JP5262242B2 - Manufacturing method of steel plate for can manufacturing - Google Patents

Abstract

Provided is a method of manufacturing a steel sheet for cans, where excessively high strengthening due to work hardening in cold-rolling is avoided, and thickness variation in the longitudinal direction of a steel sheet coil is inhibited, in a reduction in the steel sheet manufacturing cost by omitting the recrystallization annealing step. The steel compositions contain, in mass%, C: 0.005% or less, Mn: 0.05 to 0.5%, Al: 0.01 to 0.10%, N: 0.0010 to 0.0070%, and B: 0.15xN to 0.75xN (0.20xN to 0.97xN in atomic ratio) and further contain either or both Nb: 4xC to 20×C (0.52xC to 2.58xC in atomic ratio) and Ti: 2xC to 10×C (0.50xC to 2.51×C in atomic ratio), and the balance is Fe and inevitable impurity elements. The steel is continuously cast into a slab, the slab is hot-rolled at a finishing temperature of not higher than Ar 3 transformation point, and the hot-rolled steel sheet is subjected to coiling, pickling, and then cold-rolling at a reduction of 50 to 96%.

Description

  The present invention relates to a method for manufacturing a steel plate for can making with excellent plate thickness accuracy, and particularly for applications in which the can height is drawn to the same extent as the can barrel diameter, or bent into a cylindrical or rectangular tube shape. The present invention relates to a method of manufacturing a steel plate for can making suitable for a use in which flange processing is performed after joining portions to form a can body.

Cans such as beverage cans, food cans, 18 liter cans, and pail cans can be roughly classified into two-piece cans and three-piece cans from the manufacturing method (process).
The two-piece can is a surface drawing steel plate that has been subjected to tin plating, chrome plating, metal oxide coating treatment, chemical conversion treatment, inorganic coating coating treatment, organic resin coating coating treatment, oil coating, etc., shallow drawing and DWI processing The can is composed of two parts in which the bottom of the can and the can body are integrally formed by processing such as DRD processing and a lid is attached thereto.
A three-piece can is a three-piece can that is formed by bending a surface-treated steel plate into a cylindrical shape or a rectangular tube shape and joining end portions to form a can body, and then attaching a canopy and a bottom cover to the can body.

  These cans have a relatively high ratio of material costs to can costs. Therefore, there is a strong demand for reducing the cost of steel sheets in reducing can costs. Here, it goes without saying that in the manufacture of a steel sheet, the cost increases as the number of processing steps increases. Especially, the annealing process which recrystallizes a steel plate at high temperature is a process which raises manufacturing cost since it requires many energy costs for heating. Therefore, a method of reducing the cost by omitting this step can be considered. However, steel sheets that are not recrystallized after cold rolling are in a state of excessively high strength due to work hardening and are not suitable for can manufacturing. In view of this, methods for obtaining a steel sheet with appropriate strength by appropriately controlling steel components and hot rolling conditions have been studied in the past.

For example, in Patent Document 1, Nb, which is a carbonitride-forming element, is added to ultra-low carbon steel, hot rolling is performed in a so-called α region below the Ar ₃ point, and annealing is not performed after cold rolling. The manufacturing method of the steel plate for cans characterized by these is disclosed. However, since the steel sheet obtained by the technique of Patent Document 1 is in a cold rolled state, it is inferior in ductility and does not have sufficient workability depending on the application.

As a technique for improving such a point, Patent Document 2 adds Nb and Ti as carbonitride-forming elements to ultra-low carbon steel, performs hot rolling at Ar ₃ points or less, performs cold rolling, A technique for improving ductility by annealing is disclosed. The low temperature annealing referred to here is performed at a temperature at which recrystallization does not occur, so that the energy cost for heating is reduced.
In Patent Document 3, carbon nitride-forming elements Nb, Ti, Zr, V, and B are added to ultra-low carbon steel, hot rolling is performed at an Ar ₃ point or less, cold rolling, and then recrystallization. A technique for performing annealing at a temperature below the temperature is disclosed.
JP-A-4-280926 JP-A-8-41549 JP-A-6-248339

A feature common to the background arts of Patent Documents 1 to 3 is that hot rolling is performed at a temperature of ₃ or less points of Ar using ultra-low carbon steel as a steel and further adding a carbonitride-forming element. However, the steel plate manufactured under these conditions has a problem that the plate thickness uniformity in the longitudinal direction of the steel plate coil is inferior. Further, the annealing after cold rolling performed in Patent Document 2 and Patent Document 3 is performed at a temperature higher than 400 ° C. according to the Examples, and at a relatively low temperature as compared with the conventional recrystallization annealing. Although it has been carried out, it is still a treatment at a high temperature, which is insufficient to sufficiently reduce the energy cost required for heating.

  The present invention has been made in view of such circumstances, and in order to reduce the steel sheet manufacturing cost by omitting the recrystallization annealing step, avoid excessive strengthening due to work hardening in cold rolling, It aims at providing the manufacturing method of the steel plate for can manufacturing which suppresses the plate | board thickness fluctuation | variation in a longitudinal direction, and exhibits the cost reduction effect by omission of a recrystallization annealing process to the maximum.

The gist of the present invention is as follows.
[1] Steel component is mass%, C: 0.005% or less, Mn: 0.05 to 0.5%, Al: 0.01 to 0.12%, N: 0.0010 to 0.0070 %, B: 0.15 × N to 0.75 × N (in atomic ratio, 0.20 × N to 0.97 × N), and Nb: 4 × C to 20 × C (in atomic ratio) 0.52 × C to 2.58 × C), Ti: 2 × C to 10 × C (in atomic ratio, 0.50 × C to 2.51 × C) Made of Fe and unavoidable impurity elements is made into a slab by continuous casting, hot rolled at a finishing temperature below the Ar ₃ transformation point, wound, pickled, and then cooled at a reduction rate of 50 to 96%. A method for producing a steel plate for can making, characterized by performing hot rolling.
[2] A method for producing a steel plate for can making according to [1], wherein the winding is performed at a temperature of 640 to 750 ° C.
[3] The method for producing a steel plate for canning according to [1] or [2], wherein heat treatment is performed at a temperature of 150 to 400 ° C. after the cold rolling.

  In the present invention, the percentages indicating the steel components are all mass%.

According to the present invention, the steel sheet manufacturing cost can be reduced by omitting the recrystallization annealing step. And the steel plate which suppressed the board thickness fluctuation | variation in the longitudinal direction of a steel plate coil is obtained.
As described above, the steel sheet that suppresses fluctuations in the plate thickness in the longitudinal direction of the steel sheet coil can be obtained by omitting recrystallization annealing, making it possible to manufacture steel sheets at a lower cost than before, and reducing the cost of the can itself. Can also contribute.

Hereinafter, the present invention will be described in detail.
The inventors of the present invention investigate the thickness variation in the longitudinal direction of the steel sheet coil when hot rolling a cold carbon steel added with a carbonitride-forming element at a temperature of ₃ points or less and further cold rolling. Thus, the present invention has been completed. The present invention is described in detail below.

First, the reasons for limiting the steel components will be described.
C: 0.005% or less
This invention is a manufacturing method of the steel plate for cans which aims at cost reduction by omitting a recrystallization annealing process. However, steel sheets that are not recrystallized after cold rolling are in an excessively high strength state due to work hardening and are inferior in ductility, and are not suitable for can manufacturing. Therefore, it is necessary to use steel having low strength in advance for the steel itself. Therefore, it is necessary to use an ultra-low carbon steel in which carbon having a high solid solution strengthening ability is reduced as a steel component. If C is more than 0.005%, the strength becomes excessively high after cold rolling and the ductility is inferior, and it is not suitable for can manufacturing. Therefore, the C content is 0.005% or less. Preferably, it is 0.003% or less. In addition, if steel with low strength is used in advance for steel itself, the lower the content of C, the better. However, in order to reduce the C content, it takes time for decarburization operation and increases the manufacturing cost. Much. Therefore, the lower limit of the C content is preferably 0.0005% or more, more preferably 0.0015% or more.
Mn: 0.05 to 0.5%
If the Mn content is less than 0.05%, it is difficult to avoid so-called hot brittleness even if the S content is reduced, and problems such as surface cracks may occur. On the other hand, if it exceeds 0.50%, the transformation point is too low, and it becomes difficult to obtain a desired structure when rolling below the transformation point. Therefore, the Mn content is 0.05% or more and 0.50% or less. In addition, when the workability is particularly important, the content is preferably 0.20% or less.
S: 0.008% or less (preferred conditions)
S does not particularly affect the steel sheet characteristics of the present invention. However, when the amount of S exceeds 0.008%, when the amount of N exceeds 0.0044%, a large amount of generated MnS is used as a precipitation nucleus to form nitrides and carbonitrides BN, Nb ( C, N), AlN precipitates, reducing the hot ductility. Therefore, the S amount is desirably 0.008% or less.
Al: 0.01 to 0.12%
If the Al content is less than 0.01%, a sufficient deoxidation effect cannot be obtained. Moreover, the effect of reducing the solid solution N in steel by forming N and AlN cannot be sufficiently obtained. On the other hand, if it exceeds 0.12%, these effects are saturated, and inclusions such as alumina tend to be generated. Therefore, the Al content is set to 0.01% or more and 0.12% or less.
N: 0.0010 to 0.0070%
If N is less than 0.0010%, the manufacturing cost of the steel sheet increases and stable manufacturing becomes difficult. In the present invention, the ratio of B and N is important as will be described later. However, if the amount of N is small, it becomes difficult to control the amount of B in order to keep the ratio of B and N within a certain range. On the other hand, if N exceeds 0.0070%, the hot ductility of steel deteriorates. This is because when N content exceeds 0.0070%, nitrides such as BN, Nb (N, C), AlN, and carbonitrides precipitate, resulting in embrittlement. Increased risk of cracking. When a slab crack occurs, a process of cutting a corner part and a grinding work with a grinder is necessary for the slab cracked part, and a lot of labor and cost are required, which greatly impedes productivity. Therefore, the N amount is set to be 0.0010% or more and 0.0070% or less. Preferably, it is 0.0044% or less.
B: 0.15 × N to 0.75 × N
B is an important element having a great influence on the properties of the steel sheet in the present invention.
Since the present invention is a method for manufacturing a steel plate for can making to reduce costs by omitting the recrystallization annealing step, (1) using ultra-low carbon steel for steel, and (2) adding a carbonitride-forming element. (3) Hot rolling is performed at a temperature of ₃ or less Ar. However, the steel plate manufactured under these conditions has a problem that the plate thickness uniformity in the longitudinal direction of the steel plate coil is inferior. Therefore, in the present invention, as a result of examining this phenomenon in detail, the inventors have come to the knowledge that the plate thickness uniformity in the longitudinal direction of the steel plate coil can be kept well by adding an appropriate amount of B to the steel. This is considered to be based on the following mechanism. First, the non-uniformity of the plate thickness in the longitudinal direction of the steel plate coil occurred at the stage of the hot rolled steel plate. This is because the deformation resistance changes discontinuously when transforming from austenite to ferrite at the Ar ₃ point in the ultra-low carbon steel to which the carbonitride-forming element is added. It is thought that fluctuations in tension between the stands and rolling load occur, resulting in fluctuations in sheet thickness. It is considered that the addition of B suppresses such discontinuous changes in deformation resistance and improves the thickness uniformity. That is, the important point in the present invention is to appropriately define the amount of B added and suppress discontinuous changes in deformation resistance. As a result of the study, it is necessary to add B in an appropriate relationship with the amount of N that forms BN. To obtain such an effect, addition of B of 0.15 × N or more in mass ratio is required. I found it necessary. On the other hand, addition of 0.75 × N or more of B in mass% causes the above effect to be saturated and causes an increase in cost. Therefore, the addition amount of B shall be 0.15 * N-0.75 * N (atomic ratio 0.20 * N-0.97 * N).
Nb: 4 × C to 20 × C (atomic ratio, 0.52 × C to 2.58 × C), Ti: 2 × C to 10 × C (atomic ratio, 0.50 × C to 2.51 1 type or 2 types Nb of xC) is a carbonitride forming element, and has an effect of reducing the strength of steel by fixing C and N in the steel as precipitates. In order to exhibit the effect sufficiently, an addition amount of 4 × C or more is necessary in terms of mass ratio. On the other hand, if the amount of Nb added is too large, the function of reducing the solute C is saturated, and Nb is expensive, so the production cost also increases. Therefore, it is necessary to suppress the Nb amount to 20 × C or less. Therefore, the amount of Nb is in the range of 4 × C to 20 × C in terms of mass ratio (0.52 × C to 2.58 × C in terms of atomic ratio).
Ti is a carbonitride-forming element and has an effect of reducing the strength of steel by fixing C and N in the steel as precipitates. In order to exhibit the effect sufficiently, an addition amount of 2 × C or more is necessary in terms of mass ratio. On the other hand, if the amount of Ti added is too large, the function of reducing the solute C is saturated, and the production cost is increased because Ti is expensive. Therefore, it is necessary to suppress the Ti amount to 10 × C or less. Therefore, the amount of Ti is in the range of 2 × C to 10 × C in terms of mass ratio (0.50 × C to 2.51 × C in terms of atomic ratio).

The remainder other than the above consists of Fe and inevitable impurities. As the unavoidable impurities, for example, the following elements may be contained within a range that does not impair the effects of the present invention.
Si: 0.020% or less When the Si content exceeds 0.020%, the surface properties of the steel sheet are deteriorated, which is not desirable as a surface-treated steel sheet, and the steel is hardened to make the hot rolling process difficult. . Accordingly, the Si content is preferably 0.020% or less.
P: 0.020% or less By reducing the P content, workability and corrosion resistance can be improved. However, excessive reduction leads to an increase in manufacturing cost. 0.020% or less is preferable.
In addition to the above components, unavoidable impurities such as Cr and Cu are included, but these components do not particularly affect the steel sheet characteristics of the present invention, so that they are appropriately included within a range that does not affect other characteristics. Can do. Moreover, elements other than those described above can be added within a range that does not adversely affect the properties of the steel sheet.

Next, the reasons for limiting the manufacturing conditions will be described.
The steel sheet for can manufacturing according to the present invention is a steel slab adjusted to the above chemical composition range, made into a slab by continuous casting, hot rolled at a finishing temperature not higher than the Ar ₃ transformation point, wound, pickled, It can be obtained by cold rolling at a reduction of ~ 96%. Preferably, the winding is performed at a winding temperature of 640 to 750 ° C. More preferably, after the cold rolling, heat treatment is performed at a temperature of 150 to 400 ° C. These will be described in detail below.
Hot rolling conditions Hot pressure finishing temperature: Ar ₃ transformation point or less The hot rolling finishing temperature is an important requirement in the present invention. By subjecting the steel of the component defined in the present invention to hot rolling at a finishing temperature not higher than the Ar ₃ transformation point, a steel plate material that can withstand canning can be obtained. This is because by hot rolling below the Ar ₃ transformation point, the grain size of the hot-rolled steel sheet becomes sufficiently coarse, work hardening in cold rolling is suppressed, and the strength after cold rolling does not become excessive. This is probably because of this.
The Ar ₃ transformation point can be determined as a temperature at which a volume change associated with the Ar ₃ transformation occurs when a thermomechanical test that reproduces the processing and thermal history during hot rolling is performed. The Ar ₃ transformation point of the steel component defined in the present invention is about 900 ° C. and the finishing temperature may be lower than this, but it is desirable to make it 860 ° C. or lower in order to achieve this reliably.

Further, although the detailed mechanism is unknown, the uniformity of the structure is excellent and the material stability is improved by setting the total rolling ratio below 40% and the final rolling ratio to 25% or more at the Ar ₃ transformation point or lower. . In order to further increase this, it is preferable that the total rolling reduction is 50% or more and the final rolling reduction is 30% or more.
In addition, in the present invention, the temperature at the entrance of the finishing mill is 950 ° C. or less, so that the hot rolling can be surely made the Ar ₃ transformation point or less and the structure can be made uniform. More preferred. Although the detailed mechanism has not been fully elucidated, it is presumed that the austenite grain size immediately before the start of finish rolling is related. From the viewpoint of preventing generation of scale flaws, it is more desirable to set the temperature to 920 ° C. or lower.
Winding temperature: 640 to 750 ° C. (preferred conditions)
The coiling temperature needs to be set so as not to hinder the pickling / cold rolling as the next step. That is, when the coil is wound at a temperature exceeding 750 ° C., the scale thickness of the steel sheet is remarkably increased, and the descalability during pickling is deteriorated. Problems such as deformation may occur. On the other hand, when the temperature is lower than 640 ° C., the heat retaining effect after winding is not sufficient, and the particle diameter of the hot-rolled steel sheet is not sufficiently coarsened.
The hot-rolled steel sheet after pickling is subjected to pickling for scale removal before cold rolling. Pickling may be performed according to a conventional method.
Cold rolling conditions after pickling: reduction rate of 50 to 96%
In cold rolling after pickling, the rolling reduction is 50 to 96%. If the rolling reduction is less than 50%, the crystal structure becomes non-uniform, so that when the can-making process is performed, the deformation becomes non-uniform and the surface of the product becomes rough. In addition, since this cold rolling also serves to adjust the shape and roughness of the steel sheet, it is an essential condition in these respects to perform reduction of approximately 50% or more. The upper limit depends on the required strength and thickness of the product and the hot / cold rolling equipment capacity, but rolling over 96% avoids deterioration of local ductility. Can not be applied except for very special purposes.
Heat treatment temperature after cold rolling: 150 to 400 ° C. (preferred conditions)
When heat treatment is performed after cold rolling, the heat treatment temperature is set to 150 to 400 ° C. In the components of the present invention, the recrystallization temperature is generally 730 ° C. or higher, so recrystallization does not occur at 150 to 400 ° C., but the above temperature is determined by the quantitative relationship of C, Nb, N, and B defined in the present invention. By performing the heat treatment in the range, the strength can be lowered and the ductility can be improved. Since this phenomenon is softened at a relatively low temperature, it is a phenomenon caused by the interaction between a solid solution element such as C and N, which is likely to diffuse at such a temperature, and a dislocation introduced by cold rolling. Conceivable. In other words, due to the quantitative relationship of C, Nb, Ti, N, and B defined in the present invention, the solid solution C and N in the ferrite phase is in an ideal state, so that the strength decreases at a relatively low temperature. It is thought that improvement of ductility can be obtained. In particular, the influence of the addition condition of B specified in the present invention is large, and B and N form BN to lower the solid solution N, and the solid solution B segregates at the grain boundary, so that C, N The segregation of the steel was prevented, the dislocations introduced by cold rolling in the matrix were released from the state where C and N were fixed, and the fixing was released by heat treatment, and these resulted in a decrease in strength and an improvement in ductility. It is considered a thing. The lower limit temperature at which such an improvement effect can be expected is 150 ° C. On the other hand, when the temperature is 400 ° C. or higher, recovery starts preferentially with some crystal grains with large strain energy accumulation in cold rolling, and the deformation becomes non-uniform when the can manufacturing process is performed. The surface of the skin becomes rough. From this, the heat processing temperature after cold rolling shall be 150-400 degreeC. In addition, in order to acquire intensity | strength and ductility stably, the range of 200-350 degreeC is preferable. The heat treatment time is not particularly limited as long as it is sufficient for the solid solution element to dissociate the dislocation from the element estimated in the present invention, but is preferably in the range of about 10 to 90 s.

Examples will be described below.
Various steels shown in Table 1 were melted to form slabs, heated at a heating temperature of 1100 to 1250 ° C., hot-rolled at the finishing temperature shown in Table 1, and wound up at a winding temperature of 680 ° C. Next, after pickling, cold rolling was performed at a rolling rate of 90%.
The plate thickness fluctuation | variation was evaluated with respect to the steel plate obtained by the above. Sheet thickness fluctuation is measured with the X-ray plate thickness meter installed in the cold rolling equipment for the total length of the steel sheet coil length, and evaluated by the rate of change relative to the average plate thickness. Those acceptable ± 3% or less are indicated as “good” as acceptable, and those exceeding ± 3% are indicated as “bad” as unacceptable.
Moreover, in Table 1, the finishing temperature of hot rolling was set to ○ when the temperature was lower than or equal to the Ar ₃ transformation point defined in the present invention, and x was set to exceed the Ar ₃ transformation point excluded in the present invention.
The results obtained as described above are shown in Table 1 together with the conditions.

  From Table 1, it can be seen that in the examples of the present invention, the plate thickness variation is ± 3% or less, and a steel plate in which the plate thickness variation in the longitudinal direction of the steel plate coil is suppressed is obtained. That is, it can be seen that suppression of plate pressure fluctuation, which is the first problem of the present invention, can be solved by satisfying the conditions defined in claim 1 as shown in Table 1.

Various steels shown in Table 2 were melted to form slabs, heated at a heating temperature of 1100 to 1250 ° C., then hot-rolled at 820 ° C., which is below the Ar ₃ transformation point, and wound up as shown in Table 2. Winded up at temperature. Next, pickling was performed, and cold rolling was performed at a rolling rate shown in Table 2.
The plate thickness fluctuation | variation was evaluated with respect to the steel plate obtained by the above. The plate thickness variation was evaluated by measuring the plate thickness after cold rolling with respect to the average plate thickness by measuring the full length of the steel plate coil with an X-ray plate thickness meter installed in the cold rolling facility. The evaluation results are shown in Table 2. Fluctuations are indicated by ○ when the product is acceptable within ± 3% or less, and marked by × when the product exceeds ± 3%.
Next, the steel plate was heat-treated at a heat treatment temperature shown in Table 2 for 30 s. Thereafter, two types of surface treatments were performed. One was tin-free steel (hereinafter referred to as TFS) with Cr plating on the surface, and a PET resin film was laminated. The other was tinplate with Sn plating on the surface.
The TFS laminated with a PET resin film was processed into a DRD can with a drawing ratio of 2.2, and the skin roughness was evaluated by visual judgment at the can body and bottom. The evaluation was made by comparing with a limit sample of excellent, good and impossible. Here, “excellent” indicates that the rough skin does not occur, “good” indicates that the rough skin is slightly generated but is in a practically acceptable range, and “unsatisfactory” indicates that the rough skin occurs at a level that is practically unacceptable. In the evaluation results, “Excellent” means “Good”, “Good” means “No”, and “No” means “No”. The obtained results are shown in Table 2.
In addition, the cover was a 52 mm diameter welded can, and flanges with expansion rates of 6% and 8% were subjected to evaluation of the occurrence of flange cracks. The evaluation results are as follows: 6% and 8% flange processing with no cracking, 8% flange processing with cracking, 6% with no cracking △, 6% and 8% In any case, the case where cracking occurred in the flange processing was marked with x. The obtained results are shown in Table 2.

From Table 2, suppression of plate pressure fluctuation, which is the first problem of the present invention, can be solved by satisfying the conditions defined in claim 1. In actual can molding, rough skin and flange cracking are at acceptable levels.
Furthermore, it can be seen that, by satisfying the conditions defined in claims 2 and 3, the suppression of rough skin and flange cracking in actual can molding is further improved.

  The present invention is most suitable as a food can or a beverage can. And besides these, using organic resin film laminated steel plate as envisioned in the present invention as a raw material, using conventional DI molding, avoiding damage to the film, for applications where can body pullability is required Are also preferably used.

Claims (3)

Steel component is mass%, C: 0.005% or less, Mn: 0.05 to 0.5%, Al: 0.01 to 0.12%, N: 0.0010 to 0.0070%, B : 0.15 × N to 0.75 × N (atomic ratio, 0.20 × N to 0.97 × N), and Nb: 4 × C to 20 × C (atomic ratio, 0. 52 × C to 2.58 × C), Ti: 2 × C to 10 × C (in atomic ratio, 0.50 × C to 2.51 × C), including one or two, with the balance being Fe and Steel consisting of inevitable impurity elements is made into a slab by continuous casting, hot rolled at a finishing temperature below the Ar ₃ transformation point, wound, pickled, and then cold rolled at a reduction rate of 50 to 96%. A method for producing a steel plate for can making, characterized in that.   The said winding is performed at the temperature of 640-750 degreeC, The manufacturing method of the steel plate for cans of Claim 1 characterized by the above-mentioned.   The method for producing a steel plate for can manufacturing according to claim 1 or 2, wherein heat treatment is performed at a temperature of 150 to 400 ° C after the cold rolling.