR material, a tensile strength of not lower than about 520 MPa is necessary to ensure an economic effect due to thinning thereof. It is difficult to ensure for conventional DR materials both of formability and strength as mentioned above and thus the SR material has been used for EOEs. However, demands for applying the DR material to EOEs also are currently increasing in terms of cost reduction.
With that background, Japanese Patent No. 3740779 discloses a steel sheet for easy open cans lids excellent in rivet formability, characterized in that its carbon content is not greater than 0.02% and its boron content is in a range of 0.010 to 0.020%, and a manufacturing method thereof, characterized in that second cold rolling is performed with a rolling reduction ratio of not greater than 30%. Moreover, WO 2008/018531 discloses a DR material characterized in that its average Lankford value after an aging treatment is not greater than 1.0, and describes that the DR material is excellent in EOE rivet formability.
However, the conventional techniques described above have problems. As a diameter of a can lid to be applied becomes greater, a greater strength is required for a steel sheet, but since the steel sheet described in JP '779 has a small carbon content, the nitrogen content needs to be large to obtain a high strength. However, because the steel sheet contains at least a certain amount of boron, when the nitrogen content is large, its ductility at a high temperature becomes small and a slab crack is caused upon continuous casting. Therefore, the steel sheet described in JP '779 cannot be applied to an EOE having a large diameter.
The steel sheet described in WO '531 achieves good rivet formability by reducing the average Lankford value. However, that method exerts its effects only when a rivet is formed by column-like bulging, and when a rivet is formed by sphere-like bulging, the rivet formability becomes insufficient. Therefore, provision of a high strength and high formability steel sheet having a tensile strength of not lower than 520 MPa and an Erichsen value of not less than 5.0 mm has been desired.
It could therefore be helpful to provide a high strength and high formability steel sheet having a tensile strength of not lower than 520 MPa and an Erichsen value of not less than 5.0 mm and a manufacturing method thereof.

SUMMARY

We found that it is effective in achieving both formability and strength of a steel sheet, to ensure strength by increasing the nitrogen content while preventing deterioration of formability by restricting the carbon content to an appropriate range, and to restrict the second cold rolling reduction ratio after annealing to an appropriate range. Moreover, we found that it is necessary to restrict also the coiling temperature to an appropriate range because, when the coiling temperature after hot rolling is high, precipitated cementite becomes coarse and local elongation deteriorates. Furthermore, we found that rivet formability by bulging is remarkably improved by providing a resin film layer having an appropriate thickness on a side to be an inner surface of a can.
We thus provide:

- A high strength and high formability steel sheet includes, in mass %: greater than 0.020% and less than 0.040% of C; not less than 0.003% and not greater than 0.100% of Si; not less than 0.10% and not greater than 0.60% of Mn; not less than 0.001% and not greater than 0.100% of P; not less than 0.001% and not greater than 0.020% of S; not less than 0.005% and not greater than 0.100% of Al; greater than 0.0130% and not greater than 0.0170% of N; and a remainder being Fe and inevitable impurities, wherein the high strength and high formability steel sheet has: a resin film layer at least on a side to be an inner surface of a can; a tensile strength in a rolling direction of not less than 520 MPa; and an Erichsen value of not less than 5.0 mm.
- The thickness of the resin film layer is preferably 5 to 100 μm.
- A method of manufacturing a high strength and high formability steel sheet includes: forming a slab by continuously casting a steel including, in mass %: greater than 0.020% and less than 0.040% of C; not less than 0.003% and not greater than 0.100% of Si; not less than 0.10% and not greater than 0.60% of Mn; not less than 0.001% and not greater than 0.100% of P; not less than 0.001% and not greater than 0.020% of S; not less than 0.005% and not greater than 0.100% of Al; greater than 0.0130% and not greater than 0.0170% of N; and a remainder being Fe and inevitable impurities; performing hot rolling at a slab reheating temperature of not lower than 1150° C.; coiling at a temperature of not higher than 600° C.; thereafter performing first cold rolling; thereafter performing continuous annealing at a soaking temperature of 600 to 700° C. for a soaking period of 10 to 50 seconds; thereafter performing second cold rolling at a reduction ratio of 8.0 to 15.0%; attaching a resin film at least on a side to be an inner surface of a can after forming a surface treatment film by an electrolytic process; and manufacturing a steel sheet having a tensile strength in a rolling direction of not less than 520 MPa and an Erichsen value of not less than 5.0 mm.

According to the high strength and high formability steel sheet and the manufacturing method thereof, it is possible to obtain a high strength and high formability steel sheet having a tensile strength of not lower than 520 MPa and an Erichsen value of not less than 5.0 mm. Further, as a result, it is possible to manufacture a lid with a DR material having a small thickness, without cracking upon EOE rivet formation, and thus to achieve thinning of a steel sheet for EOEs to a great extent.

DETAILED DESCRIPTION

In the following, our steel sheets and methods are described in detail.
The high strength and high formability steel sheet can be applied to a steel sheet for easy open ends having tensile strength of not lower than 520 MPa and an Erichsen value of not less than 5.0 mm. Such a steel sheet can be manufactured with steel having carbon content of less than 0.040%, by setting the coiling temperature after hot rolling and the second cold rolling reduction ratio to appropriate conditions, and attaching a resin film on a side to become an inner surface of a can. In the following, the component composition of the high strength and high formability steel sheet is described.

Component Composition of High Strength and High Formability Steel Sheet

(1) C: Greater than 0.020% and Less than 0.040%
The high strength and high formability steel sheet exerts high formability by suppressing the carbon (C) content. When the C content is not less than 0.040%, a steel sheet becomes excessively hard, thus making it impossible to manufacture a thin steel sheet by second cold rolling while ensuring formability. Thus, the upper limit of C content is less than 0.040%. However, when the C content is not greater than 0.020%, the tensile strength of 520 MPa that is required to obtain significant economic effects resulted by thinning of a steel sheet cannot be obtained. Thus, the lower limit of C content is to exceed more than 0.020%.
(2) Si: Not Less than 0.003% and not Greater than 0.100%
When the silicon (Si) content exceeds 0.100%, there occur problems of deterioration of surface treatability, deterioration of corrosion resistance and the like. Thus, the upper limit of Si content is 0.100%. When Si content is less than 0.003%, refining cost is excessively high. Therefore, the lower limit of Si content is 0.003%. The preferable Si content is not less than 0.003% and not greater than 0.035%.
(3) Mn: Not Less than 0.10% and not Greater than 0.60%
Manganese (Mn) has functions of preventing red shortness during hot rolling due to sulfur (S) and of refining crystal grains, and is an element necessary to ensure the desirable quality of a material. The addition of at least 0.10% or more of Mn is required to exert such effects. However, when an excessive amount of Mn is added, the corrosion resistance deteriorates and a steel sheet becomes excessively hard. The upper limit of Mn amount is therefore 0.60%. The preferable Mn content is not less than 0.19% and not greater than 0.60%.
(4) P: Not Less than 0.001% and not Greater than 0.100%
Phosphorus (P) is a harmful element that hardens steel, and deteriorates formability and, in addition, also deteriorates corrosion resistance. Thus, the upper limit of P content is 0.100%. However, when the P content is less than 0.001%, the cost of dephosphorization becomes excessively high. The lower limit of P content is therefore 0.001%. The preferable P content is not less than 0.001% and not greater than 0.015%.
(5) S: Not Less than 0.001% and not Greater than 0.020%
S exists as inclusions in steel, and is a harmful element causing deterioration of formability and deterioration of corrosion resistance. The upper limit of S content is therefore 0.020%. When the S content is less than 0.001%, the cost of desulfurization becomes excessively high. The lower limit of S content is therefore 0.001%. The preferable P content is not less than 0.007% and not greater than 0.014%.
(6) Al: Not Less than 0.005% and not Greater than 0.100%
Aluminum (Al) is an element necessary as a deoxidizer in a steelmaking process. When the Al content is small, deoxidation is insufficient, and inclusions increase, thus deteriorating formability. When the Al content is not less than 0.005%, it can be considered that deoxidation is performed sufficiently. However, when the Al content exceeds 0.100%, the frequency of occurrence of surface defects due to alumina clusters and the like is increased. The Al content is therefore not less than 0.005% and not greater than 0.100%.
(7) N: Greater than 0.0130% and not greater than 0.0170%
In the high strength and high formability steel sheet, nitrogen (N) content is increased, instead of reducing C content, to ensure strength. Strengthening using N has small effects on bulging formability, and thus it is possible to strengthen a steel sheet without deteriorating an Erichsen value. When N content is not greater than 0.0130%, the strength necessary for a can lid cannot be obtained. However, when a large amount of N is added, the hot ductility deteriorates, thus causing a slab crack in continuous casting. The upper limit of N content is therefore 0.0170%.

(8) Other Components

The balance other than the components described above is iron (Fe) and inevitable impurities, and may include component elements normally contained in a known steel sheet for welded cans. For example, the component elements such as chromium (Cr): not greater than 0.10%, copper (Cu): not greater than 0.20%, nickel (Ni): not greater than 0.15%, molybdenum (Mo): not greater than 0.05%, titanium (Ti): not greater than 0.3%, niobium (Nb): not greater than 0.3%, zirconium (Zr): not greater than 0.3%, vanadium (V): not greater than 0.3%, calcium (Ca): not greater than 0.01%, may be contained depending on a purpose.

Characteristics of High Strength and High Formability Steel Sheet

Next, the mechanical characteristics of the high strength and high formability steel sheet are described.
The tensile strength of the high strength and high formability steel sheet is not lower than 520 MPa. When the tensile strength is lower than 520 MPa, a steel sheet cannot be made thin enough to obtain significant economic effects to ensure the strength of the steel sheet as a material for manufacturing lids. The tensile strength is therefore not lower than 520 MPa. The above tensile strength can be measured by Metallic materials-Tensile testing defined by “JIS Z 2241.”
The Erichsen value of the high strength and high formability steel sheet is not less than 5.0 mm. When the Erichsen value is smaller than 5.0 mm, a crack occurs in rivet formation. The Erichsen value is therefore not less than 5.0 mm. The Erichsen value can be measured by Method of Erichsen cupping test defined by “JIS Z 2247.” In rivet formation, the processing form applied on a steel sheet is bulging, which can be regarded as tensile deformation toward all directions parallel to a sheet surface. The evaluation of deformability of a steel sheet by such processing requires a test by similar bulging, and the deformability cannot be evaluated with a total elongation value or a Lankford value by the simple uniaxial tensile testing.

Surface Coating of High Strength and High Formability Steel Sheet

Next, the surface coating of the high strength and high formability steel sheet is described.
Rivet formation is performed by bulging, and processing for bulging toward the outer side of a can is performed. In the processing, therefore, a steel sheet is deformed by a tool contacting the inner side surface of the can. The lubricating ability between a tool and a steel sheet is improved by contacting them with a resin film interposed therebetween. Thus, uniformity of bulging is improved, effectively suppressing the occurrence of a crack. It is more preferable that a surface of a steel sheet be coated with a resin film in addition to interposing a resin film between a tool and a steel sheet, because those contribute to corrosion resistance.
A resin film is not particularly limited, and various thermoplastic resins and thermosetting resins can be used. For example, there may be used an olefin resin film such as of polyethylene, polypropylene, ethylene-propylene copolymer, ethylene-vinyl acetate copolymer, ethylene-acrylic ester copolymer, and ionomer, or a polyester film such as of polybutylene terephthalate, or a thermoplastic resin film including a polyamide film such as of nylon 6, nylon 6-6, nylon 11, and nylon 12, a polyvinylchloride film, and a polyvinylidene chloride film without stretching them or by stretching them biaxially.
When an adhesive is used to attach a resin film on a steel sheet, an urethane adhesive, an epoxy adhesive, an acid-modified olefin resin adhesive, a copolyamide adhesive, a copolyester adhesive (thickness: 0.1 to 5.0 μm) and the like are used preferably. Moreover, thermosetting coating is applied on the steel sheet side or the resin film side with a thickness of 0.05 to 2.0 μm, and this may be regarded as an adhesive. Moreover, thermoplastic or thermosetting coating including modified epoxy coating such as of phenol epoxy and amino-epoxy, vinyl chloride-vinyl acetate copolymer, vinyl chloride acetate saponified copolymer, vinyl chloride-vinyl acetate-maleic anhydride copolymer, epoxy modified-, epoxy amino modified-, epoxy phenol modified-vinyl coating or modified vinyl coating, acryl coating, and a synthetic rubber coating such as of styrene-butadiene copolymer may be used individually or in combination of two or more thereof.
The thickness of a resin film is preferably 5 to 100 μm. When the thickness of a resin film is smaller than 5 μm, the resin film is fractured in bulging, and it is more possible that the effects are not exerted sufficiently. When the thickness of a resin film exceeds 100 μm, the effect of increasing a deformation amount of a steel sheet becomes greater, and a crack of the steel sheet will occur more easily.

Manufacturing Method of High Strength and High Formability Steel Sheet

Next, the manufacturing method of the high strength and high formability steel sheet is described.
The high strength and high formability steel sheet is manufactured, with use of a steel slab having the above composition manufactured by continuous casting, by performing hot rolling at a slab reheating temperature of not lower than 1150° C., coiling it at a temperature of not higher than 600° C., performing first cold rolling, performing continuous annealing at a soaking temperature of 600 to 700° C. for a soaking period of 10 to 50 seconds, performing second cold rolling with a reduction ratio of 8.0 to 15.0%, forming a surface treatment film by an electrolytic process, and then attaching a resin film at least on a side to become an inner surface of a can.
It is normally difficult, with only one-time cold rolling, to make a sheet thin enough to obtain significant economic effects. That is, to obtain a thin sheet with one-time cold rolling, the load on a mill becomes too high, and it is impossible to achieve it depending on a plant capacity. For example, when a final sheet thickness is made 0.15 mm, the first cold reduction ratio of as much as 92.5% is required if a sheet thickness after hot rolling is 2.0 mm. It can be also considered that a sheet is rolled to be thinner than usual at the step of hot rolling to reduce a sheet thickness after cold rolling. However, when the reduction ratio in hot rolling is increased, the reduction of a temperature of a steel sheet during rolling becomes great, and a given finish rolling temperature cannot be obtained. Moreover, when continuous annealing is performed, the possibility of the occurrence of troubles such as fracture or deformation of a steel sheet during annealing becomes higher if a sheet thickness before annealing is small. For these reasons, it is preferable that the cold rolling for the second time (second cold rolling) be performed after annealing to obtain an ultrathin steel sheet.
When a coiling temperature after hot rolling exceeds 600° C., a pearlite structure to be formed becomes coarse, which is a starting point of brittle fracture and thus reduces local elongation, making it difficult to obtain an Erichsen value of not less than 5.0 mm. The coiling temperature after hot rolling is therefore preferably not higher than 600° C., and is more preferably 550 to 600° C.
When the soaking temperature of continuous annealing is lower than 600° C. or the soaking period thereof is shorter than 10 seconds, recrystallization is insufficient, thus making it difficult to obtain an Erichsen value of not less than 5.0 mm. However, when the soaking temperature exceeds 700° C. or the soaking period exceeds 50 seconds, the grain growth through recrystallization becomes excessive, thus making it difficult to obtain the tensile strength of 520 MPa. The continuous annealing is therefore preferably performed under conditions of a soaking temperature of 600 to 700° C. and a soaking period of 10 to 50 seconds.
When the second cold rolling reduction ratio exceeds 15.0%, work hardening by the second cold rolling becomes excessive, thus making it difficult to obtain an Erichsen value of not less than 5.0 mm. The second cold rolling reduction ratio is therefore preferably not greater than 15.0%. However, when the second cold rolling reduction ratio is less than 8.0%, it is difficult to obtain strength necessary for a can lid. Thus, the lower limit of the second cold rolling reduction ratio is preferably 8.0%.
After the second cold rolling, a surface treatment film is formed by an electrolytic process. As a film, a Sn electroplating film, an electrolytic Cr acid treatment film, or the like, which is widely used for a can lid as a tin plate or tin-free steel, can be applied. Adherence between a resin film and a steel sheet can be improved by providing such a film.
After the surface treatment film is formed, a resin film is attached at least on a side to become an inner surface of a can. The attachment method can be a method of heating a steel sheet and heat-sealing a resin film, or a method of attaching it using an adhesive.

Examples

A steel slab was obtained by melting steel having the component compositions illustrated in Table 1 and the balance including Fe and inevitable impurities in an actual converter and subjecting it to continuous casting. The obtained steel slab was heated again and subjected to hot rolling under the conditions illustrated in Table 2. A finish rolling temperature of hot rolling was set at 880° C., and pickling was performed after the rolling. Next, after first cold rolling was performed with a reduction ratio of 90%, continuous annealing and second cold rolling were performed under the conditions illustrated in Table 2. The electrolytic Cr acid treatment was continuously performed on the both surfaces of the steel sheet obtained in the above manner, whereby tin-free steel having a Cr coating build-up per side of 100 mg/m²was obtained. Then, an isophthalic acid copolymerized polyethylene terephthalate film having a copolymerization ratio of 12 mol % was laminated on the both surfaces, and thus a resin coated steel sheet was obtained. The laminating was performed such that a steel sheet heated to 245° C. and a film were nipped by a pair of rubber covered rolls so that the film was fused to the metallic sheet, and the laminate was cooled with water within one second after it passed the rubber covered rolls. A feed rate of the steel sheet was 40 m/min, and the nip length of the rubber covered rolls was 17 mm. The nip length is a length in a feed direction of a part where the rubber covered rolls and the steel sheet are in contact. The thickness of film layers was listed in Table 1.

TABLE 1

		Thickness
		of resin
	Component composition (mass %)	film

No.	C	Si	Mn	P	S	Al	N	layer (μm)

1	0.031	0.011	0.29	0.009	0.010	0.039	0.0153	18
2	0.021	0.010	0.23	0.010	0.012	0.018	0.0161	24
3	0.039	0.012	0.25	0.009	0.010	0.025	0.0140	15
4	0.026	0.008	0.28	0.012	0.008	0.042	0.0170	5
5	0.035	0.009	0.30	0.013	0.011	0.048	0.0131	51
6	0.029	0.010	0.19	0.010	0.012	0.041	0.0148	100
7	0.020	0.011	0.26	0.011	0.009	0.040	0.0152	30
8	0.040	0.013	0.25	0.010	0.010	0.051	0.0160	29
9	0.032	0.012	0.27	0.009	0.011	0.044	0.0130	19
10	0.028	0.010	0.22	0.012	0.010	0.038	0.0175	—
11	0.035	0.014	0.27	0.010	0.009	0.033	0.0162	20
12	0.029	0.011	0.25	0.011	0.012	0.054	0.0159	36
13	0.030	0.009	0.24	0.013	0.014	0.064	0.0141	14
14	0.031	0.008	0.21	0.010	0.010	0.050	0.0135	27
15	0.022	0.010	0.30	0.012	0.011	0.042	0.0155	43
16	0.026	0.012	0.28	0.008	0.012	0.040	0.0152	26
17	0.033	0.011	0.25	0.010	0.009	0.034	0.0143	39
18	0.037	0.010	0.31	0.011	0.010	0.032	0.0148	3
19	0.034	0.013	0.24	0.009	0.013	0.041	0.0151	112

*Due to occurrence of slab crack in steel sheet No. 10 in continuous casting, operations thereafter were not performed.

TABLE 2

	Hot rolling			Second cold
	coiling	Continuous	Continuous	rolling
	temperature	annealing soaking	annealing soaking	reduction
No.	(° C.)	temperature (° C.)	period (second)	ratio (%)

1	582	668	21	11.5
2	589	685	21	9.8
3	575	698	10	8.3
4	598	621	23	10.6
5	552	605	49	14.9
6	563	654	22	12.7
7	584	620	23	13.1
8	571	683	21	11.1
9	591	667	21	10.9
10	—	—	—	—
11	604	644	22	9.2
12	585	598	24	12.2
13	587	703	15	14.0
14	592	683	9	12.5
15	566	672	52	10.3
16	570	658	22	7.8
17	581	631	23	15.5
18	590	689	21	13.3
19	588	690	21	10.1

*Due to occurrence of slab crack in steel sheet No. 10 in continuous casting, operations thereafter were not performed.

The resin coated steel sheet obtained as described above was subjected to tensile testing. The tensile testing conforms to Metallic materials-Tensile testing defined by “JIS Z 2241,” and strength of tension (tensile strength) was measured using a test piece for tensile testing having a size of JIS5. Moreover, the obtained resin coated steel sheet was subjected to Erichsen test. The Erichsen test conforms to Method of Erichsen cupping test defined by “JIS Z 2247,” and an Erichsen value (a bulging height at which a penetration crack occurred) was measured using a test piece of 90 mm×90 mm. Furthermore, a rivet to attach an EOE tab was formed using the obtained resin coated steel sheet, and the rivet formability was evaluated. Rivet formation was performed by three phases of press working, and processing to reduce the diameter was performed after bulging to form a spherical-head-formed rivet having a diameter of 4.0 mm and a height of 2.5 mm. Occurrence of a crack in a rivet portion was evaluated as “C,” occurrence of necking in a thickness direction, which is a previous stage leading to a crack, was evaluated as “B,” and no occurrence of a crack or necking in a thickness direction was evaluated as “A.” The obtained results are listed in Table 3.

TABLE 3

	Tensile	Erichsen	Rivet
No.	strength (MPa)	value (mm)	formability

1	552	6.9	A	Example
2	535	7.4	A	Example
3	523	7.6	A	Example
4	539	7.0	A	Example
5	591	5.2	A	Example
6	557	6.5	A	Example
7	516	6.2	A	Comparative
				Example
8	592	4.8	C	Comparative
				Example
9	517	7.3	A	Comparative
				Example
10	—	—	—	Comparative
				Example
11	532	4.2	C	Comparative
				Example
12	595	4.8	C	Comparative
				Example
13	512	6.1	A	Comparative
				Example
14	603	4.9	C	Comparative
				Example
15	515	7.2	A	Comparative
				Example
16	517	7.9	A	Comparative
				Example
17	599	4.9	C	Comparative
				Example
18	564	6.0	B	Examples
				of Claims 1 and 3
				Comparative
				Example of Claim 2
19	538	7.3	B	Examples
				of Claims 1 and 3
				Comparative
				Example of Claim 2

*Due to occurrence of slab crack in steel sheet No. 10 in continuous casting, operations thereafter were not performed.

As listed in Table 3, the steel sheets of Examples No. 1 to No. 6 are excellent in strength, and achieve tensile strength of not lower than 520 MPa that is required as an ultrathin steel sheet for cans. Moreover, they are also excellent in formability, and have an Erichsen value of not less than 5.0 mm that is required in EOE processing. Furthermore, even if the rivet formation is performed, no crack or necking in a thickness direction occurs. By contrast, each of the steel sheets of Comparative Examples No. 7 and No. 9 has such small C and N content that they are lacking in tensile strength. The steel sheet of Comparative Example No. 8 has such large C content that the formability is deteriorated by second cold rolling, resulting in the lack in Erichsen value and thus causing a crack in rivet formation.
The steel sheet of Comparative Example No. 10 has such large N content that a slab crack has occurred in continuous casting. Regarding the steel sheet of Comparative Example No. 11, the local elongation deteriorates because the coiling temperature after hot rolling is too high, resulting in the lack in Erichsen value and thus causing a crack in rivet formation. Regarding the steel sheet of Comparative Example No. 12, recrystallization is insufficient because the soaking temperature in continuous annealing is too low, resulting in the lack in Erichsen value and thus causing a crack in rivet formation. Regarding the steel sheet of Comparative Example No. 13, grain growth is excessive because the soaking temperature in continuous annealing is too high, resulting in the lack in tensile strength. Regarding the steel sheet of Comparative Example No. 14, recrystallization is insufficient because the soaking period in continuous annealing is too short, resulting in the lack in Erichsen value and thus causing a crack in rivet formation.
Regarding the steel sheet of Comparative Example No. 15, grain growth is excessive because the soaking period in continuous annealing is too long, resulting in the lack in tensile strength. The steel sheet of Comparative Example No. 16 is lacking in tensile strength because the second cold rolling reduction ratio is too small. Regarding the steel sheet of Comparative Example No. 17, work hardening becomes excessive because the second cold rolling reduction ratio is too high, resulting in the lack in Erichsen value and thus causing a crack in rivet formation. Regarding the steel sheet of No. 18 that is Example of claims 1 and 3 and is Comparative Example of claim 2, the thickness of the resin film coating the surface of the steel sheet is too thin, and thus the effects thereof are not sufficiently exerted in rivet formation, causing necking in a thickness direction before leading to a crack. Regarding the steel sheet of No. 19 that is Example of claims 1 and 3 and is Comparative Example of claim 2, the thickness of the resin film coating the surface of the steel sheet is too thick, and thus the deformation amount of the steel sheet is increased in rivet formation, causing necking in a thickness direction before leading to a crack.
Based on the above, it was confirmed that according to the steel sheets of the Examples, it is possible to obtain a high strength and high formability steel sheet having tensile strength of not lower than 520 MPa and an Erichsen value of not less than 5.0 mm.
The examples to which our steel sheets and methods are applied have been described. However, this disclosure is not limited by the description that forms a part of the disclosure. That is, other examples and operation technologies that are made based on this disclosure by those skilled in the art are all included in the scope of the appended claims.

INDUSTRIAL APPLICABILITY

It is possible to provide a high strength and high formability steel sheet having tensile strength of not lower than 520 MPa and an Erichsen value of not less than 5.0 mm.

Claims

1. A high strength and high formability steel sheet comprising:

a steel sheet layer comprising, in mass %, greater than 0.020% and less than 0.040% of C;

not less than 0.003% and not greater than 0.100% of Si;

not less than 0.10% and not greater than 0.60% of Mn;

not less than 0.001% and not greater than 0.100% of P;

not less than 0.001% and not greater than 0.020% of S;

not less than 0.005% and not greater than 0.100% of Al;

greater than 0.0130% and not greater than 0.0170% of N;

a remainder being Fe and inevitable impurities; and

a resin film layer on at least one side of the steel sheet layer;

the steel sheet having:

a tensile strength in a rolling direction of not less than 520 MPa; and

an Erichsen value of not less than 5.0 mm.

2. The steel sheet according to claim 1, wherein thickness of the resin film layer is 5 to 100 μm.

3. A method of manufacturing a high strength and high formability steel sheet comprising:

forming a slab by continuously casting a steel including, in mass %:

greater than 0.020% and less than 0.040% of C;

not less than 0.003% and not greater than 0.100% of Si;

not less than 0.10% and not greater than 0.60% of Mn;

not less than 0.001% and not greater than 0.100% of P;

not less than 0.001% and not greater than 0.020% of S;

not less than 0.005% and not greater than 0.100% of Al;

greater than 0.0130% and not greater than 0.0170% of N; and

a remainder being Fe and inevitable impurities;

performing hot rolling at a slab reheating temperature of not lower than 1150° C.;

coiling at a temperature of not higher than 600° C.;

thereafter performing first cold rolling;

thereafter performing continuous annealing at a soaking temperature of 600 to 700° C. for a soaking period of 10 to 50 seconds;

thereafter performing second cold rolling at a reduction ratio of 8.0 to 15.0%;

attaching a resin film on at least one side of the steel sheet to be an inner surface of a can after forming a surface treatment film by an electrolytic process

such that the steel sheet has a tensile strength in a rolling direction of not less than 520 MPa and an Erichsen value of not less than 5.0 mm.