JP2013072110A - High-tensile, cold-rolled steel sheet excellent in surface quality after molding and method for manufacturing the same - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a high-tensile, cold-rolled steel sheet which is excellent in surface quality after molding and is useful as an automotive exterior and interior panels.SOLUTION: The high-tensile, cold-rolled steel sheet has a composition comprising, by mass%, 0.0005-0.0050% C, ≤0.50% Si, ≤2.00% Mn, ≤0.100% P, ≤0.020% S, 0.010-0.100% Ti, ≤0.080% sol. Al, ≤0.0070% N, provided that C, N, S and Ti satisfy the following relation (1): ([%Ti]/48-[%N]/14-[%S]/32)/([%C]/12)≥1.00 (wherein [%M] represents element M content in steel (mass%)), and the balance being Fe and unavoidable impurities.

Description

  The present invention relates to a high-tensile cold-rolled steel sheet excellent in surface quality after forming, which is suitable for application to an outer plate of an automobile and the like, and a method for producing the same.

  In recent years, in response to the growing needs for weight reduction of automobiles, not only skeletal parts but also outer plates have been made thinner and lighter by applying high-tensile steel plates. Since the formability of a steel sheet decreases with increasing tensile strength, many inventions have been made to improve the formability in the past. On the other hand, strict surface quality is required for outer plates and the like. The surface defects that influence the surface quality are roughly classified into those that are recognized on the surface in the manufacturing stage of the steel sheet and those that appear after being formed in the press line of an automobile.

The former surface defects are relatively easy to find, so the impact on automobile production is small. In addition, as disclosed in Patent Document 1, for example, measures at the material stage are also known.
On the other hand, since the latter surface defect may be found for the first time in the final inspection process after being molded into a part or further incorporated into a vehicle body, the influence on automobile production is extremely large.
Moreover, no effective countermeasure has been clarified so far for the means for suppressing the latter surface defects.

JP-A-9-296222

  The present invention has been developed in view of the above-mentioned present situation, and an object of the present invention is to propose a high-tensile cold-rolled steel sheet that is particularly excellent in surface quality after forming, together with its advantageous manufacturing method.

In order to solve the above-mentioned problems, the present inventors have intensively studied the generation mechanism of defects that appear as surface defects after molding and countermeasures for suppressing them.
As a result, in steel sheets where such surface defects occur, local uneven deformation due to yield point elongation occurs during the annealing process of the steel sheet, and it is clarified that this is the cause of surface defects after forming. It was done.

In other words, if non-uniform deformation occurs in the steel sheet during the annealing process, the hardness of the non-uniform deformation portion is larger than that of the non-deformation portion, and the amount of deformation is small. A deformation | transformation part floats up as a convex part, and becomes an external appearance defect. In addition, it becomes a sharp linear defect in appearance, and exhibits a form extending obliquely at 45 ° with respect to the longitudinal direction of the steel sheet.
At first, in so-called IF steel in which solute C and N were fixed, it was generally considered that the above-mentioned defects did not occur because a clear yield point elongation was not exhibited. However, as a result of the basic studies by the present inventors, in the state where temper rolling is not performed after annealing, it is possible to observe a small but distinct yield point elongation, and even for surface defects of the same form occurring in IF steel. It became clear that it was caused by the yield point elongation.

  In order to suppress the occurrence of surface defects as described above, it is sufficient that a strain amount exceeding the yield point is not given during annealing. In general, in a continuous annealing furnace, facility design and sheet passing conditions are set under conditions that do not cause strain exceeding the yield point of the steel sheet. However, in practice, it has become clear that due to thermal strain due to heating / cooling, locally uneven strain occurs, and under certain conditions, the yield point of the steel sheet may be exceeded.

Therefore, as a result of further study on the generation factors of surface defects caused by the above-described non-uniform deformation during annealing, the present inventors have obtained a constant cooling rate in a specific temperature range in the cooling process after completion of recrystallization. When it exceeded, the thermal strain which generate | occur | produces in a steel plate will become large, the distortion exceeding the yield point of a steel plate will generate | occur | produce, and the knowledge that the surface defect expressed after shaping | molding was acquired.
The present invention is based on the above findings.

That is, the gist configuration of the present invention is as follows.
1. In mass%, C: 0.0005 to 0.0050%, Si: 0.50% or less, Mn: 2.00% or less, P: 0.100% or less, S: 0.020% or less, Ti: 0.010 to 0.100%, sol.Al: 0.080% or less and N: A strip-shaped test piece containing 0.0070% or less, C, N, S, and Ti satisfying the relationship of the following formula (1), the balance being composed of Fe and inevitable impurities, and taken in the rolling direction A high-tensile cold-rolled steel sheet with excellent surface quality after forming, in which a linear pattern does not occur when the surface is ground with a 1-5% unidirectional tensile strain.
([% Ti] / 48 − [% N] / 14 − [% S] / 32) / ([% C] / 12) ≧ 1.00 (1)
Here, [% M] represents the content (mass%) of M element in steel.

2. Furthermore, when it contains at least one selected from Nb: 0.003 to 0.100% and B: 0.0003 to 0.0030% and contains Nb in mass%, the following formula (1) is substituted instead. The high-tensile cold-rolled steel sheet having excellent surface quality after forming according to the above 1, characterized by satisfying the relationship of formula (2).
{[% Nb] / 93 + ([% Ti] / 48 − [% N] / 14 − [% S] / 32)} / ([% C] / 12) ≧ 1.00 (2)
Here, [% M] represents the content (mass%) of M element in steel.

3. 3. The high-tensile cold-rolled steel sheet having excellent surface quality after forming according to the above 1 or 2, further comprising a zinc-based plating film on the surface of the steel sheet.

4). The steel slab comprising the component composition according to 1 or 2 is hot-rolled, pickled, then cold-rolled and then subjected to continuous annealing, and a temperature range of 400 to 200 ° C. is applied in the cooling process of the continuous annealing. A method for producing a high-tensile cold-rolled steel sheet having excellent surface quality after forming, characterized by cooling at a cooling rate not exceeding 30 ° C / s.

5). 5. The method for producing a high-tensile cold-rolled steel sheet having excellent surface quality after forming as described in 4 above, further comprising a plating treatment step of forming a zinc-based plating film on the steel sheet surface.

  ADVANTAGE OF THE INVENTION According to this invention, it becomes possible to provide the high tension cold-rolled steel plate which is excellent in the surface quality after shaping | molding.

Hereinafter, the present invention will be specifically described.
First, the reason why the component composition of the steel sheet is limited to the above range in the present invention will be described. In addition,% showing the following component composition shall mean the mass% unless there is particular notice.
C: 0.0005-0.0050%
When the content of C increases, deep drawability and ductility deteriorate and it becomes difficult to impart formability as an automobile outer plate. For this reason, the upper limit of the C amount is specified to be 0.0050%, preferably 0.0040%. On the other hand, if the content is less than 0.0005%, the crystal grains become coarse and the surface of the steel sheet is liable to be roughened when formed, so the lower limit of the C content is specified to 0.0005%.

Si: 0.50% or less,
Si is an element having a high solid solution strengthening ability. On the other hand, when the content is increased, not only the steel sheet is hardened but also surface defects due to scale are likely to occur. For this reason, the upper limit of Si content is specified as 0.50%.

Mn: 2.00% or less,
Mn is an element that can increase the strength of the steel sheet by containing Mn. On the other hand, when it adds excessively, deep drawability will fall. For this reason, the upper limit of the amount of Mn is specified as 2.00%. If the amount of Mn added is too small, the effect of increasing the strength may be insufficient. Therefore, the lower limit of the amount of Mn is preferably 0.50%, more preferably 0.60%.

P: 0.100% or less,
P is an effective element that can increase the strength of the steel sheet when the content increases even in a small amount. On the other hand, if contained excessively, ductility and weldability deteriorate. For this reason, the upper limit of the amount of P is specified as 0.100%.

S: 0.020% or less,
If the content of S is high, the toughness of the welded portion deteriorates as in the case of P. For this reason, the upper limit of the amount of S is suppressed to 0.020%, preferably 0.015%.

Ti: 0.010 to 0.100%
Ti is an especially important element in the present invention. By fixing solute C as carbide or carbonitride, it is possible to obtain deep drawability suitable for automobile outer plates and the like. If Ti is less than 0.010%, the desired effect cannot be obtained. On the other hand, the addition of more than 0.100% not only saturates the effect, but also hardens the steel sheet and deteriorates formability. It is specified as 0.100%.

sol.Al: 0.080% or less, N: 0.0070% or less
Since sol.Al and N do not impair the effects of the present invention as long as they are contained in ordinary steel, they are defined as sol.Al: 0.080% or less and N: 0.0070% or less, respectively.

Moreover, in order to control the amount of solute C, it is necessary to satisfy the following relational expression (1) for the amounts of C, N, S, and Ti.
([% Ti] / 48 − [% N] / 14 − [% S] / 32) / ([% C] / 12) ≧ 1.00 (1)
Here, [% M] represents the content (mass%) of M element in steel.
By satisfying the above relational expression, solid solution C can be completely fixed as TiC (TiCN) or a composite carbide or carbonitride thereof, and deep drawability suitable for an automobile outer plate can be obtained. . If the relational expression is not satisfied, the deep drawability deteriorates. Further, it is desirable that the left side of the above formula (1) is 1.20 or more to completely fix the solid solution C. On the other hand, even if the left side of the formula (1) exceeds 15.0, the fixing effect of solute C is saturated.

  The basic components have been described above. However, in the present invention, it is preferable that the following elements are appropriately contained as necessary.

Nb: 0.003 to 0.100%
Nb can be added in combination with Ti. Nb can be fixed as carbonitride and carbide by appropriately controlling the amount of Nb added relative to the amount of C. Here, if the amount of Nb is less than 0.003%, it is difficult to control the amount of dissolved C and the desired effect may not be obtained. On the other hand, if it exceeds 0.100%, the particle size becomes extremely fine and hardened. Therefore, the Nb content is specified in the range of 0.003 to 0.100%.

B: 0.0003 to 0.0030%
B is added in order to improve the secondary work embrittlement resistance of the deep-drawn parts. However, if the amount of B is less than 0.0003%, a desired effect cannot be obtained, while if it exceeds 0.0030%, it becomes hard and the formability deteriorates. Therefore, the amount of B is specified in the range of 0.0003 to 0.0030%.

And when it contains the said Nb, it replaces with the said Formula (1), and it is preferable to satisfy the following relational expressions (2).
{[% Nb] / 93 + ([% Ti] / 48 − [% N] / 14 − [% S] / 32)} / ([% C] / 12) ≧ 1.00 (2)
Here, [% M] represents the content (mass%) of M element in steel.
By satisfying the above relational expression, solid solution C is completely fixed as TiC (TiCN), NbC (NbCN) or their composite carbides, carbonitrides, and deep drawability suitable for automobile outer panels, etc. Can be obtained. If the relational expression is not satisfied, deep drawability may be deteriorated. Further, it is desirable that the left side of the above formula (2) is 1.20 or more and the solid solution C is completely fixed. On the other hand, even if the left side of the formula (2) exceeds 15.0, the fixing effect of the solute C is saturated.

  Moreover, V, W, Cu, Ni, Sn, Cr, Mo, Sb, etc. can be added for the purpose of improving surface quality by suppressing moldability such as deep drawability and surface element concentration in the manufacturing process. . The effects of the present invention are not impaired unless these addition amounts are larger than 0.5%. In addition, when adding Ca for the purpose of controlling the form of inclusions, or when increasing the upper limit of O content for the purpose of widening the allowable range of deoxygenation level to improve the efficiency during refining, 30 ppm and 50 ppm respectively. If the addition is not excessive, the effect of the present invention is not impaired.

  The balance other than the above-described components is Fe and inevitable impurities.

Evaluation of surface quality of cold-rolled steel sheet The following describes the evaluation method of surface quality after forming. As described above, surface defects that appear after molding may be found for the first time in the final inspection process after being molded into a part or after being incorporated into a vehicle body, compared to surface defects that appear at the manufacturing stage. Therefore, the impact on automobile production is extremely large. As a result of intensive investigations on the method of detecting streak defects due to local plastic deformation during the manufacturing process, the present inventors applied an appropriate amount of strain to the steel sheet, and by grinding the surface, It was clarified that it can be detected effectively.
As for the amount of strain, if it is too little or too much, the difference in deformation behavior due to the difference in hardness between the portion where plastic deformation has occurred and the portion where it does not become small, so about 1 to 5% is optimal. The test piece may be a strip-shaped test piece with the rolling direction as the longitudinal direction. Since it is necessary to check the entire width of the product, it is efficient to make the area as wide as possible within the specification range of the tensile test piece. Further, by using a test piece whose longitudinal direction is the test piece, a linear pattern (striped defect) can be appropriately evaluated.
In addition, the streak defect that appears after the tensile deformation that is the subject of the present invention is not a stretcher strain caused by so-called yield point elongation, but is only caused by local plastic deformation introduced into the steel sheet during the manufacturing process. This is due to the presence of a portion that is very small but harder than the surroundings. Stretcher strain has a strip shape with a width of 10 mm or more when pulled with a strip-shaped test piece, but the width of the defect targeted in the present invention is within 5 mm and exhibits a sharp linear shape. It is a feature.

Next, the manufacturing process of the present invention will be described.
In the present invention, the steel slab adjusted to the above component composition is cast, hot-rolled, pickled, then cold-rolled, and then subjected to continuous annealing to obtain a cold-rolled steel sheet. In the present invention, during the above-described continuous annealing, it is important to cool the temperature range of 400 to 200 ° C. particularly at a cooling rate not exceeding 30 ° C./s during the cooling process.

According to the study by the inventors, in the temperature range of 400 to 200 ° C., the yield strength is relatively low and the yield point elongation is clearly expressed. This temperature range is likely to cause uniform deformation. In this respect, in a temperature range exceeding 400 ° C., the yield strength is sufficiently low and the growth of dislocations is easy, so that non-uniform deformation hardly occurs. On the other hand, in the temperature range below 200 ° C., the yield strength is sufficiently high, and even if distortion occurs, the yield strength is not exceeded.
In addition, the cooling rate is set to 30 ° C./s or less because when the cooling rate exceeds this, the thermal strain generated by the shrinkage increases, resulting in uneven deformation locally exceeding the yield strength of the steel sheet. It is. On the other hand, the smaller the cooling rate, the smaller the strain at the time of cooling. However, if the limit is extremely small, the line length becomes too long.

In addition, the manufacturing process other than changing the cooling in the temperature range of 400 to 200 ° C. in the cooling process of the above-described continuous annealing to the above-described controlled cooling may be performed according to a conventional method and is not particularly limited. For example, it is possible to apply a slab manufacturing method by ingot forming or continuous casting, or continuous hot rolling by rough hot rolling bar connection in hot rolling. Further, a temperature rise within 200 ° C. using an induction heater in the hot rolling process does not adversely affect the effects of the present invention.
Regarding other suitable production conditions, the steel slab heating temperature in hot rolling is 1150 to 1300 ° C, the finish rolling finish temperature is 800 to 950 ° C, the coiling temperature is 500 to 700 ° C, and the rolling reduction in cold rolling is 50 The soaking temperature in continuous annealing (or continuous hot dip galvanizing) is preferably 750 to 900 ° C.
In this invention, it can also be set as the manufacturing method which has the plating process process which forms a zinc-type plating film on the steel plate surface. A zinc-based plating film of pure zinc or zinc alloy (zinc-iron, zinc-Ni, zinc-aluminum, etc.) can be formed on the steel plate surface by electroplating or hot dipping. In the case of galvanizing treatment, annealing and plating treatment can be made as separate steps, and annealing and plating treatment can be made into a series of steps (for example, continuous galvanizing). .

  In the case of a hot-dip galvanized steel sheet, even if the surface of the cold-rolled steel sheet is a plated steel sheet or a coated pre-coated steel sheet, the present invention is a process for imparting lubricity to the surface or a coating process. Even if it gives, the effect of this invention is not impaired.

Examples of the present invention will be specifically described below.
The steel adjusted to the component composition shown in Table 1 was made into a slab by continuous casting after melting, and it was made into a hot-rolled sheet under the conditions of heating temperature: 1200 ° C, finish rolling finishing temperature: 900 ° C, coiling temperature: 600 ° C. . Then, after pickling, cold rolling with a reduction ratio of 75% was made into a cold rolled sheet with a sheet thickness of 0.75 mm. Subsequently, continuous annealing or continuous hot dip galvanizing was performed under the conditions shown in Table 2 to obtain cold-rolled steel sheets or hot-dip galvanized steel sheets. Then, temper rolling with a rolling reduction of 0.3% was performed. The conditions of hot dip galvanizing are: plating bath temperature: 460 ° C, Al concentration of plating bath: (when alloying treatment is performed: 0.13%, when alloying treatment is not performed: 0.2%), plating coating amount: 45 g per side / m ² (double-sided plating), alloying treatment temperature: 480 to 580 ° C., alloying degree (Fe mass%): 10%.

Next, strip test pieces with a length of 150 mm and a width of 30 mm were collected from these coils (steel strips) with the rolling direction as the longitudinal direction, and taken to a tensile testing machine (crosshead speed: 10 mm / min). 1%, 3% and 5% strain was applied (the tensile direction is the longitudinal direction). Thereafter, a pre-strained test piece was placed on a flat desk, the surface was abraded, and the presence or absence of a linear pattern (streaky defect) was examined (in Table 2, ○: no defect, ×: Defect) The presence / absence of defects was visually observed, and x was indicated when streak defects were observed even at one location.
As for mechanical properties, a tensile test (crosshead speed: 10 mm / min) was performed using a JIS No. 5 test piece, and a tensile strength TS and a total elongation EL were measured. The tensile test was evaluated with test pieces taken along the rolling direction.
Furthermore, the deep drawability is determined by using JIS No. 5 test piece, r value of 0 °, 45 °, 90 ° direction with respect to the rolling direction (crosshead speed: 10mm / min, giving pre-strain 15%) r0, r45 and r90 were measured, and an average value (r0 + 2 × r45 + r90) / 4 was calculated and evaluated.
The obtained results are also shown in Table 2.

From Table 2, according to the present invention, by controlling the cooling rate in the temperature range of 400 to 200 ° C. after continuous annealing to 30 ° C./s or less, excellent deep drawability and no streak defects occur after molding. It was found that high-tensile cold-rolled steel sheets and hot-dip galvanized steel sheets can be obtained.
In addition, when the steel plate temperature is lower than 200 ° C., the yield strength of the steel plate is sufficiently increased, and it can be seen that no streak defect occurs even when the steel plate is cooled at a rate exceeding 30 ° C./s.

According to the present invention, it is possible to stably produce and supply a high-tensile cold-rolled steel sheet having excellent surface quality after forming, which is extremely useful for automobile outer plates and inner plates, and has an extremely high industrial value.

Claims (5)

In mass%, C: 0.0005 to 0.0050%, Si: 0.50% or less, Mn: 2.00% or less, P: 0.100% or less, S: 0.020% or less, Ti: 0.010 to 0.100%, sol.Al: 0.080% or less and N: A strip-shaped test piece containing 0.0070% or less, C, N, S, and Ti satisfying the relationship of the following formula (1), the balance being composed of Fe and inevitable impurities, and taken in the rolling direction A high-tensile cold-rolled steel sheet with excellent surface quality after forming, in which a linear pattern does not occur when the surface is ground with a 1-5% unidirectional tensile strain.
([% Ti] / 48 − [% N] / 14 − [% S] / 32) / ([% C] / 12) ≧ 1.00 (1)
Here, [% M] represents the content (mass%) of M element in steel. Furthermore, when it contains at least one selected from Nb: 0.003 to 0.100% and B: 0.0003 to 0.0030% and contains Nb in mass%, the following formula (1) is substituted instead. The high-tensile cold-rolled steel sheet having excellent surface quality after forming according to claim 1, wherein the relationship of formula (2) is satisfied.
{[% Nb] / 93 + ([% Ti] / 48 − [% N] / 14 − [% S] / 32)} / ([% C] / 12) ≧ 1.00 (2)
Here, [% M] represents the content (mass%) of M element in steel.   The high-tensile cold-rolled steel sheet having excellent surface quality after forming according to claim 1 or 2, further comprising a zinc-based plating film on the surface of the steel sheet.   A steel slab comprising the composition according to claim 1 or 2 is hot-rolled, pickled, then cold-rolled and then subjected to continuous annealing, and a temperature range of 400 to 200 ° C in the cooling process of the continuous annealing. Is produced at a cooling rate not exceeding 30 ° C./s, and a method for producing a high-tensile cold-rolled steel sheet having excellent surface quality after forming. The method for producing a high-tensile cold-rolled steel sheet having excellent surface quality after forming according to claim 4, further comprising a plating treatment step for forming a zinc-based plating film on the steel sheet surface.