JP5099126B2 - Soft tin steel sheet and manufacturing method thereof - Google Patents

Description

The present invention relates to a soft tin steel sheet manufactured using a continuous annealing method and a method for manufacturing the same.
This application is based on Japanese Patent Application No. 2007-109332 and incorporates the contents thereof.

  The soft tin steel sheets from T-1 to T-3 specified in JIS G 3303, which are used for beverage or food cans, have been conventionally manufactured by long-term annealing using batch annealing (BAF). It was. It is necessary to obtain a so-called non-aging material that grows crystal grains greatly, softens the material, and sufficiently precipitates C and N dissolved in the steel to prevent hardening due to aging and stretcher strain. Because there was. On the other hand, with the intensification of cost reduction requirements, the BAF manufacturing method with many processes and long construction period is gradually shunned so that a continuous annealing method that can obtain a large amount of steel of uniform material in a short time is used. It has become. The continuous annealing method is a method in which the steel strip with the coil unwound is continuously passed through the furnace and heated, but the annealing time is short and it is difficult to obtain a non-aging material. For this reason, conventionally, the continuous annealing method has been mostly applied to steel plates for hard tin sheets of T-4 or higher. However, in recent years, advancement of steel pretreatment technology has made it possible to easily produce ultra-low carbon steel (Interstitial atom Free steel, hereinafter abbreviated as IF steel) in which the content of C and N in the steel is reduced in advance. Therefore, the continuous annealing method has come to be used for steel plates for soft tin such as T-1 to T-3.

  However, IF steel is a very soft material because it has few solid solution elements, and although it can be manufactured relatively easily up to T-2 soft tin plate, it is a tin plate with a slightly hard material of about T-3. Therefore, it is necessary to add a large amount of hardening elements (hardening elements) such as Mn, P, Si, etc., or to increase the secondary cold rolling rate (temper rolling ratio) for work hardening. It was.

Among means for solving such problems of IF steel, as a method of adding a hardening element, for example, in Patent Document 1, B is added to an extremely low carbon steel, and the amount of Mn that is a hardening element is added. A technique for adjusting the hardness is disclosed. Moreover, as a method of work hardening, for example, Patent Document 2 discloses a technique for work hardening of an ultra-low carbon steel added with B at a temper rolling ratio of more than 4.0% and not more than 6.0%. Yes.
JP-A-9-227947 Japanese Patent Laid-Open No. 2001-247917

  However, in the technique described in Patent Document 1, the hardness is adjusted by the addition amount of Mn. However, in the ASTM standard which is a standard for general steel plates for cans, the addition amount of Mn from the viewpoint of corrosion resistance. Has an upper limit of 0.6%. Therefore, even if 0.6% Mn is added, there is a problem that it is not possible to obtain a tin steel plate of a material slightly hard (hardness is 52 to 60 for HR30T) of about T-3. HR30T is a definition of Rockwell hardness generally used for tin steel sheets, and the measuring method is as defined in JIS Z 2245.

  Moreover, in the technique (work hardening method) described in Patent Document 2, the temper rolling ratio is set to more than 4.0% and not more than 6.0%. There is no practical method other than using a manufacturing method (a manufacturing method called “DCR (Double Cold Rolling)” or “HRT (Heavy Reduction Temper)”) that repeats a plurality of times or using a rolling fluid. Of course, the method of repeating temper rolling a plurality of times is not preferable in terms of cost. Also, in the method of rolling down using a rolling fluid, since the IF steel material is soft, it may be excessively stretched or it may be difficult to control rolling conditions. There was a problem that it was impossible to secure the shape and shape.

  In the present specification, the term “rolling fluid” refers to a beef tallow-based emulsion (for example, “Quakeroll” manufactured by Nippon Quaker Chemical Co., Ltd.) or a synthetic ester-based aqueous solution (for example, manufactured by Nippon Quaker Chemical Co., Ltd.). The term “tinol”) is generally used to refer to lubricants generally used in temper rolling of tin steel sheets.

  Moreover, it is common for IF steel used as a base material of a soft tin steel plate to add Ti and Nb in order to precipitate C and N which are dissolved in steel. Since the recrystallization temperature of steel rises due to the fine precipitation of Ti and Nb, a high annealing temperature of 700 ° C. or higher is required. For this reason, in a tin steel plate with a thin plate thickness, wrinkles of a plate called a heat buckle are often generated in a continuous annealing plate in a furnace, and the product yield is often lowered.

  Thus, the manufacturing conditions that can stably supply a tin steel sheet with a hardness of HR30T and a hardness of 52-60 within a range that can be easily and industrially realized for continuous annealing by applying IF steel to tinplate that is rapidly progressing. Has not been proposed so far.

  This invention is made | formed in view of the said situation, The objective is using the continuous annealing method using IF steel, and providing the comparatively hard soft tin steel sheet whose hardness is 52-60 by HR30T. And providing a manufacturing method for easily obtaining the soft tin steel sheet.

  As a result of intensive studies to solve the above problems, the present inventors can improve the strength of IF steel as a base material by adjusting the composition ratio of elements in the soft tin steel sheet, It has been found that the production of a soft tin steel sheet having a hardness of 52-60 with HR30T using a continuous annealing method can be realized, and the present invention has been completed based on this finding.

That is, the gist of the present invention is as follows.
(1) C is contained in an amount of 0.0020 mass% or less, B and N are contained so as to satisfy at least one of B / N ≧ 1.5 and solid solution B in a mass ratio of 5 ppm or more, with the balance being Fe and inevitable. A soft tin steel sheet having a steel composition of mechanical impurities; the hardness is 52-60 in HR30T.
(2) C is contained in an amount of 0.0020% by mass or less, B and N are contained so as to satisfy at least one of B / N ≧ 1.5 and solid solution B in a mass ratio of 5 ppm or more, with the balance being Fe and inevitable. Obtained by subjecting a slab having a steel composition consisting of mechanical impurities to hot rolling, cold rolling, annealing, and then secondary cold rolling at a rolling reduction of 1.3% to 3.5%, Soft tin steel sheet.
(3) The soft tin steel sheet according to (2), wherein the hardness is 52-60 in HR30T.
(4) The soft tin steel sheet according to any one of (1) to (3), wherein the addition amount of B is 0.020% by mass or less.
(5) As steel composition, Si: 0.05 mass% or less, Mn: 0.20 mass% to 0.60 mass%, P: 0.020 mass% or less, S: 0.020 mass% or less, Al: One or two selected from the group consisting of 0.010 mass% to 0.10 mass%, Cr: 0.10 mass% or less, Ti: 0.01 mass% or less, Nb: 0.01 mass% or less The soft tin steel sheet according to any one of (1) to (3), further including the above elements.

(6) C is contained in an amount of 0.0020 mass% or less, B and N are contained so as to satisfy at least one of B / N ≧ 1.5 and solid solution B in a mass ratio of 5 ppm or more, with the balance being Fe and inevitable. Of a soft tin steel sheet that is hot-rolled, cold-rolled and annealed to a slab having a steel composition consisting of mechanical impurities, followed by secondary cold rolling at a rolling reduction of 1.3% to 3.5% Method.
(7) As steel composition, Si: 0.05 mass% or less, Mn: 0.20 mass% to 0.60 mass%, P: 0.020 mass% or less, S: 0.020 mass% or less, Al: One or two selected from the group consisting of 0.010 mass% to 0.10 mass%, Cr: 0.10 mass% or less, Ti: 0.01 mass% or less, Nb: 0.01 mass% or less The method for producing a soft tin steel sheet according to (6), further including the above elements.
(8) The method for producing a soft tin steel sheet according to (6) or (7), wherein the annealing is performed at a temperature of 650 ° C. to 700 ° C. using a continuous annealing facility having a temperature increase rate of less than 300 ° C./second.

  According to the soft tin steel sheet and the manufacturing method thereof according to the present invention, a relatively hard soft tin plate having a non-aging hardness of 52-60 in HR30T, which could not be obtained by a continuous annealing method using conventional IF steel. A steel plate can be obtained easily. Therefore, according to the present invention, since a soft tin steel sheet of about T-3 can be manufactured using a continuous annealing method, the yield is improved and cost reduction is achieved even when a relatively hard tin steel sheet is obtained. be able to.

  Hereinafter, preferred embodiments of the present invention will be described in detail.

<Configuration of soft tin steel sheet according to the present invention>
The soft tin steel sheet of the present invention uses a slab having a predetermined steel composition, and after performing hot rolling, cold rolling and annealing on the slab, secondary cold rolling (temper rolling) at a predetermined reduction rate This is a tin steel sheet having a hardness of 52-60 in HR30T (ie, about T-3).

(About steel composition)
Hereinafter, the steel composition of the slab used as a base material of the soft tin steel sheet of the present invention will be described. The slab is mainly composed of carbon (C), boron (B), nitrogen (N), silicon (Si), manganese (Mn), phosphorus (P), sulfur (S), aluminum (as a component in steel). Al) and the like, and the balance is made of Fe and inevitable impurities, and among these components, three elements C, B, and N are essential components. The contents of these components in the slab are as follows.

[About C]
Content of C in the slab used as a base material of the soft tin steel plate concerning this invention needs to be 0.0020 mass% or less.

  The reason is that, generally, the greater the amount of C dissolved in the steel, the higher the yield elongation (YP-EL), and this tends to cause age hardening and stretcher strain during processing. This is because, in the present invention for obtaining a soft tin steel sheet by using it, it is necessary to control so as to keep the C content as low as possible in the steelmaking stage. Specifically, the C content is set to 0.0020% by mass or less for the following reason. That is, for example, in a general can manufacturing process, if YP-EL is 2% or less, stretcher strain does not develop. However, when used for can top plate applications, YP-EL is 1. If the amount is not less than 4%, the steel sheet after pressing may be warped due to a change in hardness due to aging. This is because the probability of being 4% or more becomes very high. Further, considering the mixing of C from a refractory during casting, the amount of solute C in the steel in the steelmaking stage is preferably 0.0010% by mass or less.

[About B and N]
Moreover, B and N in the slab used as the base material of the soft tin steel plate according to the present invention must be contained so that B / N is 1.5 or more by mass ratio.

  B and N are elements having the most important role in the present invention. B not only prevents age hardening by combining with solid solution N in the steel and precipitates as BN, but according to the study by the present inventors, it exceeds the amount necessary for BN to precipitate. It is recognized that the B added excessively has the effect of making the crystal grains in the slab, which is the base material, fine. This is presumably because B added excessively exists as a solid solution B at the crystal grain boundary and suppresses the growth of crystal grains. As a result, the hardness of the base material increases, and a soft tin steel sheet having a hardness of about T-3 (52 to 60 for HR30T) can be obtained. Here, the solid solution B is B which does not precipitate as a compound with other elements but exists in a solid solution state in the steel, and its amount is precipitated as BN from the total amount of added B. It is obtained by subtracting the amount of B (solid solution B = BTotal−BasBN). The total amount of B and the amount of BN can be measured by a general chemical dissolution method or the like. Moreover, it can calculate | require simply by the numerical formula of solid solution B (mass%) = B (content, mass%)-10.8 / 14.0 * N (content, mass%).

  In order to exhibit the effect of increasing the hardness of the base material due to such refinement of crystal grains, it is necessary to deposit a large amount of B as a solid solution B after depositing BN. From the results of the various tests conducted by No. 1, the knowledge that B / N ≧ 1.5 by mass ratio and / or at least 5 ppm or more of B as solute B must be present. In Patent Document 1 described above, a method of adding B up to 24 ppm (B / N <0.8) is proposed in order to increase the hardness of the base material. However, even if N can be fixed as BN with this amount of B, since no solid solution B exists, the effect of increasing the hardness of the base material due to the refinement of crystal grains cannot be obtained. Thus, the amount of solute B effective for crystal grain refinement is preferably 40 ppm or more, then preferably 50 ppm or more, more preferably 60 ppm or more, more preferably 70 ppm or more, and most preferably 80 ppm or more. It is necessary to.

  In addition, as a result of fixing N by B, the grain boundary becomes brittle due to precipitated BN, so there is a concern of metallurgical flaws due to cracking during slab casting, or there is a concern that casting itself becomes impossible due to slab tearing in the casting machine Therefore, the addition amount of B is preferably 100 ppm (0.010% by mass) or less. As a result, the lower limit of B / N is preferably 1.5 or higher, then preferably 1.6 or higher, more preferably 1.7 or higher, most preferably 1.8 or higher, while the upper limit is preferably It is 4.0 or less, more preferably 3.0 or less, and most preferably 2.0 or less. If B / N is less than 1.5, an effective amount of solid solution B does not exist at the grain boundaries, and the effect of miniaturization cannot be obtained. On the other hand, if B / N exceeds 4.0, the above-mentioned problems such as inability to cast and excessive hardness occur.

[About Si]
Moreover, it is preferable that content of Si in the slab used as the base material of the soft tin steel plate concerning this invention is 0.05 mass% or less. This is because generally the corrosion resistance of the base material is reduced when a large amount of Si is contained. In the present invention, it is preferable that the upper limit of the content of Si contained in the base material is 0.05% by mass. In particular, when used in cans filled with contents that require corrosion resistance, the Si content is more preferably 0.03% by mass or less.

[About Mn]
Moreover, it is preferable that content of Mn in the slab used as the base material of the soft tin steel plate concerning this invention is 0.20 mass% or more and 0.60 mass% or less. Mn needs to be added in an amount of at least 0.20% by mass or more, more preferably 0.40% by mass or more in order to promote hardening of the steel to be added. On the other hand, when Mn is added in a large amount, the corrosion resistance of the base material is lowered. Therefore, it is preferable to set the upper limit of the Mn content to 0.6% by mass as defined by ASTM.

[About P]
Moreover, it is preferable that content of P in the slab used as the base material of the soft tin steel plate concerning this invention is 0.020 mass% or less. P significantly hardens the steel to be added while lowering the corrosion resistance. Therefore, in the present invention, the content of P is set to 0.020 mass in the same manner as in a general method for manufacturing a tin steel plate. % Or less is preferable. In particular, when used for applications requiring corrosion resistance, the P content is more preferably 0.015% by mass or less.

[About S]
Moreover, it is preferable that content of S in the slab used as the base material of the soft tin steel plate concerning this invention is 0.020 mass% or less. This is because S causes the steel to become brittle as inclusions and lowers the corrosion resistance. In the present invention, the S content is 0.020% by mass or less, as in the general method of manufacturing a tin steel sheet. It is preferable to make it.

[About Al]
Moreover, it is preferable that content of Al in the slab used as the base material of the soft tin steel plate concerning this invention is 0.010 mass% or more and 0.10 mass% or less. Al is added as a deoxidizing material in the steel making stage, and in order to obtain deoxidation hardening, the Al content is preferably 0.010% by mass or more. On the other hand, Al, like solute C, has a hardening that precipitates solute N that causes age hardening, but if added in a large amount, there is a concern that an alumina-based metallurgical iron may be generated. Is preferably 0.10% by mass or less.

[About Cr]
Moreover, it is preferable that content of Cr in the slab used as the base material of the soft tin steel plate concerning this invention is 0.10 mass% or less. Cr does not significantly affect the mechanical properties of the material. However, when Cr is used as the surface treatment for tinplate steel, a large amount of Cr in the steel becomes a disturbance factor for the on-line Cr adhesion meter and is strictly controlled. The content of Cr is preferably set to 0.10% by mass or less because the quality of surface treatments that require a reduction in quality and the upper limit of Cr is defined as 0.10% by mass according to the ASTM standard. .

[Ti and Nb]
Moreover, it is preferable that content of Ti and Nb in the slab used as the base material of the soft tin steel plate concerning this invention is 0.01 mass% or less, respectively. As described above, the IF steel used as the base material for the soft tin steel sheet is recrystallized due to fine precipitation of Ti and Nb added to precipitate C and N dissolved in the steel. The temperature rises above 700 ° C. In the present invention, solute C is made 0.0020 mass% or less at the molten steel stage by vacuum degassing or the like, and solute N is precipitated as BN by adding B to make it harmless. No addition is necessary. Therefore, in order to keep the annealing temperature low and improve the industrial productivity, it is preferable to set the contents of Ti and Nb to 0.01% by mass or less, respectively.

[Other chemical components]
As a component of the soft tin steel sheet of the present invention, Cu: 0.1% or less, preferably 0.01% or less, Ni: 0.1% or less, preferably 0.01% or less, Mo: 0.05% or less, preferably 0.005% or less, Zr: 0.05% or less, preferably 0.005% or less, V: 0.1% or less, preferably 0.01% or less, Ca or Mg You may contain 1 type (s) or 2 or more types among each component element of 0.003% or less, Preferably 0.0005% or less.

<Method for producing soft tin steel sheet according to the present invention>
The configuration of the soft tin steel sheet according to the present invention has been described above. Next, the method for producing the soft tin steel sheet according to the present invention having such a configuration will be described in detail.

  In the method for producing a soft tin steel sheet according to the present invention, hot rolling, pickling, cold rolling, and annealing are sequentially performed on a slab having the steel composition as described above, and then a rolling reduction of 1.3% or more and 3. By performing secondary cold rolling (temper rolling) at 5% or less, a relatively hard soft tin steel sheet is produced.

(Hot rolling / Pickling / Cold rolling)
Among the above production steps, general steel production conditions may be used for hot rolling, pickling, and cold rolling. For example, after heating the slab to 1000 ° C. to 1300 ° C., using a hot strip facility such as a hot strip mill, the finishing temperature is set to 800 ° C. to 1000 ° C., and rolling to a thickness of 1.8 mm to 4.0 mm is performed. A hot-rolled steel sheet is produced at 400 ° C to 800 ° C. Thereafter, pickling using hydrochloric acid or the like and rolling to a thickness of 0.1 mm to 0.6 mm at room temperature using cold rolling equipment such as a cold strip mill.

(Annealing)
Annealing is performed for the purpose of adjusting the material so that the steel structure work-hardened by cold rolling can be softened by recrystallization and can be processed into a can. As described above, the IF steel used as a base material for the soft tin steel sheet of the present invention is obtained by fine precipitation of Ti and Nb added to precipitate C and N dissolved in the steel. In many cases, an annealing temperature of 700 ° C. or higher is required. However, since Ti and Nb are not included as components of the soft tin steel sheet of the present invention and the recrystallization temperature does not increase, an annealing temperature of 650 to 700 ° C. is sufficient. On the other hand, when the annealing temperature is less than 650 ° C., the steel does not recrystallize, which is not preferable, and when the annealing temperature exceeds 700 ° C., there is a problem that heat buckles are likely to occur, which is not preferable. In addition, since the supply of heat is relatively small as described above, it is effective as a secondary effect for heat source countermeasures. Note that the rate of temperature increase during annealing of the IF steel of the present invention may be the same as that of a general process used in normal industrial production, and the value is preferably less than 300 ° C./second, more preferably 200 ° C./second. Less than, most preferably less than 100 ° C./second. Similarly, the soaking time may be a normal annealing condition of about 20 seconds to 100 seconds.

(Secondary cold rolling)
In the secondary cold rolling (temper rolling) process of the present invention, when a rolling fluid is used (so-called WET pressure regulation called “DCR” or “HRT”), stable steel sheet production cannot be performed as described above. Therefore, in this invention, what is called DRY pressure regulation which does not use a rolling fluid is given. In addition, although the present inventors performed the technical examination at the time of performing the secondary cold rolling using a rolling liquid with respect to IF steel after continuous annealing, it reached actual machine verification, but the steel plate as mentioned above It is difficult to industrially apply because there is a risk that not only the thickness of the steel will be excessively stretched, but also the thickness control and the shape of the steel sheet will be defective, and the rolling load of automatic control will be extremely reduced and rolling will become impossible. It was confirmed that

  The secondary cold rolling in the present invention needs to be performed at a rolling reduction (temper rolling ratio) of 1.3% or more and 3.5% or less. The reason why the rolling reduction of 1.3% or more is required is necessary for the purpose of reducing the YP-EL, the shape correction, and the transfer of the surface roughness of the rolling roll, which are the original purposes of secondary cold rolling. This is because a hardness of 52 or more cannot be obtained with HR30T at a rolling reduction below this. Furthermore, in order to ensure sufficient hardness, it is preferable to work harden at the highest reduction rate. However, when DRY pressure adjustment is performed with a two-stand rolling mill that is generally used as a pressure-regulating rolling mill for tinplate, about 3.5% of the equipment capacity is rolled due to the relationship between mill rigidity and rolling load. Therefore, the rolling reduction during the secondary cold rolling in the present invention is set to 1.3% or more and 3.5% or less.

  By subjecting a slab having the steel composition as described above to hot rolling, pickling, cold rolling and annealing in sequence, then secondary cold rolling (temper rolling) under the conditions as described above. A relatively hard and soft tin steel plate that is non-aging and has a hardness of 52 to 60 in HR30T (that is, about T-3) that could not be obtained by a continuous annealing method using conventional IF steel. Can be manufactured.

  Next, the present invention will be described more specifically with reference to examples. However, the present invention is not limited to the following examples.

(Manufacture of soft tin steel sheet)
First, the manufacture example of the soft tin steel plate manufactured using the manufacturing method of this invention is demonstrated.
After casting steel A to D series slabs having the compositions shown in Tables 1 and 2 below and heating these slabs at 1235 ° C., using a hot strip mill, a finishing temperature of 900 ° C. and a winding temperature of 650 ° C. Under the condition of ° C., hot rolling was performed until the finished plate thickness after rolling was 3.0 mm. Next, the steel strip after hot rolling is pickled and cold rolled until the finished plate thickness after rolling is 0.25 mm, and then two temperature conditions of 680 ° C. and 640 ° C. in a continuous annealing furnace. Annealing was performed. Further, secondary cold rolling was performed on the annealed steel sheet under two conditions of temper rolling ratio of 3% and 5%. In addition, when the temper rolling rate was 3%, DRY pressure control without using a rolling fluid was performed, and under the condition of a temper rolling rate of 5%, WET pressure control using a rolling fluid was performed. As the rolling fluid in the case of WET pressure regulation, a solution obtained by diluting tinol made by Nippon Quaker Chemical Co. to 0.2% with pure water was used.

Among the above-mentioned secondary cold rolling conditions, the sample subjected to the secondary cold rolling at a temper rolling rate of 5% using the rolling liquid became impossible to control the rolling immediately after the start of rolling. Canceled. This phenomenon can be explained as follows. In the case of ordinary steel, the load and tension of the rolling stand are automatically controlled so as to balance the hardness of the steel, and the set temper rolling ratio can be stably maintained. However, since IF steel is soft, even if the initial setting of the stand load and tension is lower than usual, the steel is rolled strongly exceeding the set temper rolling ratio. In this case, although the load and tension are continuously reduced by automatic control, the rolling rate continues to increase without finding a balance point due to the softness of IF steel. If the automatic control range is exceeded, the rolling rate, thickness, and shape cannot be controlled. The present inventors paid attention also to the lubrication conditions, and carried out the temper rolling using only pure water having a high friction coefficient as a rolling fluid, but the results did not change. About the sample other than that, the tin plating process was performed with the adhesion amount of 1000 mg / m < ² > after secondary cold rolling.

  The steel compositions shown in Tables 1 and 2 are the solid-state emission spectroscopy (QV) method, which is a commonly performed analysis, the infrared absorption method specified in JIS G 1211 and 1215, and the steel composition specified in JIS G 1227. Measured by methylene blue absorptiometry.

(Measurement of hardness and yield elongation)
About the tin steel plate manufactured as mentioned above, hardness (HR30T) was measured by the method prescribed | regulated to JISZ2245, and yield elongation (YP-EL) was measured by the method prescribed | regulated to JISZ2241. Note that both the hardness and the yield elongation were measured after a heat treatment at 210 ° C. for 30 minutes provided by ordinary paint baking.

  The results of measuring the hardness (HR30T) and the yield elongation (YP-EL) of the tin steel sheet as described above are shown in Tables 1 and 2 together.

  From these Tables 1 and 2, the following can be understood. That is, B and N that belong to the scope of the present invention are B / N ≧ 1.5 by mass ratio and / or a steel in which solute B is 5 ppm or more, HR30T has a sufficient hardness of 52-60, And YP-EL was also almost 0.0, and there was no problem. On the other hand, No. with B / N of less than 1.5 and solid solution B of less than 5 ppm. As for B12, HR30T was 50, and the hardness of the tin plate was insufficient. In addition, No. 2 in which the rolling reduction of secondary cold rolling is less than 1.3%. As for B6, B8, and B9, HR30T was 51 and the hardness of the tin plate was insufficient. Further, B1 having a C content exceeding 0.0020 mass% had a high YP-EL of 1.8, and age hardening occurred.

  As mentioned above, although preferred embodiment of this invention was described, it cannot be overemphasized that this invention is not limited only to this example. It will be apparent to those skilled in the art that various changes and modifications can be made within the scope of the claims, and these are naturally within the technical scope of the present invention. Understood.

  According to the present invention, since a soft tin steel sheet of about T-3 can be manufactured using a continuous annealing method, the yield can be improved and cost reduction can be achieved even when a relatively hard tin steel sheet is obtained. it can.

Claims (8)

0.0020 mass% or less of C,
Further, B and N are included so as to satisfy at least one of B / N ≧ 1.5 by mass ratio and solid solution B of 5 ppm or more,
The remainder has a steel composition consisting of Fe and inevitable impurities;
The hardness is 52-60 in HR30T;
A soft tin steel sheet characterized by that. 0.0020 mass% or less of C,
Further, B and N are included so as to satisfy at least one of B / N ≧ 1.5 by mass ratio and solid solution B of 5 ppm or more,
In the slab having the steel composition consisting of Fe and inevitable impurities as the balance,
A soft tin steel sheet obtained by subjecting to hot rolling, cold rolling and annealing, and then secondary cold rolling at a rolling reduction of 1.3% to 3.5%.   The soft tin steel sheet according to claim 2, wherein the hardness is 52-60 in HR30T.   The soft tin steel sheet according to any one of claims 1 to 3, wherein the addition amount of B is 0.020 mass% or less. As steel composition, Si: 0.05 mass% or less, Mn: 0.20 mass% to 0.60 mass%, P: 0.020 mass% or less, S: 0.020 mass% or less, Al: 0.010 One or more elements selected from the group consisting of mass% to 0.10 mass%, Cr: 0.10 mass% or less, Ti: 0.01 mass% or less, Nb: 0.01 mass% or less The soft tin steel sheet according to any one of claims 1 to 3, further comprising: 0.0020 mass% or less of C,
Further, B and N are included so as to satisfy at least one of B / N ≧ 1.5 by mass ratio and solid solution B of 5 ppm or more,
In the slab having the steel composition consisting of Fe and inevitable impurities as the balance,
After hot rolling, cold rolling and annealing,
A method for producing a soft tin steel sheet, comprising performing secondary cold rolling at a rolling reduction of 1.3% or more and 3.5% or less. As steel composition, Si: 0.05 mass% or less, Mn: 0.20 mass% to 0.60 mass%, P: 0.020 mass% or less, S: 0.020 mass% or less, Al: 0.010 One or more elements selected from the group consisting of mass% to 0.10 mass%, Cr: 0.10 mass% or less, Ti: 0.01 mass% or less, Nb: 0.01 mass% or less The method for producing a soft tin steel sheet according to claim 6, further comprising: The said annealing is performed at the temperature of 650 degreeC-700 degreeC using the continuous annealing equipment with a temperature increase rate of less than 300 degrees C / sec, The manufacturing method of the soft tin steel plate of Claim 6 or 7 characterized by the above-mentioned.