JPH0835039A - Steel sheet for can manufacturing, excellent in baking hardenability and aging resistance and having high strength and high workability, and its production - Google Patents

Abstract

PURPOSE:To produce a steel sheet for can manufacturing, excellent in baking hardenability and aging resistance and having high strength and high workability, by preparing a steel sheet for can manufacturing, in which the contents of components are specified and also metallic structure and sheet thickness are respectively specified. CONSTITUTION:A steel sheet, consisting of, by weight, 0.05-0.15% C, >0.10-0.30% Si, 0.05-1.20% Mn, 0.015-0.150% P, <=0.010% S, 0.020-0.150% Al, <=0.0100% N, and the balance iron with inevitable impurities, is prepared. At this time, the structure of this steel sheet is composed of a mixed structure consisting of ferritic phases of <=15mum average crystalline grain size and pearlitic phases finely and uniformly dispersed among ferritic crystalline grains or pearlitic phases containing <=5vol.% bainitic phases and finely and uniformly dispersed among ferritic crystalline grains, and sheet thickness is regulated to <=0.30mm. By this method, the steel sheet for can manufacturing, excellent in baking hardenability and aging resistance and having high strength and high workability, can be obtained, and a product having sufficient can strength at the time of use after can manufacturing can be produced.

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a property that the yield stress of a material is increased by baking coating performed during can making, that is, it is excellent in so-called bake hardenability, and the structure of the material is hard to change with time. TECHNICAL FIELD The present invention relates to a high strength and high workability steel sheet for cans having excellent aging resistance and a method for producing the same. Si is an element that deteriorates the surface properties of steel sheets, and its use has been shunned in the past, but the ultra-high pressure descaling technology and the temperature control technology for rolled steel sheets have made remarkable progress, and it is possible to increase the Si content. Therefore, the present invention aims to stabilize the mixed structure of steel by positively containing Si in the steel material.

[0002]

2. Description of the Related Art In general, a can-making steel plate is required to have excellent workability during can making (high workability) and sufficient can strength after use (high strength). In addition to this, it is desirable that it is excellent in bake hardenability and aging resistance. In order to increase the strength of the steel sheet for can making, it is general to manufacture it by a double cold rolling method as described in JP-B-38-8563. However, since this steel plate is intended to have high strength by strengthening work, it is thermally unstable, its bake hardenability and aging resistance are unfavorable, and its workability is poor.

Therefore, Japanese Patent Application Laid-Open No. 59-50125 discloses that
An example of developing a steel sheet for can making which has both high strength and high workability is described. The method for producing a steel sheet for can manufacturing described in this publication forms a two-phase structure of a ferrite phase and an austenite phase by maintaining the temperature in the temperature range of 730 to 850 ° C after cold rolling and then quenching. It depends. This steel sheet for can making is aimed at satisfying both high strength and high workability by adjusting the precipitation ratio of the highly ductile ferrite phase and the hardened precipitation phase (martensite phase). is there.

[0004]

However, in the steel sheet for can-making manufactured by the manufacturing method described in the above-mentioned publication, the precipitation ratio of the ferrite phase and the precipitation phase can be controlled, but the ferrite crystal grains are not separated from each other. The existing precipitation phase tends to be finally layered by processing such as rolling, and it is difficult to make the layered precipitation phase into a uniform fine dispersion state by this manufacturing method. This layered structure is not preferable for workability, and the in-plane anisotropy due to the processing becomes large. Therefore, when this steel sheet is applied to a two-piece DI can or the like, non-earring during deep drawing is performed. Depending on the application, such as deterioration in sex, it became an obstacle during use. Further, the steel sheet for can making described in the above-mentioned publication is excellent in bake hardenability, but since the thermodynamically unstable precipitation phase is precipitated by quenching, the structure is thermally unstable. , Aging may cause a structural change. In addition, since the martensite is too hard, there is a strong tendency for the variation in the material to increase. As a result, in some cases, it is not preferable because it may cause defective formation during or after can making.

Therefore, an object of the present invention is to control the precipitation ratio of a ferrite phase and a precipitation phase (mainly a pearlite phase) and to control the precipitation phase existing between ferrite crystal grains.
It is to obtain a high-strength and high-workability steel sheet for cans, which is excellent in both bake hardenability and aging resistance, and a method for producing the same, by uniformly and finely dispersing and precipitating.

[0006]

In view of the above object, the inventors can satisfy the above-mentioned various properties required for a steel sheet for can making by optimizing the compositional components, the steel structure, and the production conditions. Found.

That is, the steel sheet for high strength and high workability according to the present invention has a C content of 0.05 to 0.15 wt% and a Si content of more than 0.10 wt% and 0.30.
wt% or less, Mn: 0.05 to 1.20 wt%, P: 0.015 to 0.150 wt
%, S: 0.010 wt% or less, Al: 0.020 to 0.150 wt%, N: 0.0100 wt% or less, and the balance consisting of unavoidable impurities and iron, and a ferrite phase having an average grain size of 15 μm or less, and a ferrite crystal. The pearlite phase is uniformly and finely dispersed among the grains, or a mixed structure with the pearlite phase that contains 5 vol% or less of the bainite phase and is uniformly and finely dispersed between the ferrite crystal grains, and the plate thickness is 0.30 mm or less.

The steel sheet has a C content of 0.05 to 0.15 wt%,
Si: over 0.10wt% and under 0.30wt%, Mn: 0.05-1.20wt%,
P: 0.015 to 0.150 wt%, S: 0.010 wt% or less, Al: 0.
020 to 0.150 wt%, N: 0.0100 wt% or less, Cu: 0.050 to 0.500 wt%, Ni: 0.050 to 0.500 wt%, C
It is preferable that at least one of r: 0.050 to 1.000 wt% and B: 0.0005 to 0.0030 wt% is contained, and the balance is inevitable impurities and iron.

The method for producing a steel sheet for cans according to the present invention having a high strength and a high workability is C: 0.05 to 0.15 wt%, Si: more than 0.10 wt% and 0.30.
wt% or less, Mn: 0.05 to 1.20 wt%, P: 0.015 to 0.150 wt
%, S: 0.010 wt% or less, Al: 0.020 to 0.150 wt%,
N: 0.0100wt% or less, and the steel material consisting of the balance unavoidable impurities and iron is hot-rolled at a finishing temperature of 850 to 930 ° C, and then cooled to 50 ° C / s or more within 1 second. Cool at a speed of 540 ° C or less and wind in the temperature range of 400 ° C or more,
After performing the primary cold rolling at a reduction rate of 70 to 90% after pickling,
Ratio of the amount of austenite to the total amount of the amount of ferrite and the amount of austenite kept soaking for at least 20 seconds in the temperature range of (Ac ₁ + 10 ° C) to (Ac ₁ + 50 ° C) below 850 ° C. Is controlled within the range of 10 to 50 vol%, and then 70 ° C.
30% by rapidly cooling to a temperature of 400 ° C or less at a cooling rate of / s or more
The temperature is kept constant in the temperature range of 0 ° C. or higher for 20 to 60 seconds, normal annealing is performed, and then secondary cold rolling is performed at a reduction rate of 10 to 35%.

In the above manufacturing method, the steel material is C: 0.05.
~ 0.15wt%, Si: over 0.10wt%, 0.30wt% or less, Mn: 0.05
〜1.20wt%, P: 0.015〜0.150wt%, S: 0.010wt% or less, Al: 0.020〜0.150wt%, N: 0.0100wt% or less, and further Cu: 0.050〜0.500wt%, Ni: 0.050 to 0.5
00wt%, Cr: 0.050 to 1.000wt%, B: 0.0005 to 0.0030wt%
It is preferable to contain at least one of the above.

Further, the method for producing a steel plate for a can having high strength and high workability of the present invention, particularly when workability is more important,
C: 0.05 to 0.15 wt%, Si: more than 0.10 wt% and 0.30 wt% or less,
Mn: 0.05 to 1.20 wt%, P: 0.015 to 0.150 wt%, S: 0.
010wt% or less, Al: 0.020 to 0.150wt%, N: 0.0050wt%
The following, and after the steel material consisting of the balance unavoidable impurities and iron is hot-rolled to a finishing temperature of 850 to 930 ° C, it is cooled at a cooling rate of 50 ° C / s or more within 1 second.
540 ℃ or less Winding in the temperature range of 400 ℃ or more, pickling 70 ~
After performing the primary cold rolling at a reduction rate of 90%, the temperature is kept uniform for 20 seconds or more in the temperature range of 850 ° C or lower and (Ac ₁ + 10 ° C) to (Ac ₁ + 50 ° C), The ratio of the amount of austenite to the total amount of ferrite and austenite is 10
It is preferable to control the temperature within a range of up to 50 vol% and then rapidly cool to a temperature of 400 ° C or lower at a cooling rate of 70 ° C / s or more and maintain a constant temperature in the temperature range of 300 ° C or more for 20 to 60 seconds. .

In the above manufacturing method, the steel material is C: 0.05.
~ 0.15wt%, Si: over 0.10wt%, 0.30wt% or less, Mn: 0.05
-1.20wt%, P: 0.015-0.150wt%, S: 0.010wt% or less, Al: 0.020-0.150wt%, N: 0.0050wt% or less, and further Cu: 0.050-0.500wt%, Ni: 0.050 to 0.5
00wt%, Cr: 0.050 to 1.000wt%, B: 0.0005 to 0.0030wt%
It is more preferable to contain at least one of the above.

[0013]

The composition components described in the present invention are as follows:
The steel structure and the reasons for limiting the manufacturing conditions will be described separately. C: 0.05 to 0.15 wt% In order to obtain a satisfactory strength, it is necessary that the C content be 0.05 wt% or more, more preferably 0.08 wt% or more. However, since the C content tends to deteriorate the weldability as it increases, its upper limit is made 0.15 wt%. In addition,
In the C content, the ratio of the austenite amount to the total amount of the sum of the ferrite amount and the austenite amount is 10 to 50% when the soaking is maintained, and the precipitation phase is uniformly finely dispersed between ferrite crystal grains. Set to do.

Si: more than 0.10 wt% and not more than 0.30 wt% Si in the steel is stable in the ferrite phase and also has the function of eliminating C in the ferrite phase into the austenite phase. Therefore, the ferrite phase can be highly purified and the austenite phase can be stabilized by C, which is an element advantageous for obtaining a stable mixed structure of the ferrite phase and the precipitation phase (mainly pearlite phase). Is. On the other hand, on the other hand, the surface texture tends to be deteriorated, and thus the content had to be reduced in the past (conventional Si content: 0.10 wt% or less), but the inventors conducted various studies. As a result, by using a device with sufficient scale removal capacity during hot rolling, ensuring a sufficiently high finishing temperature, and further performing heat treatment after primary cold rolling at a relatively high temperature, a large amount of Si was added to the steel. Added to 0.30wt%
It has been found that the deterioration of the surface properties is not so problematic if it is below. It was also found that a steel sheet containing Si in an amount of more than 0.10 wt% has a wider welding current range than usual steel sheets when welding with a three-piece can, for example. Therefore, the Si content exceeds 0.10 wt% and 0.30 wt%
The range was as follows. In addition, when a better surface quality is required, it is desirable that the Si content be 0.20 wt% or less.

Mn: 0.05 to 1.20 wt% Mn is an element which is desirable to be added in order to finally obtain a target finely dispersed structure at a cooling rate during ordinary annealing. In the case of the present invention, it is an extremely thin steel sheet. Therefore, even with ordinary gas jet cooling, a relatively large cooling rate can be achieved, so it is not necessary to add a large amount of Mn for this purpose.
If the content is about 0.05 wt% or more, a target fine dispersed structure can be obtained. Also, the Mn content is 1.20 wt%
If it exceeds, the corrosion resistance of the steel plate is adversely affected and
The layered structure resulting from the cast segregation of Mn itself is not finally improved, and further the workability by cold rolling is reduced. Therefore, the Mn content is set to the range of 0.05 to 1.20 wt%. In the actual operation, 0.30 in consideration of operational stability in continuous annealing.
It is desirable to set it to wt% or more. Also, the upper limit of the amount of Mn added
It is desirable to set it to 0.80% from the viewpoint of workability.

P: 0.015 to 0.150 wt% P is a desirable element in terms of material because it is advantageous for increasing strength and is inexpensive, but if it exceeds 0.150 wt%, a layered structure due to segregation occurs. It is not preferable because it further promotes In addition, the lower limit is 0.015wt%, which takes into account the cost increase required for de-P treatment and improves the material quality.
More than that. Therefore, the P content is set to the range of 0.015 to 0.150 wt%. Further, in order to stably obtain a uniform fine structure, the P content is more preferably 0.080 wt% or less.

S: 0.010 wt% or less Since the S content deteriorates the corrosion resistance after can making and promotes the formation of the layered structure, the S content is preferably as small as possible. Particularly, the higher the strength of the steel sheet, the more the formation of the layered structure is promoted. Therefore, the S content is set to 0.010 wt% or less in consideration of the deterioration of cost efficiency in reducing S. When considering the flange formability, it is preferably 0.007 wt% or less.

Al: 0.020 to 0.150 wt% Al is an element necessary as a deoxidizing agent and for reducing inclusions. For sufficient steel cleaning, the Al content should be 0.02
It is necessary to set it to 0 wt% or more. On the other hand, if it exceeds 0.150 wt%, abnormal hardening of the steel and surface defects are likely to occur, which is not preferable for use as a steel sheet for cans. Therefore, Al
The content was 0.020 to 0.150 wt%. It should be noted that in order to stably reduce inclusions and stabilize the surface texture, 0.040 to 0.
It is desirable to set it in the range of 120 wt%.

N: 0.0100 wt% or less N has been conventionally used as a solid solution strengthening element. However, when annealing is carried out in a low temperature region below the transformation point as in the prior art, aging tends to occur, and especially secondary When the cold rolling rate was low, its addition was limited. However, under the manufacturing conditions of the present invention, it was found that aging can be suppressed even if the N content is increased to about 0.0100 wt% as compared with the conventional steel, and thereby the strength of the material is enhanced. Is possible, but 0.0100wt
If it exceeds%, the bake hardenability is improved, but the aging resistance tends to be deteriorated, and it is difficult to control the components, which causes a variation in the material. Therefore, the N content is 0.01
It was set to 00 wt% or less. In addition, in order to prevent the formation of blowholes, it is desirable to set it to 0.0080% or less. Further, when high workability is emphasized rather than high strength, the N content is preferably 0.0050 wt% or less, more preferably 0.0030 wt% or less.

In addition to the above-mentioned elements, Cu, Ni, Cr,
More preferably, at least one of B and B is contained. Cu: 0.050 to 0.500 wt% Cu is a desirable element that can strengthen the steel without impairing the ductility of the steel, and at the same time lowers the transformation point of the steel to relax the regulation of the finishing temperature during hot rolling. The effect of accelerating the formation of the mixed structure by the heat treatment after the primary cold rolling. This effect is recognized from the Cu content of 0.050 wt%, and when it exceeds 0.500 wt%, it is saturated and the effect becomes small. Therefore, increasing the Cu content insignificantly is
This is not desirable because it leads to an increase in the cost of melting steel. Therefore, the Cu content is set in the range of 0.050 to 0.500 wt%. Further, since Cu also has an effect of improving corrosion resistance, it is desirable to contain 0.10% or more in order to exert this effect.

Ni: 0.050 to 0.500 wt% Ni, like Cu, also has the effect of lowering the transformation point of steel, and contributes to the improvement of the material through the refinement of the structure. Although the range of Cu content is limited for the same reason as Cu, it is desirable to contain Ni in the range of Cu × (0.2 to 1.0) when the beauty of the surface is required. The effect of this Ni can be
It is obtained regardless of any combination with. When the surface beauty is required more strictly,
The range of (% Cu) x (0.5 to 1.0) is more desirable.

Cr: 0.050 to 1.000 wt% Cr also has the same effect as Cu and the effect of improving corrosion resistance.
The effect is recognized at 0.050 wt% or more, and it is saturated if it exceeds 1.000 wt%. Therefore, the Cr content is set to 0.050 to 1.000 wt%.

B: 0.0005 to 0.0030 wt% As is conventionally known, B has the effect of fixing N even if the coiling temperature after hot rolling is lowered, but in the present invention, this effect is In addition, it prevents abnormal growth of the structure during transformation in the two-phase region, and suppresses N from remaining in a solid solution state even when rapid cooling is performed after heat treatment to prevent material deterioration due to aging. It has the effect of preventing. The B content for exerting such an effect is 0.0005 wt% or more. If the B content is excessive, the in-plane anisotropy of the material tends to increase, so the B content is set to 0.0030 wt% or less so that no problem occurs. The effect of addition of B is exhibited either singly or simultaneously with Ni and Cu. When this steel sheet is subjected to deep drawing, it is preferably 0.0010 wt% or less particularly for applications where the occurrence of earrings is a problem.

Next, the structure of the steel according to the present invention will be described. Optimization of the steel structure is one of the important issues in the present invention. In the case of a steel structure, where the precipitation phase existing between ferrite crystal grains is a layered structure, the mechanical properties change discontinuously in the plate thickness direction. It is not preferable because it deteriorates the sex. Further, when the average grain size of ferrite crystal grains exceeds 15 μm, the earring characteristics after the secondary cold rolling are significantly deteriorated, and in addition to the important characteristics of the present invention, bake hardenability and aging resistance, Improvement cannot be achieved at the same time. On the other hand, the average particle size is 10μ
When it is not more than m, a remarkable increase in strength is obtained, which is more desirable. The cause of this is unknown, but it is considered to be based on a change in behavior of an interstitial solid solution element such as C segregated at the grain boundary. For the structure of steel, it is advantageous for workability and aging resistance that the precipitation phase is finally and finely dispersed between ferrite crystal grains. This precipitation phase is preferably pearlite from the viewpoint of the balance between strength and workability, but 5 vol% is included in the precipitation phase in order to improve the strength.
The following bainite may be contained, in which case significant material deterioration does not occur.

Finally, manufacturing conditions will be described. (1) Finishing temperature after hot rolling When the finishing temperature is less than 850 ° C, the formation of a layered structure is promoted, the steel structure becomes nonuniform, and the workability deteriorates. Further, if the finishing temperature exceeds 930 ° C., the material structure tends to become coarse, and the final product structure tends to become coarse accordingly, which is not preferable. Therefore, the finish rolling temperature is 850-93.
The range was 0 ° C. In order to stabilize the material of the width direction edge portion and the longitudinal direction front and rear end portions, it is more preferable to set the temperature in the range of 870 to 920 ° C.

(2) Cooling after hot rolling Cooling after hot rolling tends to coarsen the structure if it is not started within 1 second, which will reduce the strength of the final product. Workability also deteriorates. If the cooling rate is less than 50 ° C / s, sufficient strength cannot be obtained in the final product stage, so the cooling rate was set to 50 ° C / s or more.

(3) Winding temperature after cooling The winding temperature also affects the structure of the steel, and as a result, is a factor that determines the strength and workability of the final product.
It is important to optimize it. That is, if the coiling temperature is 540 ° C or less, a material with a uniform material and excellent strength and workability can be produced. However, if the coiling temperature is less than 400 ° C, the effect is almost saturated and good results are obtained. Operational obstruction factors such as the inability to obtain a perfect coil shape occur. Therefore, the coiling temperature after hot rolling is 540 ℃ or less, 40
The temperature was 0 ° C or higher.

(4) Primary Cold Rolling In cold rolling, a uniform and fine structure can be obtained after heat treatment by setting the rolling reduction to 70% or more. However, if the cold reduction exceeds 90%, the anisotropy of the mechanical properties of the steel sheet tends to increase. Therefore, the reduction ratio during cold rolling is 70-90.
%. In addition, in order to make the structure more uniform, it is desirable that the reduction rate is 82% or more.

(5) Heat Treatment After Primary Cold Rolling Heating Temperature and Soaking Hold Time The heating temperature is one of the important matters of the present invention. That is, the heating temperature is 850 ° C or lower and (Ac ₁ + 10 ° C) to (A
(c ₁ + 50 ° C) The temperature is set so that the soaking and holding time is 20 seconds or more, and the austenite amount during soaking is 10 to 50 vol%, so that the precipitation phase It is possible to obtain a finely dispersed structure. In order to control the amount of austenite during soaking within the range of 10 to 50 vol%, it is important to control the soaking time as well as the heating temperature. A stable material cannot be obtained unless a soaking time of at least 20 seconds is secured.

Cooling Rate The cooling rate is important from the viewpoint of controlling strength and aging. The cooling rate was set to 70 ° C / s or more in order to obtain desired bake hardenability as the strength increased. There is no particular restriction on the upper limit, but there is no problem as long as it is within a range that is generally achieved by gas jet cooling. Further, in order to obtain an extremely large strength increase, it is preferable to set the cooling rate to 100 ° C./s or more. In order to obtain bake hardenability, 40
It is rapidly cooled to 0 ° C or less at this cooling rate. Although the detailed reason is unknown, it is presumed that the rapid cooling to 400 ° C or lower can suppress the monotonous growth of pearlite during the cooling. In order to obtain a more remarkable strength increase, it is more desirable to rapidly cool to 350 ° C. or lower at this cooling rate.

Constant temperature holding temperature and its holding time After being cooled to 400 ° C. or less at the cooling rate, it is held at a constant temperature in the temperature range of 300 ° C. or more for a time of 20 to 60 s to increase the bake hardening amount. It is possible to suppress the deterioration of the material due to the aging at room temperature without damaging it.

(6) Rolling Conditions for Secondary Cold Rolling Secondary cold rolling is an important project for improving strength, and is also important for preventing material deterioration due to aging before working. By setting the reduction ratio during cold rolling to 10% or more, it is possible to almost completely suppress the occurrence of defects due to stretcher strain during processing. Desired mechanical properties can be obtained by adjusting the rolling reduction in the range of 10% or more. However, a rolling reduction of more than 35% is not preferable because the effect of improving the strength of the material by cold rolling cannot be sufficiently obtained, while the earring property is significantly deteriorated.
The difficulty of the rolling operation itself also increases rapidly. Therefore, the rolling reduction during the secondary cold rolling is set in the range of 10 to 35%.

[0033]

【Example】

Example 1 Steels having the components shown in Table 1 were melted in a converter, and the production conditions according to the present invention shown in Table 2, that is, hot rolling, cold rolling, heat treatment, and a reduction rate of 15% were used. Steel sheets A to I produced by sequentially performing secondary cold rolling and tin plating and steels having the components shown in Table 3 are melted in a converter, and production conditions according to the present invention shown in Table 4, that is, heat Steel plates J to R produced by sequentially performing hot rolling, cold rolling, heat treatment, temper rolling with a reduction rate of 0.50%, and tin plating were evaluated for bake hardenability and aging resistance. In addition, the non-earring property was also evaluated. The results are shown in Tables 5 and 6. The steel sheets A to R all have high strength and high workability, but the steel sheets A to I are manufactured with particular emphasis on strength, while the steel sheets J to R particularly emphasize workability. Manufactured by

As a comparative example, Table 5 shows a steel sheet a manufactured by the conventional method of cold rolling twice (reduction ratio of secondary cold rolling: 30%), and manufacturing conditions are shown in Table 2. The production conditions are the same as those of the present invention, but the results of evaluation of steel sheets b to h whose component compositions are out of the limited range of the present invention are also shown. Steel plate i manufactured by a conventional method by hot rolling (rolling reduction of secondary cold rolling: 30%), and steel plates j whose manufacturing conditions are the same as those of the present invention but whose composition is out of the limited range of the present invention The results of evaluating p and p are also shown. In addition, in Table 5 and Table 6,
For reference, the tensile properties are also shown.

The bake hardenability was evaluated by using a JIS No. 5 test piece, after applying a 2% pre-strain, aging treatment at 210 ° C. for 20 minutes, and the increase in deformation stress before and after the aging treatment. The aging resistance was evaluated by measuring the amount (%) of elongation at yield at the time of carrying out an aging treatment at 100 ° C. for 30 minutes without strain and performing a tensile test.
The smaller this elongation, the better the aging resistance. The non-earring property was measured by forming a cup with a punch diameter of 33 mm and a drawing ratio of 1.65 and measuring the earring ratio at this time. The earring rate is the difference between the maximum height Hmax of the cup Hmin and the minimum height Hmin of the cup Hmin-Hmin, and the minimum height H of the cup H
Expressed as a percentage when divided by min. The bake hardening amount (BH) should be about 3 kgf / mm ² or more, and the aging resistance should be 2% or less at the yield point elongation. Similarly, the tensile properties were evaluated using JIS No. 5 test pieces.

[0036]

[Table 1]

[0037]

[Table 2]

[0038]

[Table 3]

[0039]

[Table 4]

[0040]

[Table 5]

[0041]

[Table 6]

As is clear from the results of Tables 5 and 6,
Steel Plates A to I and Steel Plates J to R manufactured according to the present invention
Are excellent in all of the properties of bake hardenability, aging resistance, and non-earring property, as compared with the steel plates a and i shown in Comparative Examples, respectively. It can be seen that even in the case of h and the steel plates j to p, the overall performances thereof are excellent in a well-balanced manner, and also the strength and workability are equivalent to those of the comparative examples.

Further, the steel plates A to R of the present invention do not cause surface defects that are harmful to the steel plate for can making. Further, the microstructure observation of the steel sheets A to R of the present invention revealed that, although the steel sheets had different precipitation rates of pearlite as a precipitation phase, the pearlite phases were uniformly finely dispersed between ferrite crystal grains. It was found to have tissue.

The so-called two-piece cans and three-piece cans are generally known as the types of cans. The invention steel plates A to R are used as these two types of cans corresponding to commercially available 350 g cans. After molding, various investigations were conducted. (i) Two-piece can (DRD can, DTR can, DI can) (a) When using the steel sheets A to I of the present invention, only relatively shallow forming is possible, and ironing workability is equivalent to that of conventional steel sheets. there were. Further, the following findings were obtained. The relatively good ductility makes the canning process easier. (In the present invention steel sheet, the wrinkle occurrence frequency during forming was reduced to about 90% of the total number of cans.) ・ In the case of the present invention steel sheet, the canning process is stable because the aging property is small. Letcher strain does not occur.) ・ Since the in-plane anisotropy is small, ears are less likely to occur during can making and the yield is improved. -Since it has bake hardening properties, the final strength of the can itself is high.

(B) When the steel sheets J to R of the present invention are used (DI
Only cans are evaluated.) Good ductility makes the drawing process of cans easier. (In the invention steel sheet this time, the frequency of wrinkles during forming is about the total number of cans.
It was reduced to 70%. ) ・ In the case of the steel sheet of the present invention, the aging property is small, so the drawing process of the can is stable. -Since the in-plane anisotropy is small, ears are less likely to occur during can making and the yield is improved. -Strain propagation is more uniform due to low yield stress. -Since it has bake hardening properties, the final strength of the can itself is high.

(Ii) In the case of a three-piece can (a) In the case of using the invention steel sheets A to I-Since the aging property is small, the can manufacturing process is stable.・ A waist break does not occur. -Since it has bake hardening properties, the final strength of the can itself is high.・ Because the C content can be made relatively low, the weldability is good.

(B) Inventive Steel Sheets J to R are used: Since the aging property is small, the can manufacturing process is stable. -Strain propagation is more uniform due to low yield stress. -Since it has bake hardening properties, the final strength of the can itself is high.

In addition, in the case of a steel plate which is work-hardened only by secondary cold rolling according to the conventional manufacturing method as a comparative material,
Since the curing itself is thermally unstable, it may be accompanied by a sudden decrease in strength when subjected to heat treatment at a high temperature for a relatively long time. Further, in the case of the conventional double cold-rolled steel sheet, it is not easy to strictly control the reduction rate in the manufacturing process thereof, and therefore, the variation of the material is large and the final can strength is It was a major cause of variation.

On the other hand, the invention steel sheets A to I can be given a certain degree of strength by heat treatment.
Even if the reduction ratio in the secondary cold rolling was suppressed to a low level, sufficient strength could be obtained and material control became easier. Further, the invention steel sheets J to R basically do not require cold rolling after heat treatment, and the materials can be controlled with extremely high accuracy by controlling the steel composition and heat treatment conditions.

Example 2 Two kinds of invention steel sheets A and J were manufactured according to the invention (condition 1) and according to the invention shown in Table 7 (reduction ratio in secondary cold rolling: 15%) and Table 8, respectively. 15 # tinplate and
A 25 # tin plate was used and the same performance as in Example 1 was evaluated. The evaluation results are shown in Table 9 and Table 10, respectively.

[0051]

[Table 7]

[0052]

[Table 8]

[0053]

[Table 9]

[0054]

[Table 10]

As is clear from the results of Tables 9 and 10,
Steel plates A and J manufactured under the manufacturing condition 1 according to the present invention,
Manufacturing conditions 2 to 9 not according to the invention shown in Comparative Examples, respectively
Compared with the case of manufacturing in the same manner, it is superior in all properties of bake hardenability, aging resistance and non-earring property, and has strength and workability equivalent to or better than the comparative example. You can see that

Example 3 Inventive steel plate B and comparative steel plate a, and inventive steel plate M and comparative steel plate b were manufactured respectively within the manufacturing conditions according to the present invention, and these manufactured steel plates were used for beverage cans. The strength of the can when molded was evaluated.

(A) Inventive steel plate B and comparative steel plate a were molded into a 250 ml three-piece beverage can having an original plate thickness of 0.210 mm,
The axial load resistance strength and can body compressive strength of this can were evaluated. After the molding, a baking coating treatment of 205 ° C. × 20 min. Was performed. The axial load resistance strength is the buckling strength when the can is axially compressed. Can body compressive strength is 12.5 mmφ and length is
A 40 mm columnar body was pressed against the body of the can to apply a local pressure, and the critical load when the depression was generated was evaluated. The evaluation results are shown in Table 11.

[0058]

[Table 11]

From the evaluation results, it is understood that the invention steel sheet B has a higher final pressure resistance strength than the comparative steel sheet a, although the strength of the original sheet is lower than that of the comparative steel sheet a. In addition,
The steel sheet of the present invention is well adapted to the use in which an organic resin film is added to the surface (however, in that case, the surface treatment should be chromium plating instead of tin), especially. The invention steel sheet is excellent in that it is thermally stable in that the material does not deteriorate or fluctuate due to the heat treatment during the film attachment processing.

(B) Inventive steel sheet M and comparative steel sheet b were molded into a beverage can of 350 ml having a thickness of the original plate of 0.24 mm.
The axial load resistance and the bottom pressure resistance were evaluated. In addition,
After molding, baking treatment was performed at 200 ° C for 20 min. The bottom compressive strength is measured by applying hydrostatic pressure to the can to determine the critical stress that causes buckling at the bottom. Table 12 shows the results of these evaluations.

[0061]

[Table 12]

From the evaluation results, it is understood that the invention steel sheet M has a higher final pressure resistance strength than the comparative steel sheet b, although the strength of the original sheet is lower than that of the comparative steel sheet b.

[0063]

According to the present invention, it is possible to provide a steel plate for a can having high strength and high workability, which is excellent in bake hardenability and aging resistance.
Therefore, it becomes possible to manufacture a product having sufficient can strength when used after can manufacturing.

─────────────────────────────────────────────────── ─── Continuation of front page (51) Int.Cl. ⁶ Identification number Internal reference number FI Technical indication C22C 38/54 (72) Inventor Hideo Kuminato 1 Kawasaki-cho, Chuo-ku, Chiba-shi, Chiba Kawasaki Steel Stock Company Chiba Steel Works

Claims (6)

[Claims] 1. C: 0.05 to 0.15 wt%, Si: more than 0.10 wt% 0.
30wt% or less, Mn: 0.05 to 1.20wt%, P: 0.015 to 0.150wt%, S: 0.010wt% or less, Al: 0.020 to 0.150wt%, N: 0.0100wt% or less, and the balance inevitable impurities and iron And a ferrite phase with an average crystal grain size of 15 μm or less,
A pearlite phase uniformly dispersed between ferrite crystal grains,
Alternatively, it is composed of a mixed structure with a pearlite phase that contains 5 vol% or less of bainite phase and is finely dispersed between ferrite crystal grains, and has a plate thickness of 0.30 mm or less, which is excellent in bake hardenability and aging resistance. Workable steel plate for can manufacturing. 2. C: 0.05 to 0.15 wt%, Si: more than 0.10 wt% 0.
30 wt% or less, Mn: 0.05 to 1.20 wt%, P: 0.015 to 0.150 wt%, S: 0.010 wt% or less, Al: 0.020 to 0.150 wt%, N: 0.0100 wt% or less, and further Cu: 0.050 〜0.500wt%, Ni: 0.050〜0.500wt%, Cr: 0.050〜1.000wt%, B: 0.0005〜0.0030wt%, and the balance is inevitable impurities and iron. Has a mixed structure of a ferrite phase having an average of 15 μm or less and a pearlite phase uniformly finely dispersed between ferrite crystal grains, or a pearlite phase having a bainite phase of 5 vol% or less and uniformly finely dispersed between ferrite crystal grains. Steel plate for cans with a thickness of 0.30 mm or less, which is excellent in bake hardenability and aging resistance and has high strength and high workability. 3. C: 0.05 to 0.15 wt%, Si: more than 0.10 wt% 0.
30 wt% or less, Mn: 0.05 to 1.20 wt%, P: 0.015 to 0.150 wt%, S: 0.010 wt% or less, Al: 0.020 to 0.150 wt%, N: 0.0100 wt% or less, and the balance inevitable impurities and iron Or
Steel material with a hot finish of 850 to 930 ℃
Cooling speed of 50 ° C / s or more within 1 second after rolling
And cool it in the temperature range of 540 ℃ or less and 400 ℃ or more.
After performing the primary cold rolling at a reduction rate of 70 to 90% after pickling,
Below 850 ° C and (Ac₁+ 10 ° C) ~ (Ac ₁+ 50 ℃)
Austenite amount is maintained for 20 seconds or more in the temperature range.
The total amount of ferrite and austenite
Control the ratio to 10 to 50 vol% and then 70 ℃
30% by rapidly cooling to a temperature of 400 ° C or less at a cooling rate of / s or more
Maintain a constant temperature in the temperature range of 0 ° C or higher for 20 to 60 seconds.
Secondary cold rolling with a reduction rate of 10 to 35% after normal annealing.
Bake hardenability and aging resistance, characterized by being rolled
A method for producing a steel plate for cans with excellent strength and high workability. 4. C: 0.05 to 0.15 wt%, Si: more than 0.10 wt% 0.
30 wt% or less, Mn: 0.05 to 1.20 wt%, P: 0.015 to 0.150 wt%, S: 0.010 wt% or less, Al: 0.020 to 0.150 wt%, N: 0.0100 wt% or less, and further Cu: 0.050 ~ 0.500wt%, Ni: 0.050 ~ 0.500wt%, Cr: 0.050 ~ 1.000wt%, B: 0.0005 ~ 0.0030wt% At least one of the following is included, and the balance is a steel material consisting of unavoidable impurities and iron. After hot rolling at a temperature of 850 to 930 ℃, cool within 1 second at a cooling rate of 50 ℃ / s or more and wind it in the temperature range of 540 ℃ or less and 400 ℃ or more,
After performing the primary cold rolling at a reduction rate of 70 to 90% after pickling,
The temperature is kept at 850 ℃ or less and in the temperature range of (Ac ₁ +10 ℃) to (Ac ₁ +50 ℃) for 20 seconds or more, so that the ratio of austenite content to the total amount of ferrite content and austenite content is increased. Control in the range of 10 to 50vol%, then 70 ℃
300% by rapidly cooling to a temperature of 400 ° C or less at a cooling rate of / s or more
Bake hardenability, which is characterized by performing a constant cold holding for 20 to 60 seconds in a temperature range of ℃ or more, and further performing ordinary annealing and then performing secondary cold rolling at a rolling reduction of 10 to 35%. A method for producing a steel sheet for cans having high strength and high workability with excellent aging resistance. 5. C: 0.05 to 0.15 wt%, Si: more than 0.10 wt% 0.
30 wt% or less, Mn: 0.05 to 1.20 wt%, P: 0.015 to 0.150 wt%, S: 0.010 wt% or less, Al: 0.020 to 0.150 wt%, N: 0.0050 wt% or less, and the balance inevitable impurities and iron Or
Steel material with a hot finish of 850 to 930 ℃
Cooling speed of 50 ° C / s or more within 1 second after rolling
And cool it in the temperature range of 540 ℃ or less and 400 ℃ or more.
After performing the primary cold rolling at a reduction rate of 70 to 90% after pickling,
Below 850 ° C and (Ac₁+ 10 ° C) ~ (Ac ₁+ 50 ℃)
Austenite amount is maintained for 20 seconds or more in the temperature range.
The total amount of ferrite and austenite
Control the ratio to 10 to 50 vol% and then 70 ℃
30% by rapidly cooling to a temperature of 400 ° C or less at a cooling rate of / s or more
Keep the temperature constant above 0 ℃ for 20 to 60 seconds.
High strength with excellent bake hardenability and aging resistance
A method of manufacturing a steel plate for a highly workable can. 6. C: 0.05 to 0.15 wt%, Si: more than 0.10 wt% 0.
30 wt% or less, Mn: 0.05 to 1.20 wt%, P: 0.015 to 0.150 wt%, S: 0.010 wt% or less, Al: 0.020 to 0.150 wt%, N: 0.0050 wt% or less, and further Cu: 0.050 To 0.500wt%, Ni: 0.050 to 0.500wt%, Cr: 0.050 to 1.000wt%, B: 0.0005 to 0.0030wt%, and the balance is a steel material consisting of inevitable impurities and iron. After hot rolling to a finishing temperature of 850 to 930 ℃, cool it within 1 second at a cooling rate of 50 ℃ / s or more and wind it in the temperature range of 540 ℃ or less and 400 ℃ or more, and after pickling. After primary cold rolling at a rolling reduction of 70 to 90%, the temperature is below 850 ° C and (Ac ₁ +10 ° C) to (Ac ₁ +50 ° C)
The temperature of the austenite is kept soaking for 20 seconds or more to control the ratio of the sum of the amount of ferrite and the amount of austenite to the total amount of 10 to 50 vol%.
Rapidly cool to a temperature below 400 ° C at a cooling rate of ℃ / s or more
A method for producing a steel plate for a high-strength and high-workability can having excellent bake hardenability and aging resistance, which is characterized by maintaining a constant temperature in a temperature range of 300 ° C or higher for 20 to 60 seconds.