JP2005307350A - Steel sheet for flexible can, and its production method - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a steel sheet for a flexible can which has excellent weldability, non-aging property, and workability and is less reduced in can height and its production method. <P>SOLUTION: The steel sheet has steel components containing, by mass %, 0.0015 to 0.005% C, 0.1 to 0.8% Mn, 0.01 to 0.10 Al, 0.015 to 0.0070% N, 4xC to 20xC (0.52xC to 2.58xC by atomic ratio) Nb, 0.15xN to 0.75xN (0.20xN to 0.97xN by atomic ratio) B and the balance Fe and inevitable impurities, and is manufactured by a continuous annealing method, wherein an average Lankford value r<SB>ave</SB>ranges from 1.3 to 1.8, and satisfies at least one among three relational expressions consisting of of r0<r45-0.2, r90<r45-0.2, ¾r0-r90¾>0.3 and the temper degree ranges from T2 to T3.5. <P>COPYRIGHT: (C)2006,JPO&NCIPI

Description

  The present invention relates to a soft steel plate for cans produced by a continuous annealing method, and has a tempering degree T2 to T3.5 having non-aging properties, workability, and weldability substantially the same as those produced by a batch annealing method. Relates to a steel sheet for soft cans.

  Of the steel plates for cans such as tinplate and tin-free steel (TFS), most hard materials with tempering grades T4 to T6 are manufactured by continuous annealing, but soft materials are mainly manufactured by batch annealing. . Batch annealing is inferior in productivity because of a longer processing time than continuous annealing, and is also disadvantageous in terms of steel plate shape and uniformity of mechanical properties. Therefore, the manufacturing method of the soft material by the continuous annealing method is examined.

  For example, Patent Document 1 proposes a method of annealing a low carbon steel with a continuous annealing line provided with an overaging treatment zone. In continuous annealing, solid solution C is supersaturated by rapid cooling after soaking, and when passing through the overaging treatment zone after rapid cooling, a method of softening and non-aging by precipitating most of the solid solution C is a method. Proposed. However, in this method, C cannot be completely precipitated, and a slight amount of solute C remains, so that it cannot be said that the non-aging property is sufficient.

  When there is no heating process before the can manufacturing process, aging is at a level that does not cause a problem, but when a heating process such as paint baking is performed before the can manufacturing process, aging is promoted, Defects such as stretcher strain (pulling wrinkles due to Luders elongation) and fluting (wrinkle wrinkles due to buckling) may occur.

  Patent Document 2 proposes a method of adding Nb to an extremely low carbon steel. In this method, since the total amount of C in the steel is precipitated as NbC by Nb having a strong affinity for C, solid solution C does not remain and complete non-aging is achieved. However, when used in welding applications, cracks may occur in the heat affected zone (HAZ) depending on the processing conditions after welding. This is considered to be because the hardenability is inferior due to the extremely low carbon steel, and the strength of the HAZ part is insufficient. In addition, the Nb-added ultra-low carbon steel has a drawback that the reduction in can height is large when can barrel processing such as expansion processing or bead processing is performed after welding because the Rankford value is too high. It was. Thus, the Nb-added ultra-low carbon steel has problems such as cracking of the HAZ part and reduction in can height when used mainly for welding applications.

  Patent Document 3 proposes a method of adding B to ultra-low carbon steel. This method is characterized by excellent weldability due to the presence of B even though it is an extremely low carbon steel. However, in this conventional method, solid solution N can be precipitated as BN, but solid solution C cannot be fixed. Therefore, the non-aging property is not sufficient, and when a heating process such as paint baking is performed in a can manufacturer, the aging is promoted, and in the can manufacturing process after the heating process, there are molding defects such as stretcher strain and fluting. It sometimes occurred.

  Patent Document 4 proposes a method of adding one or more of Nb, Ti, and B to ultra-low carbon steel. This method is characterized by excellent non-aging due to the effects of Nb and B. However, in this conventional method, it is necessary to limit C to 0.0015% or less. With the current technology, it is difficult to stably manufacture a steel plate having C of 0.0015% or less at low cost.

  Patent Document 5 proposes a method of adding both Nb and B to an extremely low carbon steel. It is described that this method satisfies various required characteristics required for steel plates for cans, such as weldability, workability, optimum crystal grain size, and corrosion resistance. However, Nb: 0.001 to 0.1%, B: 0.0001 to 0.005%, and the component range is very wide, so it could not be said that an optimum range was found for each required characteristic.

  In Patent Document 6, in the component composition of carbon steel containing N, Nb, Ti, the component composition is specified, and N, Nb, Ti is satisfied with a specific relational expression, or In addition, there has been proposed a continuous cast slab that is free from intergranular cracking defects and is characterized in that the relationship between Nb and N is adjusted to satisfy other specific formulas. However, this slab contains Ti: 0.004 to 0.1%, and Ti concentrates on the surface of the steel sheet, and there is a problem that the plating property (surface appearance and quality) is deteriorated. Is difficult to use.

As described above, in the conventional technique, a steel sheet for a soft can which is excellent in weldability and non-aging property and has a small reduction in can height in can body processing after welding has not been obtained by the continuous annealing method. For this reason, some can manufacturers and some can types use steel sheets for soft cans manufactured by the continuous annealing method, but most can manufacturers and most can types use the batch annealing method. The manufactured steel plate was used.
Japanese Examined Patent Publication No. 63-10213 Japanese Patent Publication No. 1-52450 Japanese Patent No. 3377155 (Japanese Patent Laid-Open No. 9-227947) Japanese Patent No. 2035952 (Japanese Patent Laid-Open No. 5-263143) JP-A-6-41683 Japanese Patent Laid-Open No. 2003-166038

  As described above, in the conventional technology, the same characteristics as those obtained by the batch annealing method are not obtained in the steel sheet for soft cans by the continuous annealing method. Therefore, until now, most steel sheets for soft cans have been manufactured by a batch annealing method. An object of this invention is to solve said problem with respect to the tempering degree T2-T3.5 among the steel plates for soft cans. Here, “tempering degree” is an index indicating the hardness of tin or tin-free steel used as a steel plate for cans. In JIS G3303 and JIS G3315, Rockwell hardness (HR30T) and T2 is 53 ± 3. , T2.5 is 55 ± 3, T3 is 57 ± 3, and T4 is 61 ± 3. T3.5 is not particularly specified in JIS, but generally, it is valid as 59 ± 3 in terms of Rockwell hardness (HR30T) at an intermediate level between T3 and T4. Define as

  The problems to be solved by the present invention will be described below.

(1) Weldability
In a can manufacturer, various types of welding such as spot welding, projection welding, and seam welding are performed depending on the type of can. Further, it is often further processed after welding, and the can after being made can be used for various purposes, so that an excessive load may be applied to the welded portion. Therefore, the strength of the weld heat-affected zone is sufficiently secured for various types of welding, and cracks do not occur in the weld heat-affected zone during processing after welding and when a can is used at the customer site. is required.

(2) Non-aging
In can makers, paint baking is often performed before can making processing. When aging is accelerated by heating during paint baking, defects such as fluting and stretcher / strain occur during can manufacturing after baking. Therefore, it is necessary to be excellent in non-aging properties.

(3) Change in can height
Steel plates for soft cans may be used for welding can applications such as pail cans. These cans are often subjected to beading and expanding after seam welding. In that case, if the reduction amount of the can height by the bead processing or the expansion processing is large, a step may be generated between the welded portion where the can height is not reduced. Therefore, it is important that the can height does not decrease so much. To that end, the Rankford value needs to be low.

(4) Workability
As a result of detailed investigation, it was found that the steel sheet for soft cans by the conventional continuous annealing method is inferior in workability even in the case of the same tempering degree as compared with the steel sheet for soft cans by the batch annealing method. This is considered to be due to the fact that the continuous annealed steel sheet has a higher yield strength than the batch annealed steel sheet even if it has the same tempering degree. It is necessary to reduce yield strength and ensure the same level of workability as a batch-annealed steel sheet in order to avoid confusion when processing under the same can-making conditions as a batch-annealed steel sheet at a can manufacturer.

  The present invention has been made to solve the above-described problems, and has an object to provide a steel sheet for a soft can that is excellent in weldability, non-aging property, workability, and has a small reduction in can height, and a method for producing the same. To do.

(5) Hot ductility The steel to which N, B, Nb, Al, and C are added is nitrided with BN, Nb (N, C), AlN, etc. when the steel composition is transformed from γ to α. It was found that emulsification and carbonitride precipitated at large austenite grain boundaries, resulting in embrittlement and slab cracking during continuous casting. 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. For this reason, it is necessary to optimize the amounts of N, B, Nb, Al, and C, particularly the amount of N so as not to cause slab cracking.

  The inventors of the present invention have made various studies on steel components, crystal grain forms, production methods, etc., and have found a solution for soft cans having a tempering degree of T2 to T3.5.

(1) In the steel sheet for soft cans according to the present invention, the steel component is mass%, C: 0.0015 to 0.0050%, Mn: 0.1 to 0.8%, Al: 0.01 to 0. 10%, N: 0.0015 to 0.0070%, Nb: 4 × C to 20 × C (atomic ratio, 0.52 × C to 2.58 × C), B: 0.15 × N to 0.75 × N (in atomic ratio: 0.20 × N to 0.97 × N), the balance is made of Fe and inevitable impurities, manufactured by a continuous annealing method, and the average Rankford value r _ave is 1.3 to 1.8 and at least one of three relational expressions consisting of r0 <r45-0.2, r90 <r45-0.2, and | r0-r90 |> 0.3. And the tempering degree is in the range of T2 to T3.5.

  (2) In the steel sheet for soft cans according to the present invention, the steel components are mass%, C: 0.0015 to 0.0050%, Mn: 0.1 to 0.8%, Al: 0.01 to 0. 10%, N: 0.0015 to 0.0070%, Nb: 4 × C to 20 × C (atomic ratio, 0.52 × C to 2.58 × C), B: 0.15 × N to 0.75 × N (at an atomic ratio of 0.20 × N to 0.97 × N), the balance is made of Fe and inevitable impurities, manufactured by a continuous annealing method, and the length in the L direction of the ferrite crystal grains The average value Ls-ave at the surface layer, the maximum value Ls-max at the surface layer, the average value Lc-ave at the thickness center, and the maximum value Lc-max at the thickness center are Ls-ave / Lc-ave It satisfies the relationship of <0.9, satisfies the relationship of Ls-max / Lc-max <0.8, and has a tempering degree in the range of T2 to T3.5.

  (3) In the steel plate described in the above (1) or (2), non-recrystallized grains after continuous annealing are left in an area ratio of 0.5 to 5% in the cross section in the rolling direction.

(4) The method for producing a steel sheet for a soft can according to the present invention is a range of 70 to 90% as a cold rolling condition for the steel strip of any one of the above components (1) to (3). As a continuous annealing condition, the soaking time t is 20 to 90 seconds, the soaking temperature T is 700 to 780 ° C., and the soaking time t (seconds), the soaking temperature T (° C.), and the steel components (mass) %) Satisfies the relationship 770 ≦ t / 3 + T−14.8 × Log _e (Nb) −32 × B / N ≦ 840, and the tempering degree is obtained by performing temper rolling at a rolling rate of 0.5 to 5%. The range is from T2 to T3.5.

  According to the present invention, using a continuous annealing method that is more advantageous in terms of quality uniformity and production cost than the batch annealing method, it is possible to secure almost the same characteristics as a steel sheet for soft cans manufactured by the batch annealing method. It was.

  The present inventors have conducted various studies on the steel sheet for soft cans produced by the continuous annealing method, and as a result of intensive studies, the present invention has been completed. The present invention is described in detail below.

First, the reasons for limiting the Rankford value will be described. In the case of deep drawing of a two-piece can, a higher Rankford value is advantageous. If the average Rankford value r _ave is less than L3, problems such as fracture may occur during deep drawing. Therefore, in the present invention, the Rankford value r _ave is limited to 1.3 or more.

On the other hand, the steel plate for soft cans may be used not only for 2-piece cans but also for 3-piece cans. In the can body of a three-piece can, it is often subjected to can body processing such as expansion processing and bead processing after being formed into a cylindrical shape by seam welding. In this case, the can body is stretched in the circumferential direction, but if the Rankford value is large, the plate thickness is not reduced and the can height is likely to be reduced. On the other hand, if the Rankford value is small, the plate thickness tends to decrease, so the amount of reduction in can height is small. If the reduction amount of the can height is large, a step may be formed between the weld portion and the can height that does not change so much. According to the investigations so far, it has been found that when the Rankford value r _ave exceeds 1.8, the reduction in can height becomes significant. Therefore, the Rankford value is limited to 1.8 or less.

  In addition, in the can body of the three-piece can, it is necessary that the Rankford value in the circumferential direction of the can body is small, but because the plate is rolled so that the rolling direction of the steel plate or the coil width direction is the can body circumferential direction, It is desirable that the Rankford value in the rolling direction or the coil width direction is small.

  Specifically, when the Rankford values in the rolling direction, coil width direction, and 45 degree direction are r0, r90, and r45, respectively, (i) r0 <r45-0.2, (ii) r90 <r45-0. 2, (iii) When at least one of the three relationships | r0-r90 |> 0.3 is satisfied, a three-piece can having a small reduction in can height in can body processing is obtained. Therefore, in the present invention, one or more of these three inequalities are satisfied.

  Next, the crystal grain length in the rolling direction will be described.

  The steel sheet for soft cans by batch annealing is a steel sheet with a small ratio of yield strength to tensile strength (YR) because the crystal grains are sufficiently grown and solid solution C does not exist by annealing for a long time. Is obtained. On the other hand, the steel sheet for soft cans by the conventional continuous annealing method has a very short annealing time, and therefore YR tends to increase. The tempering degree, which is a general management index of steel plates for cans, is classified by Rockwell hardness (HR30T), and Rockwell hardness (HR30T) has a relatively good correlation with the average value of tensile strength and yield strength. It is done. Therefore, the conventional continuously annealed steel sheet has a higher yield strength than the batch annealed steel sheet even if it has the same tempering degree, and therefore, it is disadvantageous in terms of can manufacturing process that is considered to correspond to the yield strength. As a result of detailed studies, the present inventors have found that, in order to improve workability without changing the tempering degree in a continuously annealed steel sheet, there is a difference in the ferrite crystal grain size between the surface layer portion and the thickness center portion of the steel plate. Has been found to be effective.

  This is considered as follows. Rockwell hardness (HR30T) is measured by pressing an indenter into the surface of the steel sheet, and is affected by the crystal grain size on the steel sheet surface. However, the actual can manufacturing process corresponds to the yield strength of the steel sheet, so the crystal grain size of the entire steel sheet Affected by. Therefore, by making the ferrite crystal grain size larger in the center part of the plate thickness than in the surface layer part of the steel sheet in the continuously annealed steel sheet, can workability at the same level as that of the batch annealed steel sheet having the same tempering degree can be obtained. Specifically, regarding the length in the rolling direction of ferrite crystal grains, the average value Ls-ave at the surface layer, the maximum value Ls-max at the surface layer, the average value Lc-ave at the plate thickness center, and the maximum at the plate thickness center The above effects are exhibited when the value Lc-max satisfies Ls-ave / Lc-ave <0.9 and Ls-max / Lc-max <0.8. Therefore, when the same canning processability as that of batch-annealed steel sheets having the same tempering degree is required, the crystal grain length in the rolling direction is limited to this range. More preferably, Ls-ave / Lc-ave <0.8 and Ls-max / Lc-max <0.7.

  Next, the residual ratio of non-recrystallized grains will be described.

  As a result of detailed studies, it was found that the steel of the present invention increases the strength of the steel sheet even if a small amount of non-recrystallized grains remain, but the other properties do not change much. Therefore, unrecrystallized grains can be left to adjust the steel plate strength. When the area ratio of non-recrystallized grains in the cross section in the rolling direction is less than 0.5%, the effect of increasing the steel sheet strength is not recognized. On the other hand, if it exceeds 5%, the strength of the steel sheet is excessively increased, and adverse effects such as deterioration of can manufacturing process are exhibited. Therefore, when unrecrystallized grains remain in the present invention, the range is 0.5 to 5%.

Next, the reasons for limiting the steel components will be described.
(1) C: 0.0015 to 0.0050 mass%
As described below, carbon is an important element having two large influences on the properties of the steel sheet in the present invention.

  The first is the effect on non-ageing. If solid solution C is present in the steel, aging is promoted by painting and baking at a can manufacturer, and defects such as stretcher strain and fluting are generated in subsequent can manufacturing. In the present invention, since Nb is added to form NbC, the abundance of solid solution C is kept low. However, when the C content exceeds 0.0050%, the necessary Nb content also increases. Since Nb is an expensive element, it is disadvantageous in terms of production cost, and the steel sheet is excessively hardened by the precipitation strengthening effect of NbC, so the C content is limited to 0.0050% or less.

  The second is the effect on the can height reduction. It is known that the Rankford value is improved when recrystallization progresses in the annealing process in a state where no solid solution C exists. When the Rankford value is large, when the can body processing such as bead processing or expanding processing is performed on the welded can, the reduction amount of the can height increases. Therefore, in general-purpose applications, it is desirable to avoid an extreme rise in the Rankford value. Therefore, it is necessary to have some solute C present during annealing. When the amount of C is less than 0.0015%, C precipitated by hot rolling hardly re-dissolves during the continuous annealing. For this reason, it is necessary to make C amount 0.0015% or more. Therefore, the C content is in the range of 0.0015 to 0.0050% by mass ratio.

(2) Mn: 0.1 to 0.8% by mass
If the amount of Mn is less than 0.1%, hot brittleness may occur. On the other hand, if it exceeds 0.8%, the steel sheet is excessively hardened and the can-making processability is impaired. Therefore, the amount of Mn is made into the range of 0.1 to 0.8% by mass ratio.

(3) Al: 0.01 to 0.12% by mass
If the Al content is less than 0.01%, a sufficient deoxidation effect cannot be obtained. Further, by forming N and AlN, the effect of reducing the solid solution N in the steel cannot be sufficiently obtained. On the other hand, if it exceeds 0.10%, these effects are saturated, but inclusions such as alumina are likely to occur. Therefore, the amount of Al is set to a range of 0.01 to 0.12% by mass ratio.

(4) N: 0.0010 to 0.0070 mass%
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. 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, when N exceeds 0.0070%, the amount of B necessary for ensuring weldability increases. That is, the amount of BN precipitated in the crystal grains increases, and the steel sheet may be excessively hardened by the precipitation strengthening action. Therefore, the N amount is in the range of 0.0010 to 0.0070% by mass ratio.

  Also, from the viewpoint of hot ductility, the N content is set to 0.0070% or less. A more desirable N amount is in the range of 0.0044% or less. This is because when the N content is greater than 0.0070%, when the steel structure is transformed from γ to α (although it varies depending on the component, this steel has about 850 to 1000 ° C.), BN, Nb (N, C ), Nitrides such as AlN and carbonitrides are precipitated in large amounts at the austenite grain boundaries, resulting in embrittlement and slab cracking during continuous casting. 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.

(5) 4 × C ≦ Nb ≦ 20 × C
Nb is an important element for securing non-aging properties. Nb has the function of reducing the solid solution C in the steel by forming NbC, but in order to sufficiently exhibit its effect, 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 solid solution C is saturated, but the disadvantage of raising the recrystallization temperature arises. In addition, since Nb is expensive, production costs also increase. Therefore, it is necessary to suppress the Nb amount to 20 × C or less. Therefore, the Nb amount is in the range of 4 × C to 20 × C in terms of mass ratio (0.52 × C ≦ Nb ≦ 2.58 × C in terms of atomic ratio).

(6) 0.15 × N ≦ B ≦ 0.75 × N
As described below, B is an important element having two large influences on the properties of the steel sheet in the present invention.

  The first is the effect on weldability. Part of B exists in a solid solution state in the steel, but this solid solution B segregates at the grain boundaries, thereby suppressing abnormal grain growth and resulting softening in the HAZ part when welding is performed. To do. Since B tends to form BN, it is necessary to add an amount of B corresponding to the amount of N in order to cause a part of B to exist in a solid solution state. As a result of detailed investigation, when the amount of B is less than 0.15 × N by mass ratio, the HAZ portion is softened, and cracking may occur in the HAZ portion when processing is performed after welding.

  The second is the effect on the can height reduction. Nb-added ultra-low carbon steel shows a very high Rankford value, but if B is further added, the Rankford value decreases. Although the mechanism is not clear, it has been found that the addition of an appropriate amount of B lowers the Rankford value, and in particular, reduces the Rankford value in the rolling direction and the coil width direction. It has been found that this effect is exhibited by addition of B of 0.15 × N or more.

  In addition, as described above, the addition of B lowers the Rankford value, particularly the L-direction and C-direction Rankford values, so that it is necessary to set it to 0.15 × N or more from the viewpoint of sufficiently exerting the effect. . On the other hand, when the amount of B exceeds 0.5 × N, these effects tend to be saturated. On the other hand, if it exceeds 0.75 × N, there is a problem that the recrystallization temperature rises. Therefore, the amount of B is 0.15 × N to 0.75 × N in terms of mass ratio (0.20 × N ≦ B ≦ 0.97 × N in atomic ratio), and more preferably 0.15 × N to 0.5. XN. Moreover, in order to make an unrecrystallized part 1% or less on the annealing conditions of soaking time 30 seconds or more and soaking temperature 700 degreeC or more and 730 degrees C or less, B amount is 0.15 * N-0.60 * N is preferable.

  It has been found that when an appropriate amount of B is included, the ferrite crystal grain size is larger in the plate thickness center portion than in the surface layer portion of the steel plate. As described above, when the crystal grain size in the central portion of the plate thickness is larger than that in the surface layer portion, the workability is excellent for the tempering degree. The cause of the difference in crystal grain size between the surface layer and the center of the plate thickness due to B is not clear, but this phenomenon was not observed when B was too little or too much. Is unstable, it is estimated that there is a difference in the crystal grain size between the surface layer and the center of the plate thickness. The phenomenon that the ferrite crystal grain size becomes larger at the plate thickness center portion than the surface layer portion of the steel plate is recognized at 0.15 × N or more, and gradually decreases when exceeding 0.5 × N, and becomes 0.75 × N. When it exceeded, it was not recognized.

(7) S: 0.008% by mass or less S does not particularly affect the steel sheet characteristics of the present invention, but when the S content exceeds 0.008%, the N content exceeds 0.0044%. In this case, the hot ductility is lowered because BN, Nb (C, N), and AlN, which are nitrides and carbonitrides, are precipitated using MnS generated in a large amount as precipitation nuclei. Therefore, the S amount is desirably 0.008% or less.

(8) Inevitable impurities
In addition to the above components, steel contains unavoidable impurities such as Si and P. However, since these components do not particularly affect the steel plate characteristics of the present invention, other properties are not affected. It can be included as appropriate. Moreover, elements other than those described above can be added within a range that does not adversely affect the properties of the steel sheet.

Below, the manufacturing conditions of the steel plate of this invention are described.
The steelmaking conditions may be any method as long as the steel components specified in the present invention can be obtained, and are not particularly limited. However, it is desirable to manufacture the slab by continuous casting because of the uniformity of the slab. The reheating condition of the slab is not particularly limited, but if the temperature is too high, it is disadvantageous in terms of surface defects and energy costs, and if the temperature is too low, it is difficult to ensure the hot rolling finish temperature. Therefore, it is desirable that the temperature range is 1050 to 1300 ° C.

  The hot rolling conditions are not particularly limited, but the finishing temperature is preferably 860 to 950 ° C. from the viewpoint of the uniformity, surface properties, mechanical properties, and production cost of the hot rolled steel sheet. The coil winding temperature is preferably 550 to 720 ° C. for the same reason.

  As for pickling, it is only necessary to remove the scale of the surface, and no particular method is specified. About primary cold rolling, in order to obtain an appropriate rolling direction crystal grain length and an appropriate Rankford value, it is necessary to set it as 70 to 90% of range.

The continuous annealing condition is an important item in the present invention and will be described in detail below.
If the soaking time for continuous annealing is too short or the soaking temperature is too low, recrystallization does not progress sufficiently. In addition, the degree of progress of recrystallization varies depending on the amount of steel components Nb, B, and N. As a result of experimenting steels of various components, the degree of progress of recrystallization was found to have a good correlation with the value of Log _e (Nb) with respect to the Nb amount (mass%), and the B amount and N amount. Regarding (mass%), a good correlation with the value of B / N was recognized. The relation of the following equation (1) is established with respect to each parameter of soaking time t (second), soaking temperature T (° C.), steel component (mass%) Nb, B, and N that affects the degree of progress of recrystallization. It was also found from experiments conducted by the inventors of the present application that the value of A has a good correlation with the degree of progress of recrystallization.

A = t / 3 + T-14.8 × Log _e (Nb) −32 × B / N (1)
As shown in FIG. 1, when A <770, the unrecrystallized grain residual ratio exceeded 5%, and the can-making processability deteriorated. On the other hand, it has been found that if the A value is too large, grain growth after the completion of recrystallization is promoted, causing adverse effects.

  When A> 840, the average Rankford value rave sometimes exceeded 1.8 as shown in FIG. In the case of A> 840, as shown in FIGS. 3 and 4, the relations of inequality Ls-ave <Lc-ave × 0.9 and Ls-max <Lc-max × 0.8 are not satisfied. There was also.

  From these findings, it is limited to the following range (2).

770 ≦ t / 3 + T−14.8 × Log _e (Nb) −32 × B / N + ≦ 840
... (2)
If the soaking time is less than 20 seconds, the target structure may not be obtained even when the relationship of the above equation (2) is satisfied. On the other hand, when the soaking time exceeds 90 seconds, productivity decreases. For this reason, the soaking time is preferably in the range of 20 seconds to 90 seconds.

  Even when the soaking temperature is less than 700 ° C., the target structure may not be obtained even if the relationship of the above equation (2) is satisfied. On the other hand, when the temperature exceeds 780 ° C., there is a concern that an extremely thin material such as a steel plate for cans may break in the furnace or have a defective shape. For this reason, in the present invention, the soaking temperature is limited to a range of 700 to 780 ° C.

  Moreover, in order to reduce the solid solution C, an overaging treatment may be performed after maintaining the soaking temperature. Here, the method of the overaging treatment is not particularly defined, but in order to reduce the solid solution C to + minutes, it is desirable to hold at 350 to 450 ° C. for 30 to 90 seconds. For temper rolling, if the rolling rate is too low, it becomes impossible to correct the shape of the steel sheet and adjust the surface roughness. On the other hand, if the rolling rate exceeds 5%, the can-making processability is impaired by work hardening, so the content is made 5% or less.

  As for the surface treatment, tin plating, tin-free steel plating or the like is performed when corrosion resistance is required. Moreover, you may form organic resin membranes, such as polyester, as needed.

(Example)
Steel types A to U having various components shown in Table 1-1 and Table 1-2 are melted, and a vertical bending type continuous casting machine (vertical portion 3.5 m, bending radius 10 m, slab size width 1000 mm, thickness 230 mm), Or, after casting into a lab mold (140 mm × 140 mm × 370 mm, capacity 50 kg), lab slab rolling is performed to produce a slab, and the slab reheating temperature is 1250 ° C., the finishing temperature is 890 ° C., and the winding temperature is 620 ° C. Each was hot rolled. After these hot-rolled sheets were pickled with hydrochloric acid, cold rolling, continuous annealing, and temper rolling were performed.

In Tables 2-1 and 2-2, the cold rolling rate (%), the soaking temperature T (° C.) in the continuous annealing, the soaking time t (seconds), the A value of the formula (1) (= t / 3 + T-14.8 × Log _e (Nb) −32 × B / N (indicated as A in Table 2-1, Table 2-2, and Table 3)) and temper rolling ratio (%) are shown respectively. Then, it was made tin-free steel by performing electrolytic chromate treatment. Furthermore, in consideration of the fact that cans are processed after painting and baking by a can manufacturer, an aging heat treatment was performed at 210 ° C. for 10 minutes.

In addition, the tempered degree was obtained by measuring Rockwell hardness (HR30T) of the produced steel sheet, and a JIS No. 5 tensile test piece was collected to obtain the yield strength in the rolling direction, the rolling direction, the width direction, and the Rankford in the 45 degree direction. The values r0, r90, r45 were measured. The average value r _ave was obtained from the rankford values r0, r90, r45 in the three directions using the calculation formula r _{ave =} (r0 + r90 + 2 × r45) / 4. These results are also shown in Tables 2-1 and 2-2.

  Furthermore, in order to see the characteristics at the time of can-making, a three-piece can body molding and a two-piece can molding were performed on these steel plates. For 3-piece can body forming, roll forming is performed on a 400 x 850 mm rectangular blank under conditions such that the winding width (wrap amount at both ends after roll forming) is 0 to 3 mm, generating dust Both ends were joined by performing seam welding with an upper limit welding current to obtain a cylindrical can body having a diameter of about 270 mm. Next, expand processing with a maximum diameter increase rate of about 6% is performed, then beads with a bead height of 6 to 8 mm are processed, and finally flange processing is performed so that the flange width is 6 mm. Got. The can body of the three-piece can thus obtained was evaluated using the following evaluation criteria.

(Evaluation of non-aging of 3 piece can)
Non-aging was evaluated by the occurrence of fluting during roll forming. The determination was made according to the following evaluation criteria, and the results are shown in Table 2-1 and Table 2-2, respectively.
Double round (◎) indicates that no fluting was observed by visual inspection with the naked eye, single round (○) indicates that fluting was slightly observed but was not a problem in practice, and fluting occurred The results were displayed in crosses (x).

(Evaluation of weldability of 3-piece can)
As an evaluation of weldability, the HAZ crack occurrence rate when flanging was performed after seam welding was examined. The determination was made according to the following evaluation criteria, and the results are shown in Table 2-1 and Table 2-2, respectively.
When the polished surface of the sample taken from the welded portion is observed with a microscope, a HAZ crack occurrence rate of 0.5% or less is a double circle (◎), and a HAZ crack occurrence rate is more than 0.5% and 1% or less. Is indicated by a single circle (◯), and a HAZ crack occurrence rate exceeding 1% is indicated by a cross (×).

(Evaluation of can height change of 3 piece can)
As an evaluation of changes in can height, the amount of reduction in can height after expansion and bead processing was determined. The determination was made according to the following evaluation criteria, and the results are shown in Table 2-1 and Table 2-2, respectively.
Double round (◎) for can height reduction of 1 mm or less, single round (○) for can height reduction of over 1 mm and 1.5 mm or less, and can height reduction over 1.5 mm Each is indicated by a cross (x).

  Regarding the two-piece can molding, a circular blank having a diameter of 100 mm was punched out, and a drawing process with a drawing ratio of about 0.6 and a redrawing process with a drawing ratio of about 0.75 were performed.

(Evaluation of non-aging of 2-piece can)
As non-aging evaluation, it evaluated by the presence or absence of the stretcher strain in the site | part from the bottom of the can body to the bottom of the can. The determination was made according to the following evaluation criteria, and the results are shown in Table 2-1 and Table 2-2, respectively.
Double circles (◎) indicate no occurrence of stretcher strain by visual inspection or microscopic observation, single circles (○) indicate that stretcher strain is slightly observed but have no practical problems, and stretcher strain is What was generated was indicated by crosses (x).

(Evaluation of deep drawability of 2-piece can)
The deep drawability of the two-piece can was evaluated based on the ratio of the can broken by drawing and redrawing. The determination was made according to the following evaluation criteria, and the results are shown in Table 2-1 and Table 2-2, respectively.
Double circles (◎) are those with a fracture occurrence rate of 0.3% or less, single circles (○) are those with a fracture occurrence rate of more than 0.3% and 0.5% or less, and the fracture occurrence rate is 0.5%. Those exceeding the value were displayed as crosses (x).

  The Example was a pass judgment ((double-circle) or (circle)) regarding any evaluation item. On the other hand, in the comparative example, one or more evaluation items for rejection determination (x) existed.

  About a part of produced steel plate, the ferrite structure of the rolling direction cross section was taken out. The number of ferrite grain boundaries crossing a 300 μm long line in the rolling direction was measured at a half depth position of the sheet thickness as the center of the sheet thickness and a depth of 15 μm as the surface layer, and 300 μm / (grain boundary Number) was the average grain length. The longest crystal grain boundary interval in the range of 300 μm was the maximum crystal grain length. The ratio Ls-ave / Lc-ave between the average crystal grain length Ls-ave at the surface layer and the average crystal grain length Lc-ave at the center of the plate thickness, and the maximum crystal grain length Ls-max at the surface layer Table 3 shows the ratio Ls-max / Lc-max of the maximum crystal grain length Lc-max at the center of the plate thickness.

(Processability evaluation)
Workability was evaluated by a springback test. In the springback test, the springback angle was measured after bending 180 ° with a mandrel having a diameter of 1 inch (25.4 mm). The determination was made according to the following evaluation criteria, and the results are shown in Table 3.
Double round (◎) is the one less than 1.03 times the spring back angle of batch annealed steel sheets with the same temper and the same thickness, 1 of the spring back angle of batch annealed steel sheets with the same temper and the same thickness. .03 times or more and less than 1.05 times are indicated by a single circle (○), and those having a heat treatment angle of 1.05 times or more of a batch annealed steel plate of the same refining degree and the same thickness are indicated by crosses (×) did. The results are also shown in Table 3.

  In the examples, Ls-ave / Lc-ave> 0.9 and Ls-max / Lc-max> 0.8 were satisfied, and the springback evaluation result was also acceptable (◎ or ○). On the other hand, in the comparative example, either of Ls-ave / Lc-ave> 0.9 and Ls-max / Lc-max> 0.8 is not satisfied, and the springback evaluation result is also a failure determination (×). there were.

(Evaluation of surface crack of slab)
The surface cracks of the slab cast by the continuous casting machine were visually evaluated. The determination was made according to the following evaluation criteria, and the results are shown in Table 1-2. A double circle (◎) indicates that the surface crack of the slab was not visually observed, a crack that is 100 mm or less visually confirmed at the corner of the slab, and a single that can be handled by grinding the surface of the slab with a grinder A circle (◯), and a crack that had to be cut at the long side of the slab over a length of 100 mm or more, were indicated by crosses (×).

(Evaluation of hot ductility)
Surface cracks in slabs occur mainly at temperatures where the steel structure transforms from γ to α (approximately 850 to 1000 ° C), so the temperature history and tensile stress during continuous casting were simulated for hot ductility at 950 ° C. Evaluation was performed by a hot tensile test. The evaluation method was determined by obtaining the drawing value (cross section reduction rate) of the fracture surface in the high temperature tensile test at 950 ° C. A sample was directly cut out from a lab slab and processed by processing a round bar test piece having a parallel part diameter of 8 mm and a length of 15 mm. The high-temperature tensile test was performed in a vacuum using a high-frequency induction hot-working reproducibility tester, soaked at 1420 ° C for 60 seconds, rapidly cooled to the test temperature, and held at 950 ° C for 60 seconds. Thereafter, a tensile test was performed. The heating and cooling rates were 10 ° C./s and 5 ° C./s, and the strain rate was 2 × 10 ⁻³ . As the aperture value decreases, the hot ductility decreases and surface cracks of the slab tend to occur. The determination was made according to the following evaluation criteria, and the results are shown in Table 1-1 and Table 1-2, respectively. Double round (◎) indicates that the slab crack is not generated during continuous casting when the drawing value of the fracture surface after tensile test breakage is 35% or more, and the drawing value is 10% or more and less than 35% at the corner of the slab. A crack of 100 mm or less is confirmed visually, and a single circle (○) that can cope with the process of grinding the surface of the slab with a grinder, the aperture value is smaller than 10%, and the length of the slab is longer than 100 mm on the long side. Each of the corners of the slab that had to be cut due to cracks was indicated by a cross (x).

and t / 3 + T-14.8 × Log e (Nb) -32 × B / N, characteristic diagram showing the relationship between the non-recrystallization ratio. and t / 3 + T-14.8 × Log e (Nb) -32 × B / N, characteristic diagram showing the relationship between the Lankford value r _ave. t / 3 + T-14.8 × Log _e (Nb) −32 × B / N, and Ls-ave / Lc-ave (average length Ls-ave in the L direction of crystal grains in the surface layer and crystal at the center of the plate thickness) The characteristic figure which shows the relationship with the grain L direction length average value Lc-ave). t / 3 + T-14.8 × Log _e (Nb) −32 × B / N, Ls-max / Lc-max (the crystal grain L direction length maximum value Ls-max at the surface layer and the crystal at the center of the plate thickness) The characteristic figure which shows the relationship with the ratio of the grain L direction length maximum value Lc-max).

Claims (4)

Steel component is mass%, C: 0.0015-0.0050%, Mn: 0.1-0.8%, Al: 0.01-0.10%, N: 0.0015-0.0070 %, Nb: 4 × C to 20 × C (atomic ratio, 0.52 × C to 2.58 × C), B: 0.15 × N to 0.75 × N (atomic ratio, 0.20) × N to 0.97 × N), with the balance being Fe and inevitable impurities,
Manufactured by a continuous annealing method, the average Rankford value r _ave is in the range of 1.3 to 1.8, and r0 <r45-0.2, r90 <r45-0.2, | r0-r90 | A steel sheet for soft cans characterized by satisfying at least one of three relational expressions of> 0.3 and having a tempering degree in a range of T2 to T3.5. Steel component is mass%, C: 0.0015-0.0050%, Mn: 0.1-0.8%, Al: 0.01-0.10%, N: 0.0015-0.0070 %, Nb: 4 × C to 20 × C (atomic ratio, 0.52 × C to 2.58 × C), B: 0.15 × N to 0.75 × N (atomic ratio, 0.20) × N to 0.97 × N), with the balance being Fe and inevitable impurities,
Manufactured by the continuous annealing method, regarding the L direction length of ferrite grains, the average value Ls-ave at the surface layer, the maximum value Ls-max at the surface layer, the average value Lc-ave at the plate thickness center, and the plate thickness center Maximum value Lc-max satisfies the relationship of Ls-ave / Lc-ave <0.9 and satisfies the relationship of Ls-max / Lc-max <0.8, and the tempering degree is T2 to T3. A steel sheet for a soft can, characterized by being in the range of 5. The steel sheet for soft cans according to claim 1 or 2, wherein non-recrystallized grains after continuous annealing are left in an area ratio of 0.5 to 5% in a cross section in the rolling direction. Regarding the steel strip according to any one of claims 1 to 3,
As a cold rolling condition, the rolling rate is in the range of 70 to 90%,
The soaking time t is 20 to 90 seconds, the soaking temperature T is 700 to 780 ° C. as continuous annealing conditions, and
The relationship between the soaking time t (seconds), the soaking temperature T (° C.), and the steel component (mass%) is 770 ≦ t / 3 + T−14.8 × Log _e (Nb) −32 × B / N ≦ 840. Meet,
Rolling rate: A method for producing a steel sheet for a soft can, characterized by performing temper rolling of 0.5 to 5% to a tempering degree of T2 to T3.5.

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