A METHOD OF MANUFACTURING A COLD-ROLLED STEEL SHEET HAVING A GOOD DEEP DRAWABILITY

Abstract: A method of manufacturing a cold-rolled steel sheet hav­ ing a good deep drawability is disclosed, wherein a hot rolled steel sheet having a composition of C≦0.0035%, Si≦1.0%, Mn≦1.0%, Aℓ:0.005-0.10%, P≦0.15%, N≦0.0035%, S≦0.15%, Ti:( 48 / 14N(%)+ 48 / 32S(%)) or {4 x (C(%) + N(%))} ∼ (3· 48 / 12C(%) + 48 / 14N(%) + 48 / 32S(%)) and Nb:(0.2· 93 / 12C(%))∼( 93 / 12C (%))% is cooled within 2 seconds after the completion of fin­ isher rolling and then at an average cooling rate of not less than 10°C/sec until it arrives at a coiling step, and then the cooled steel sheet is coiled at a temperature of not more than 710°C, subjected to a cold rolling at a reduction of not less than 50%, which was subjected to a continuous annealing in a heatcycle inclusive of heating from 400°C to 600°C at a heating rate of not less than 5°C/sec and soaking at a temperature range of 700°C-Ac₃ point for 1 second or more.

Description: This invention relates to a method of manufacturing a cold-rolled steel sheet suitable for use in parts such as automotive bodies and so on which require press formability, and in particular deep drawability. More particularly, the careful application of such a continuous annealing process allows the effective manufacture of cold-rolled steel sheet which has a high ductility, small anisotropy in material, excellent deep drawability and resistance to ageing and secondary brittleness. In general, press-formable steel sheets have hitherto been manufactured by a box annealing process using a low carbon Aℓ-killed steel (C: 0.02-0.07% by weight; abbreviated as "%" hereinafter) as a starting material. Recently they have been manufactured by a continuous annealing process using extremely low carbon steel (C<0.01%) as the starting material in order to obtain better press formability and higher productivity. In such extremely low carbon steels, carbonitride-forming elements such as Ti, Nb, V, Zr, Ta and the like are added in order to fix any C and N soluted in steel, which would otherwise deteriorate the ductility, drawability and aging resistance of the steel sheet. Conventionally these elements were frequently added alone since they are expensive. A comparison between properties of Ti and Nb, which are most popularly used, is as explained below. Ti-containing steel has the advantage that the recrystallisation temperature is low, and the mechanical properties such as total elongation (Eℓ), Lankford value ( r -value) and so on are good, even when the steel is subjected to low temperature coiling at temperatures of not more than 600°C. This is in contrast to Nb-containing steel. On the other hand, Nb-containing steel has the advantage that the anisotropy of the r-value is small, and the phosphate treating property as a pretreatment for painting is good, in comparison with Ti-containing steel. Japanese Patent Application Publication No. 58-107,414 discloses the development of the advantages of both Ti and Nb simultaneously. In this case, the upper limit of the Ti is restricted to an amount given by the expression ( 48 / 12 C(%)+ 48 / 14 N(%)), which is intended to prevent ageing and ensure deep drawability since a greater part of the Ti is consumed as TiN and the solute C is fixed with the remaining effective Ti (effective Ti = total Ti - Ti as TiN) and Nb. In the manufacture of outer parts of automotive vehicles by press forming, stretch forming is mainly carried out rather than drawing. Thus, steel sheets having high ductility are of commercial significance. However, the Eℓ value of steels used in this technique lies within the range of 46.8-48.1% (corresponding to that of mild steel sheet), which does not correspond to a satisfactory level of elongation. It has been found by experiment that when the effective Ti range is in accordance with that used in the above technique, the C in steel is not effectively bonded to Ti. This results in considerable deterioration in ductility and drawability, as well as deterioration in ageing property resistance on account of the remaining solute C. EPA 0 108 268 discloses a method for the production of cold rolled steel sheet having deep drawability by the combined addition of specified amounts of Ti and Nb given by the expressions: 48 / 14 (N(%)- 0.002%) < Ti < 4 C(%)+ 3.43 N(%), 0.003 - 0.025 Nb(%) Nb(%) > 2.33 C(%) and Nb(%)+ Ti(%) < 0.04%. Steel sheet obtained by this method had the further benefit of a small anisotropy of the r value. It is an object of the present invention to provide a method of manufacturing cold-rolled steel sheet which has better deep drawability, by exploiting the beneficial effects of adding both Ti and Nb. The inventors have performed various investigations into a method of manufacturing cold-rolled steel sheet from extremely low carbon steel containing both Ti and Nb. It is desirable that the steel sheet should possess all the advantageous properties associated with the aforementioned extremely low carbon steels, notably the features of a good press formability, in particular a good deep drawability, a high ductility, a small anisotropy in material, and improved ageing resistance and resistance to secondary brittleness. The inventors have examined the effect of adding both Ti and Nb in detail, and have found that in the slab reheating step or hot roughing rolling step, the TiS and TiN are preferentially precipitated and the solute C is fixed with the remaining effective Ti and Nb in lower temperature region such as the hot finishing rolling step and after coiling. It has been found that the effective amount of Ti needed may be represented by an equation in which the effective Ti = total Ti - Ti as TiN - Ti as TiS. Thus, steel sheets which are suitable as press-formable steel sheets are first obtained by limiting the amount of each of C, N, S, Ti and Nb in extremely low carbon steel and strictly controlling the cooling conditions in the hot rolling, heating and cooling stages during continuous annealing. According to a first aspect of the present invention, there is provided a method of manufacturing a cold rolled steel sheet having a good deep drawability, which comprises hot rolling a sheet of steel having a composition comprising not more than 0.0035% of C, not more than 1.0% of Si, not more than 1.0% of Mn, 0.005-0.10% of Aℓ, not more than 0.15% of P, not more than 0.0035% of N, not more than 0.015% of S, ( 48 / 14 N(%)+ 48 / 32 S(%))∼ (3. 48 / 12 C(%)+ 48 / 14 N(%)+ 48 / 32 S(%)) of Ti and (0.2. 93 / 12 C(%)) ∼( 93 / 12 C(%)) of Nb with the balance being iron and incidental elements and impurities; commencing cooling of the sheet within 2 seconds after completion of the finisher rolling and cooling the steel sheet at an average cooling rate of not less than 10°C/sec until the coiling step is reached; coiling the cooled steel sheet at a temperature of not more than 710°C; subjecting the coiled steel sheet to cold rolling at a reduction of not less than 50%; and subjecting the cold rolled steel sheet to continuous annealing including a heatcycle comprising heating from 400°C to 600°C at a heating rate of not less than 5°C/sec and soaking at a temperature range of 700°C-Ac₃ point for not less than one second. According to a second aspect of the present invention, there is provided a method of manufacturing a cold rolled steel sheet having a good deep drawability, which comprises hot rolling a sheet of steel having a composition comprising not more than 0.0035% of C, not more than 1.0% of Si, not more than 1.0% of Mn, 0.005-0.10% of Aℓ, not more than 0.15% of P, not more than 0.0035% of N, not more than 0.015% of S, 4.(C(%)+N(%))∼(3. 48 / 12 C(%)+ 48 / 14 N(%)+ 48 / 32 S(%)) of Ti and (0.2. 93 / 12 C(%))∼( 93 / 12 C(%)) of Nb with the balance being iron and incidental elements and impurities; commencing cooling of the sheet within 2 seconds after completion of the finisher rolling and cooling the steel sheet at an average cooling rate of not less than 10°C/sec until the coiling step is reached; coiling the cooled steel sheet at a temperature of not more than 710°C, subjecting the coiled steel sheet to cold rolling at a reduction of not less than 50%; and subjecting the cold rolled steel sheet to continuous annealing including a heatcycle comprising heating from 400°C to 600°C at a heating rate of not less than 5°C/sec and soaking at a temperature range of 700°C-Ac₃ point for not less than one second. For a better understanding of the invention and to show how the same may be carried into effect, reference will now be made by way of example only, to the following drawings in which: Fig. 1 is a graph showing the effect of composition on the r -value of the steel sheet; and Fig. 2 is a graph showing the effect of composition on the AI-value of the steel sheet. In order to fully appreciate the effects of adding Ti and Nb according to the invention, it is necessary to limit the composition of the starting material. The details of the invention are illustrated by the following experimental results. Each of 18 steels having a chemical composition of trace-0.02% of Si, 0.10-0.12% of Mn, 0.007-0.010% of P, 0.02-0.04% of Aℓ, 0.0027% of N, 0.0020% of C, 0.006%, 0.013% or 0.018% of S, 0.015%, 0.025% or 0.034% of Ti, and 0.008% or 0.020% of Nb was produced by melting in a laboratory, and bloomed into a sheet bar having a thickness of 30 mm, hot rolled to a thickness of 2.8 mm at seven passes and then finally rolled at a temperature of 900±5°C. The resulting steel sheet was cooled to a temperature of 550°C at a rate of 35°C/sec by means of a water spray 0.8 second after the completion of final rolling. Then, the cooled steel sheet was immediately charged into a furnace at 550°C, held at this temperature for 5 hours and subjected to furnace cooling. A coiling temperature of 550°C was simulated by this furnace cooling. Thereafter, the cooled steel sheet was subjected to cold-rolling at a reduction of 75%, following pickling. Subsequently, the cold rolled steel sheet was subjected to continuous annealing, wherein it was heated to 700°C at a heating rate of 12°C/sec by means of a resistance heater, further heated to 780°C at a heating rate of 3°C/sec, held at 780°C for 25 seconds and cooled to room temperature at a cooling rate of 5°C/sec. Then, the resulting steel sheet was subjected to a skin-pass rolling of 0.7% and thereafter submitted to a tensile test. The r -value (Lankford value, a measure of deep drawability) and AI value (ageing index, a measure of ageing resistance) were used for testing purposes. As seen from the results in Figs. 1 and 2, the properties in each of the experimental steels largely vary in accordance with the amounts of Ti, S and Nb. If the values of r ≧ 1.6 and AI ≦ 3.0 are considered standard for the properties required for a press-formable steel sheet, both the above inequalities are satisfied within a region of Ti ≧ 48 14 N(%)+ 48 32 S(%) (N=0.0027%) and Nb=0.008%. However, it is found that even when the same amounts of C and Nb are present the drawability and the ageing resistance are deteriorated as the amount of S increases; consequently an increase in the amount of Ti present corresponding to the increase in S is required. On the other hand, the effect of increasing the amount of Nb present is to reduce the value of AI, the ageing resistance, even when the amount of Ti is small and the amount of S is large. However an increase in the amount of Nb present hardly results in any improvement of the r -value. C: It is advantageous that the amount of C is as low is possible in order to improve the total elongation (Eℓ) and Lankford value ( r -value). These values are the most important for formable steel sheet, and it is preferable that C ≦ 0.0035%, more preferably C ≦ 0.0030%. As the amount of C increases, large amounts of Ti and Nb are required to fix C as a carbide. Consequently, not only does the formability deteriorate, due to precipitation hardening of the resulting precipitates such as TiC, NbC and so on, but also other harmful effects, such as an increase in the recrystallisation temperature in continuous annealing and the like, manifest themselves. Si: Si may be added to increase the strength of high strength, deep drawable steel sheets. However, when an excess of Si is added both the resistance to secondary brittleness and the phosphate treating property deteriorate badly. Therefore, the upper limit of Si is restricted to 1.0%. Mn: Mn is also restricted to 1.0% for the same reason as in the case of Si. N: N alone is not harmful since it is fixed with Ti prior to the hot rolling, as is the case for S. However, TiN formed by excess addition of N deteriorates the total elongation and the r -value, so that the upper limit of N is restricted to 0.0035%, preferably not more than 0.0030%. Furthermore, when the amount of Ti is so small that N cannot be fixed with Ti, N is fixed as AℓN. In this case, when the coiling temperature of the hot rolled steel sheet does not exceed 710°C, the enlargement of AℓN does not proceed and consequently a hard product is obtained after continuous annealing which results in deterioration of the press formability. S: S is an important element according to the invention in relation to the amount of Ti present. S is rendered harmless as TiS during the heating of slab, prior to hot rolling. However, as seen from the results of Figs. 1 and 2, an excess of S results in an increase in the amount of Ti required for the fixation of S as TiS, which causes a degradation of the properties. Therefore, the upper limit of S is restricted to 0.015%. Ti: Ti is an important element according to the invention. Ti fixes S and N prior to Aℓ and Nb before the hot rolling. As previously illustrated in Figs. 1 and 2, the lower limit of Ti is determined by the amount required for fixing S and N, and may be expressed by the following equation: Ti ≧ ( 48 14 N(%)+ 48 32 S(%)). Furthermore, when the amount of C is relatively higher than the amount of S in atomic %, and definitely when the Ti, C, N and S amounts satisfy the following inequalities: Ti ≧ 48 14 N(%)+ 48 32 S(%) and Ti < 4.(C(%)+N(%)), the deep drawability is maintained at a suitable level, and although a little deterioration in the ductility is unavoidable it is not outside the scope of the first aspect of the invention. In such a case, the addition of a somewhat large amount of Ti, i.e. an amount of Ti satisfying the following inequality: Ti ≧ 4.(C(%)+N(%)) results in a further improvement in ductility; the second aspect of the invention is directed towards achieving this feature. This effect is considered to be due to the fact that whilst a larger amount of C results in a smaller size of TiC, thereby reducing the ductility, in this case the enlargement of TiC proceeds when an amount of Ti is added which is not less than 4(C+N). In view of the fact that part of the effective Ti amount (effective Ti = total Ti - Ti as TiN - Ti as TiS) forms TiC, the upper limit of Ti should be restricted to such an extent that the precipitated TiC and the remaining solute Ti do not cause a degradation of properties, an increase in the cost of the alloy and decrease the productivity (the decrease of productivity occurring as a result of the rising recrystallisation temperature). In consideration of these facts, the upper limit of Ti is restricted to Ti=(3. 48 12 C(%)+ 48 14 N(%)+ 48 32 S(%)). Nb: Nb is an important element for fixing C when the amount of Ti is low, and is required to be present in a minimum amount given by Nb=(0.2. 93 12 C(%)) In this lowest Nb amount, it is considered that Nb is able to fix only 20% of the solute C when C can not be fixed with Ti. However, it has been experimentally confirmed that most of the remaining 80% of solute C also forms a particular pre-precipitation stage around the precipitated NbC, which does not adversely affect the ageing resistance and the ductility. By adding Nb together with Ti the anisotropies of the r -value and Eℓ are reduced; these are drawbacks occurring in the addition of only Ti. For example, in the Ti-only containing steel having an average r -value of about 1.7, r-values in the rolling direction (r o ) and in direction perpendicular to the rolling direction (r₉₀) are about 2.1 and the r-value in a diagonal direction (r₄₅) is about 1.3, so that the anisotropy (Δr = (r₀ + r₉₀ - 2r₄₅)/2) is 0.8. On the contrary, in the Ti and Nb-containing steel according to the present invention, Δr becomes about 0.2-0.4 and the anisotropy becomes considerably small, which considerably reduces the occurrence of cracks during pressing. However, excess addition of Nb not only causes the degradation of properties at low temperature coiling in the hot rolling as shown in Figs. 1 and 2, but also results in a considerable rising increase in the recrystallisation temperature and cost, so that the upper limit of Nb is restricted to an amount equal to that of the C, i.e. to ( 93 / 12 C(%)). Aℓ: Aℓ is required in an amount of at least 0.005% for fixing O in molten steel and improving the yields of Ti and Nb. On the other hand, most of the N in steel is fixed with Ti as mentioned above, so that excess addition of Aℓ results in increased costs. Therefore, the upper limit of Aℓ is restricted to 0.10%. P: P is a most effective element for increasing the strength without decreasing the r -value. However, excess addition of P is unfavourable an account of its adverse effect on the resistance to secondary brittleness. Therefore, the upper limit of P is restricted to 0.15%. Turning now to the hot rolling conditions, the slab-heating temperature prior to hot rolling is not particularly restricted, but it must not be more than 1,280°C for fixing S and N with Ti, preferably not more than 1,230°C, and more preferably not more than 1,150°C. Incidentally, the same effect can be expected even when the slab is subjected to so-called direct rolling, or a sheet bar of about 30 mm in thickness obtained by casting is subjected to hot rolling as such. The final temperature in the hot rolling is preferably not less than the Ar₃ point. However, even if it is lowered to about 700°C in the α region, the degradation of properties is small. Incidentally, the grain size of ferrite ( α ) in the hot rolled steel sheet largely varies in accordance with the change of cooling pattern from completion of the final rolling to the coiling. In general, when the cooling rate from completion of final rolling to strip coiling is slow, α-grains become coarse. In the Ti, Nb composite-added steel according to the present invention, this tendency becomes especially noticeable. As the α-grains become coarser, not only is the intergranular area reduced, hence the (111) structure is not developed after annealing and the r -value is degraded, but also the grain size of crystals after the annealing becomes larger and the resistance to secondary brittleness is deteriorated. Therefore, it is essential that after completion of the final rolling, rapid cooling such as cooling with water spray is begun as soon as possible, definitely within 2 seconds of completion of final rolling and that the average cooling rate from the beginning of cooling to the coiling is not less than 10°C/sec. Good properties can be obtained even when the coiling temperature is not greater than 600°C, however, the properties are more improved when the high-temperature coiling is carried out above 600°C. The effect on the improvement of properties is saturated when the coiling temperature exceeds 710°C and also the descaling property is considerably deteriorated. Therefore, the upper limit is restricted to 710°C. In order to improve drawability it is required that the draft in the cold-rolling after the descaling is not less than 50%, preferably 70-90%. Insofar, as the continuous annealing conditions are concerned the Ti and Nb amounts are restricted in accordance with the C, N and S amounts as previously mentioned, such that steel sheets having considerably good deep drawability, good ageing resistance and anisotropy can be produced. However, the restriction of only these elements does not improve the resistance to secondary brittleness to a sufficient extent. For example, formable steel sheets such as those intended by the present invention are frequently used in deeply formed portions such as automobile high roofs, engine oil pans and the like. Therefore it is essential to improve the resistance to secondary brittleness. When the resistance to secondary brittleness is poor, the steel sheet is broken by strong shock after press forming and this is clearly undesirable in view of vehicle body safety. The addition of B (boron), Sb (antimony) or the like is considered as a method of improving the resistance to secondary brittleness. However, there are problems such as the recrystallisation temperature rises in the boron case and the cost increases in both cases. These problems are solved in the present invention by combining cooling control in the hot rolling, as previously mentioned, with heating control in the continuous annealing, as mentioned later. The heating rate from 400 to 600°C during heating must be not less than 5°C/sec. This restriction is required due to the fact that the solute P in steel is considerably prone to causing intergranular segregation in such a temperature region. Rapid heating is performed to prevent the intergranular segregation of P, whereby the intergranular strength is enhanced to improve the resistance to secondary brittleness. In the region of 600-400°C during cooling, the resistance to secondary brittleness is good without the need for any particular restriction, as there is in the heating stage. However, if quenching is performed at a cooling rate of not less than 10°C/sec in such a temperature region, the resistance to secondary brittleness is more improved. It is essential that the soaking is carried out at not less than 700°C over the period of one second in order to ensure the deep drawability of the steel after continuous annealing. On the other hand, when the heating temperature exceeds Ac₃ point (about 920-930°C), the deep drawability suddenly deteriorates, hence the heating temperature must be restricted to 700°C-Ac₃ point. The following examples are given as an illustration of the invention and are not intended as limitations thereof. Example 1 A steel having a chemical composition of C: 0.0024%, Si: 0.01%, Mn: 0.17%, P: 0.011%, S: 0.005%, Aℓ: 0.037%, N: 0.0021%, Ti: 0.022% ( 48 / 14 N(%)+ 48 / 32 S(%) = 0.0147%<Ti<3. 48 / 12 C(%)+ 48 / 14 N(%)+ 48 / 32 S(%)=0.0435%), Nb: 0.011% (0.2 93 / 12 C(%)=0.0372%<Nb<1.0. 93 / 12 C(%)=0.0186%), and other inevitable impurities was tapped out from a converter, subjected to an RH degassing treatment, and continuously cast into a slab. Then, the resulting slab was reheated to 1,160°C and finally hot rolled at 900°C. One second thereafter, the hot rolled steel sheet was rapid cooled on a hot runout table at a rate of 35°C/sec and then coiled at 530°C. The sheet was then subjected to pickling and cold rolled at a draft of 80%. The heating rate from 400 to 600°C in the continuous annealing was varied as shown in Table 1. In this case, the cold-rolled steel sheet was heated to 400°C at a heating rate of 15°C/sec and to 600-795°C at a rate of 4°C/sec, and subjected to soaking at 795°C for 40 seconds, after which the heated sheet was cooled from 795°C to 600°C at a cooling rate of 1.5°C/sec and in the region of not more than 600°C at rate of 5°C/sec. The results obtained after 0.5% skin-pass rolling are shown in Table 1. As seen from Table 1, the resistance to secondary brittleness is improved, without deteriorating the r -value and the ductility, by restricting the heating rate according to the invention. Example 2 Test steel sheets A-N, each having a chemical composition as shown in Table 2, were produced under hot rolling conditions as shown in Table 2. In this case, the production conditions except continuous annealing conditions were the same as in Example 1. The continuous annealing conditions were as follows: the steel sheet was heated to 400°C at a rate of 13°C/sec, from 400°C to 650°C at a rate of 6°C/sec and from 650°C to 810°C at a rate of 3°C/sec, and soaked at 810°C for 20 seconds, and thereafter cooled to room temperature at a rate of 10°C/sec. Continuous annealing was carried out according to the heatcycle as shown in Table 1, and the soaking conditions and so were the same as in Example 1. The mechanical properties of the resulting products after 0.5% skin-pass rolling are shown in the following Table 3. No. YS [MPa] (kgmm⁻²) TS [MPa] (kgmm⁻²) Eℓ (%) r Δr AI (MPa] (kgmm⁻²) Occurrence of brittle cracks A 142.2 (14.5) 283.4 (28.9) 52.3 2.25 0.41 0.00 (0.0) o B 164.8 (16.8) 306.9 (31.3) 45.9 1.75 0.22 11.8 (1.2) o C 237.3 (24.2) 336.4 (34.3) 42.5 1.38 0.48 44.1 (4.5) o D 252.0 (25.7) 334.4 (34.1) 41.8 1.29 0.29 13.7 (1.4) o E 154.9 (15.8) 302.0 (30.8) 48.5 1.89 0.35 0.00 (0.0) x F 184.4 (18.8) 306.0 (31.2) 44.8 1.45 0.31 37.3 (3.8) o G 161.8 (16.5) 302.0 (30.8) 48.3 1.91 0.33 0.00 (0.0) x H 155.9 (15.9) 303.0 (30.9) 48.5 1.78 0.95 2.94 (0.3) o I 207.9 (21.2) 328.5 (33.5) 45.1 1.38 0.11 0.00 (0.0) x J 157.9 (16.1) 297.1 (30.3) 49.4 2.02 0.19 0.00 (0.0) o K 140.2 (14.3) 286.4 (29.2) 51.8 2.31 0.36 0.00 (0.0) o L 148.1 (15.1) 294.2 (30.0) 50.0 2.01 0.39 4.90 (0.5) o M 201.0 (20.5) 363.8 (37.1) 44.8 1.91 0.22 2.94 (0.3) o N 234.4 (23.9) 425.6 (43.4) 39.1 1.71 0.20 4.90 (0.5) o O 159.8 (16.3) 304.0 (31.0) 47.9 1.76 0.23 8.83 (0.9) o P 166.7 (17.0) 299.1 (30.5) 49.2 1.96 0.31 0.00 (0.0) o The amount of carbon (C) in Comparative Steels B, C and O, the amounts of nitrogen (N) and sulphur (S) in Comparative Steels D and E, and the amount of Ti and Nb in relation to the amounts of carbon, nitrogen and sulphur in Comparative Steels F, G, H and I were outside the ranges defined by the present invention, respectively. These comparative steels had poor properties. Steels A, I and P and Steels L and M are examples of soft steel and high tensile steel sheet according to the first and second aspects of the present invention, respectively. In Steel J, the amount of Ti is somewhat lower than that in Steel P, but the other conditions are almost the same. Therefore, Steel J represents an example of the first aspect of the present invention. Accordingly, good properties were obtained in not only the mild steel sheet TS ≦ 343.2 MPa (35 kg mm⁻²) but also in the high tensile steel sheet containing a strengthening element such as P, Mn or the like. According to the present invention, it is possible to produce steel sheets satisfying all the conditions required for a press-formable steel sheet such as those used for automobile bodies or the like, whose reliability is utmost.

Claims: A method of manufacturing a cold rolled steel sheet having a good deep drawability, which comprises hot rolling a sheet of steel having a composition comprising not more than 0.0035% (by weight) of C, not more than 1.0% of Si, not more than 1.0% of Mn, 0.005-0.10% of Aℓ, not more than 0.15% of P, not more than 0.0035% of N, not more than 0.015% of S, ( 48 / 14 N(%)+ 48 / 32 S(%))∼ (3. 48 / 12 C(%)+ 48 / 14 N(%)+ 48 / 32 S(%)) of Ti and (0.2. 93 / 12 C(%)) ∼( 93 / 12 C(%)) of Nb with the balance being iron and incidental elements and impurities; commencing cooling of the sheet within 2 seconds after completion of the finisher rolling and cooling the steel sheet at an average cooling rate of not less than 10°C/sec until the coiling step is reached; coiling the cooled steel sheet at a temperature of not more than 710°C; subjecting the coiled steel sheet to cold rolling at a reduction of not less than 50%; and subjecting the cold rolled steel sheet to continuous annealing including a heatcycle comprising heating from 400°C to 600°C at a heating rate of not less than 5°C/sec and soaking at a temperature range of 700°C-Ac₃ point for not less than one second. A method of manufacturing a cold rolled steel sheet having a good deep drawability, which comprises hot rolling a sheet of steel having a composition comprising not more than 0.0035% of C, not more than 1.0% of Si, not more than 1.0% of Mn, 0.005-0.10% of Aℓ, not more than 0.15% of P, not more than 0.0035% of N, not more than 0.015% of S, 4.(C(%)+N(%))∼(3. 48 / 12 C(%) + 48 / 14 N(%)+ 48 / 32 S(%)) of Ti and (0.2. 93 / 12 C(%))∼( 93 / 12 C(%)) of Nb with the balance being iron and incidental elements and impurities; commencing cooling of the sheet within 2 seconds after completion of the finisher rolling and cooling the steel sheet at an average cooling rate of not less than 10°C/sec until the coiling step is reached; coiling the cooled steel sheet at a temperature of not more than 710°C, subjecting the coiled steel sheet to cold rolling at a reduction of not less than 50%; and subjecting the cold rolled steel sheet to continuous annealing including a heatcycle comprising heating from 400°C to 600°C at a heating rate of not less than 5°C/sec and soaking at a temperature range of 700°C-Ac₃ point for not less than one second.

Inventors: HASHIGUCHI, KOICHI, OKANO, SHINOBU, SAKATA, KEI, Hashiguchi, Koichi, c/o Kawasaki Steel Corp., Okano, Shinobu, c/o Kawasaki Steel Corp., Sakata, Kei, c/o Kawasaki Steel Corp.
Applicants: KAWASAKI STEEL CORPORATION
Application year: 1986
Main classification: C21D8
IPC codes: C21D8, C22C38, C21D9, B21B3