Method for production of blister-resistant steel sheet

Abstract: Blister-resistant steel sheet consists essentially of 0.0005 to 0.003wt.% C, 0.10 to 2.2wt.% Mn, 0.6wt.% or less Si, 0.07wt.% or less P, 0.025wt.% or less S, 0.02 to 0.06wt.% of sol. Al, 0.0035wt.% or less N, 0.003wt.% or less O, [(48/14)N + (48/32)S + 4 x (48/12)C] wt.% or less Ti and the balance being Fe and inevitable impurities; and smaller one of either Ti (wt.%) or [(48/14)N + (48/32)S] (wt.%) being [0.002 t² + 0.003] or more, where t is a thickness (mm) of the steel sheet. Method for producing blister-resistant steel sheet comprises preparing a cold rolled steel sheet having the composition of described above, and continuously annealing or continuous hot dip galvanizing by heating the steel sheet from room temperature to 650 - 720°C at a rate of 20°C/sec or more and further to the soaking temperature above recrystallization temperature at a rate of 1 - 5°C/sec.

Description: The present invention relates to a method for producing blister-resistant steel sheets for use in automobiles or household electric appliances. In particular, the present invention relates to a method for producing blister-resistant steel sheets using extremely low carbon steel as the body material. Recent development of the technology of steel making and of degassing allowed the commercial production of extremely low carbon steels containing 50ppm or less of carbon and nitrogen at a relatively low cost. By adding Ti and Nb, which form carbide and nitride, to the extremely low carbon steel, what is called "IF steel" (carbon and nitrogen are fixed in the steel) was produced. The IF steel was introduced in JP-B-44-18066, JP-B-54-1245, and JP-A-59-67319 (the terms "JP-B-" and "JP-A-" referred to herein signify "examined Japanese patent publication" and "unexamined Japanese patent publication", respectively). The IF steel is widely used in cold rolled steel sheets which need good formability mainly of deep drawing. Compared with common low oxygen Al-killed steel, however, that type of IF steel likely generates blister after the final heat treatment. Blister is a rounded swelling on the surface of metal to an approximate size of lmm in width and 10mm in length. Thicker steel sheet induces blister more easily. Since blister bursts open during the processing such as press-forming, it is classified as a surface defect. If any blister is found on the product steel sheet at manufacturer's product inspection, the steel sheet is rejected. Accordingly, compared with the frequency of blister generation in manufacture line, the frequency for users to deal with the blister as a serious problem is not necessarily high. As a result, very few papers and patents deal with the blister on IF steel. Nevertheless, for the material manufacturers, the generation of blister results in a significant decrease of productive yield, and particularly when some blisters which could not be found at user's inspection burst open during the processing such as press-forming, the defect iii the processing results in the reduction of productivity. Cold rolled steel sheets which meet the compositional requirements of the present invention are disclosed in each of the following EP-A-documents : - 444 967, - 484 960 and - 295 697. EP-A-0 444 967 discloses cold-rolled steel sheets or hot-dip galvanized steel sheets for deep drawing which have excellent resistance to cold-work embrittlement, and having a chemical composition containing, all by mass, 0.01% or less C, 0.2% or less Si, 0.05-1.0% Mn, 0.10% or less P, 0.02% or less S, 0.0005-0.8% sol. Al, and 0.006% or less N, and further containing Ti (mass %) and/or Nb (mass %) solely or in combination within a range in which the relationship between the effective amount of Ti (hereinafter referred to as Ti*) defined by the following formula (1) and the amounts of Nb and C satisfy the following formula (2): Ti* = total Ti - {(48/32) x S + (48/14) x N} 1 ≦ (Ti*/48 + Nb/93)/(C/12) ≦ 4.5 and the balance of Fe and inevitable impurities. The steel sheets are characterized by having a concentration gradient that, as a result of carburizing, the amount of solid-solute carbon decreases, as it goes through the thickness direction from the surface towards the center of said steel sheets, and that a maximum value of concentration of solid-solute carbon present in a part of a one-tenth gage ratio of a surface layer is set at 15 mass ppm, and the amount of solid-solute carbon contained in the entire part of said steel sheets is set at 2 to 10 mass ppm. EP-A-0 484 960 discloses a cold rolled steel strip having excellent combined press form ability, consisting, by weight, of not more than 0.0025% C, not more than 0.05% Si, not more than 0.30% Mn, not less than 0.007% but not more than 0.30% P, not more than 0.020% S, not more than 0.080% sol. A1, not more than 0.0030% N, not less than 0.025% but not more than 0.120% Ti, not less than 0.003% but not more than 0.020% Nb, not more than 0.0004% B, and the balance Fe and incidental impurities, said steel strip having tensile strength in 45° direction of 28.5 to 31.0 kgf/mm 2 and r value in 45° direction of not less than 1.90. EP-A-0 295 697 discloses a cold rolled steel sheet having improved strength and toughness in weld portion, and which comprises not more than 0.004 wt% of C, not more than 0.1 wt% of Si, not more than 0.5 wt% of Mn, not more than 0.025 wt% of P, not more than 0.025 wt% of S, not more than 0.0040 wt% of N, 0.01∼0.04 wt% of Ti, 0.003∼0.010 wt% of Nb, 0.0001∼0.0010 wt% of B, 0.01∼0.10 wt% of A1 and the remainder being substantially Fe, and fine precipitates of Ti having a grain size of not more than 0.05µm are uniformly dispersed into said steel in an amount of not less than 30 ppm as Ti conversion amount. The object of the present invention is to provide a method for producing a blister-resistant steel sheet. To achieve the object, the present invention provides a method for producing a blister-resistant steel sheet comprising: (i) preparing a cold rolled steel sheet consisting of 0.0005 to 0.003wt.% C, 0.10 to 2.2wt.% Mn, 0.6wt.% or less Si, 0.07wt.% or less P, 0.025wt.% or less S, 0.02 to 0.06wt.% sol. A1, 0.0035wt.% or less N, 0.003wt.% or less O, [(48/14)N + (48/32)S + 4 x (48/12)C] wt.% or less Ti, optionally at least one element selected from the group consisting of 0.003 to 0.03wt.% Nb and 0.0003 to 0.0015wt.% B, and the balance being Fe and inevitable impurities; the smaller one of either Ti (wt.%) or [(48/14)N + (48/32)S] (wt.%) being [0.002 t 2 + 0.003] or more, where t is the thickness (mm) of the blister resistant steel sheet; (ii) continuously annealing the cold rolled steel sheet by heating the steel sheet from room temperature to a temperature in the range 650-720°C at a rate of 20°C/sec or more, and then continuing to heat the steel sheet to the soaking temperature (which is greater than the recrystallization temperature of the steel) at a rate of 1-5°C/sec; and (iii) temper rolling the continuously annealed steel sheet. Further the present invention provides a method for producing a blister-resistant zinc hot dip galvanising sheet comprising: (a) preparing a cold rolled steel sheet according to step (i) of the above method; (b) continuously hot dip galvanizing by heating the steel sheet from room temperature to a temperature in the range 650-720°C at a rate of 20°C/sec or more and then continuing to heat the steel sheet to the soaking temperature (which is greater than the recrystallization temperature of the steel) at a rate of 1-5°C/sec; and (c) temper rolling the continuously hot dip galvanized steel sheet. According to a further aspect, the present invention provides a method for producing a blister-resistant electroplated steel sheet comprising: (i) preparing a blister-resistant steel sheet according to the above method, and (ii) electroplating the temper rolled steel sheet. Fig. 1 shows the relation between oxygen content of the present invention and percent defective caused by blistering; Fig. 2 shows the relation between [Ti - {(48/14)N + (48/ 32)S}] / (48/12)C of the present invention and percent defective caused by blistering; Fig. 3 shows the relation between smaller one of either Ti wt.%) or [(48/14)N + (48/32)S] (wt%) and percent defective caused by blistering; Fig. 4 shows the relation between heating rate at the first stage and the second stage of the present invention and percent defective caused by blistering; Fig. 5 shows the relation between steel sheet thickness of the present invention and percent defective caused by blistering; Fig. 6 is a microscopic photograph ( x 100) showing a typical blister on IF steel sheet observed on the section lateral to rolling direction; and Fig. 7 is a microscopic photograph ( x 400) of blister on the same IF steel sheet as used in Fig. 6. The inventors investigated the mechanism of blister generation and the countermeasures against blistering, and optimized the composition of steel to obtain a steel sheet having excellent blister resistance. Regarding the blister defects, the inventors clarified the followings. The blister defect is a rounded swelling on the surface of metal caused by the crack which started from Al 2 O 3 being located at a depth around 0.1 to 0.2mm from the surface and which developed parallel to the sheet surface plane. When this type of Al 2 O 3 exists in a cluster shape, blister defect occurs even if the steel is not the one with extremely low carbon content. However, in the case that secondary oxidized Al 2 O 3 is distributed in a form of scattered islands of several microns to sub-micron in each size, blister defect occurs in an extremely low carbon steel. The cause of blister defect is, as shown in Fig. 6 and Fig. 7, the depletion of solid solution carbon which has the role of strengthening the grain boundaries, which induces grain boundary cracks easily. In concrete terms, the following steps presumably occur. Hydrogen which was concentrated to the surface layer during pickling is diffused into central region of the steel to form a solid solution. During the last stage of final heat treatment or after the treatment, atomic hydrogen is again diffused to concentrate into the deformed region generated by the difference of thermal expansion coefficient between Al 2 O 3 and matrix interface and into the fine pores generated from the decohesion at interface caused by the cold rolling. Then, the diffused and concentrated hydrogen is gasified to increase its volume, which induces the grain boundary cracks. The tendency of increasing the frequency of defect generation with the increase in steel sheet thickness is explained by the increase of hydrogen supply in the thickness direction. From the above described finding, the inventors concluded that the following three measures are effective to prevent the blister generation in extremely low carbon steel sheets, and based on the conclusion, this invention was completed. (a) To reduce the amount of Al 2 O 3 which is the initiating point of blistering. (b) To suppress the hydrogen diffusion. (c) To strengthen the grain boundaries which are the propagation route of cracks. The reason why the content of elements of the invented steel is specified will now be described as follows;. C: 0.0005 - 0.003wt.% Less C content is more preferable for formability. On the other hand, C is an essential additive element for blister resistance because C strengthens grain boundaries. Consequently, the range of C content is specified to 0.0005 - 0.003wt.%. Mn: 0.1 - 2.2wt.% Since Mn plays a role of deoxidizer element, it is necessary to add Mn to reduce the amount of Al 2 O 3 which is the initiating point of crack. Excess addition of Mn, however, results in the degradation of formability. Accordingly, the range of Mn content is specified to 0.1 - 2.2wt.%. Si: 0.6wt.% or less Although Si has a function to strengthen by solid solution, excess addition of Si induces the degradation of formability. Therefore, the upper limit of Si content is specified to 0.6wt.%. P: 0.07wt.% or less Phosphorous has a function to strengthen by solid solution. However, excess addition of P should be avoided from the viewpoint of blister resistance because P is an element to enhance brittleness of grain boundaries. Accordingly, the upper limit of P content is specified to 0.07wt.%. S: 0.025wt.% or less Excess S addition weakens grain boundaries, enhances blister generation, and induces cracks during hot rolling. Smaller content of S is more favorable, and the upper limit is specified to 0.025wt.%. sol. Al: 0.02 - 0.06wt.% Aluminum addition is needed to deoxidize the molten steel. However, excess addition of Al increases Al 2 O 3 which is not favorable for the blister prevention. Accordingly, the range of sol. Al content is specified to 0.02 - 0.06wt.%. N: 0.0035wt.% or less From the standpoint of formability, less N addition is more favorable, and the upper limit is specified to 0.0035wt.%. Nevertheless, N and S react with Ti to precipitate to play a role of trapping site of hydrogen, which suppresses the generation of blister. Therefore, the content of combined N and Ti shall be kept in a range specified in the description of Ti given below. O: 0.003wt.% or less When O addition exceeds 0.003wt.%, the generation of blister becomes significant. The trend is clearly shown in Fig. 1 which gives the relation of oxygen content and percent defective caused by blistering. Increase of O content increases Al 2 O 3 which causes blistering, and enhances the blister generation. Consequently, the upper limit of O content is specified to 0.003wt.%. In Fig. 1, the symbol ○ designates No. 1 through No. 35 steel of the present invention, and the symbol  designates No. 37 through No. 39 and No. 64 of comparative steel. Ti: Titanium is a useful element to fix C and N and to improve formability. To prevent blister generation, Ti is used in a form of TiN and TiS to trap hydrogen. To trap hydrogen, addition of a large amount of Ti is favorable. However, to avoid brittleness of grain boundaries, less Ti is more favorable. Accordingly, the Ti addition is specified to the amount which satisfies both equations given below. Ti (wt.%) ≤ [(48/14)N + (48/32)S + 4 x (48/12)C] wt.% min. [Ti, (48/14)N + (48/32)S] ≥ 0.002t 2 + 0.003 where t in equation (2) is the steel sheet thickness (mm), and the expression of {min. [Ti, (48/14)N + (48/32)S]} means the smaller one of either Ti or {(48/14)N + (48/32)S}. Titanium other than the one becomes to nitride and sulfide combines with C, which depletes the C in the grain boundary region and enhances blister generation. Therefore, equation (1) indicates the necessity to avoid excess addition of Ti. Stoichiometrically, Ti and C bound each other at a rate of 1 : 1. Actually, however, several times as much of Ti as of C, is necessary. Fig. 2 shows the frequency of blister generation as the function of [Ti - {(48/14)N + (48/32)S}] / (48/12)C. In Fig. 2, the symbol ○ designates No. 1 through No. 35 steel of the present invention, and the symbol  designates No. 54 through No. 60, and No. 65 of comparative steel. Fig. 2 indicates that when Ti other than the one formed nitride and sulfide exceeds [4 x (48/12)C], the blister generation increases rapidly. In other words, when Ti (wt.%) exceeds [(48/14)N + (48/32)S + 4 x (48/12)C] (wt.%), the blister generation increases rapidly. In concrete terms, if the Ti addition is controlled to keep the amount of Ti except for that Ti which is combined with N and S, at 4 times or less of the stoichiometric amount of C, then the presence of C at grain boundary region is secured to suppress the blister generation. Equation (2) was derived after analyses of a large volume of data from various viewpoints, and was verified by laboratory experiments. Equation (2) is a core of this invention. Equation (2) indicates that when the thickness of steel sheet increases, it is necessary to increase (TiN + TiS) precipitate, not solely increase Ti addition. Accordingly, the prevention of hydrogen diffusion is important to suppress the blister generation, and the fine precipitate acts as the trapping sites. The inventors analyzed the collected data on various kinds of precipitates and found that TiN and TiS trap hydrogen more effectively. To suppress the blister generation, it is extremely important to adequately control the amount of the precipitate of these compounds responding to the thickness of steel sheet. Strictly speaking, even if the same amount of precipitate is produced, the change of production condition varies the size of precipitate and varies the surface area to trap hydrogen. The effect of manufacturing condition is, however, relatively small, and, as shown in Fig. 3, when the condition satisfies the equation (2), sufficient result is expected. In Fig. 3, the symbols of ○ and □ designate No. 1 through No. 35 of the steel of this invention, and the symbols of  and ▪ designate No. 40 through No. 53, and No. 61 through No. 63 of the comparative steel. The symbols of □ and ▪ are for the case of Ti < [(48/14)N + (48/32)S], and the symbols of ○ and  are for the case of Ti > [(48/14)N + (48/32)S]. In Fig. 3, the A zone which satisfies the condition of equation (2) gives 0.09% or less of the percent defective caused by blistering, and the B zone gives 0.12 - 0.19% of percent defective caused by blistering, and the C zone gives 0.21% or higher percent defective caused by blistering. The steel sheet thickness applied to this invention is preferably in a range of from 0.3 to 3.0mm. When the sheet thickness is less than 0.3mm, the frequency of blister generation itself decreases, so the necessity to control chemical composition appeared in the present invention is slight. When the sheet thickness exceeds 3.0mm, Ti, S, and N have to be added to a great extent to secure the amount of TiN and TiS, which may degrade the surface quality. The above described composition is the basic scheme of the present invention. Nevertheless, the present invention may further add at least one element selected from the group consisting of 0.003 to 0.03wt.% Nb and 0.0003 to 0.0015wt.% B. Nb: 0.003 - 0.03wt.% Niobium fixes C and improves formability. In addition, after heat treatment, Nb makes a part of C free again. Addition of 0.003wt.% Nb or more improves the blister resistance. However, addition of a large amount of Nb saturates the effect and degrades the formability. Consequently, the addition of Nb is preferably in a range of 0.003 - 0.03wt.%. B: 0.0003 - 0.0015wt.% Boron is an element to strengthen grain boundaries without competing against C. Addition of 0.0003wt.% B or more gives an effect to suppress blister generation. However, excess addition of B saturates the effect and degrades the formability. Accordingly, the upper limit of B addition is specified to 0.0015wt.%. The following is the description of the manufacturing method. According to the manufacturing method of the present invention, the control of heating rate during annealing is an important condition. Although the detailed mechanism is not clear, the two step heating rate control suppresses the blister generation. Fig. 4 shows the relation between the percent defective caused by blistering and the heating rate at the first lower temperature zone and at the second higher temperature zone. The encircled figures in Fig. 4 designate the percent defective ( x 10 -2 %) of the steel No. 20, 27, 29, and 33. The prefix alphabet at the upper left of each circle corresponds to the manufacturing condition listed on Table 4. As seen in Fig. 4, in the two step heating control process, the rapid heating at a rate of 20°C/sec or more up to 650 - 720°C is followed by the gradual heating at a rate of 1 to 5°C/sec up to the soaking temperature above the recrystallization temperature. Hydrogen which is a cause element of blistering concentrates on the surface layer of steel sheet mainly by the reaction occurred during pickling. A part of the hydrogen concentrated to the surface layer is emitted to atmosphere during the heating stage of annealing process. Most of the concentrated hydrogen, however, form solid solution and diffuse to distribute in the thickness direction. When the steel sheet is rapidly heated, the steel sheet becomes to a high temperature while keeping the relatively high surface hydrogen concentration, which enhances the degree of emission of hydrogen, which was concentrated to the surface layer, into atmosphere. Nevertheless, at the temperature zone more than 650 - 720°C, the amount of solid solution of hydrogen in the steel increases, which in turn reduces the dependency of the hydrogen emission on heating rate so that the rapid heating is no longer necessary. The temperature range which needs the rapid heating is up to 650 - 720°C. On the contrary, when a rapid heating is applied in a high temperature zone, the difference of thermal expansion coefficient of Al 2 O 3 and matrix induces decohesion at the interface and develops the phenomenon. In the case of gradual heating, the stress relaxation effect of matrix suppresses the generation and development of interfacial decohesion. Blister defect occurs from the diffusion and concentration of hydrogen into the decohesion portion at the final period of and after the cooling process. Consequently, from the point of suppressing the blister generation, the combination of rapid heating at the lower temperature zone and gradual heating at the higher temperature zone, which was described above, is required. To do the heating, the heating rate is limited to 20°C/sec or more up to 650 - 720°C, then to 1 - 5°C/sec to the soaking temperature above the recrystallization temperature. The reason why the lower limit of heating rate at the higher temperature zone is defined to 1°C/sec is that the heating rate below 1°C/sec needs a long period until the system reaches a holding temperature, which requires elongated annealing line and scale up of facilities to degrade the economy of the production line. Fig. 1 through 4 show the data plot of embodiment. The comparative steels in Fig. 1 do not satisfy the specified range of O content of the present invention. The comparative steels in Fig. 2 do not satisfy the specified range of T wt.% ≤ [(48/14)N + (48/32)S, + 4 x (48/12)C] wt.% of the present invention. The comparative steels in Fig. 3 do not satisfy the min. [Ti, (48/14)N + (48/32)S] ≥ (0.002 t 2 + 0.003) of the present invention. The comparative steels in Fig. 4 do not satisfy the heating rate condition during annealing of the present invention. The steel sheet of the present invention is prepared following a known practice by melting in a converter or electric furnace and casting, by hot rolling directly or after re-heating, and by pickling and cold rolling to set a specified thickness. The cold rolled steel sheet of the present invention includes not only the one prepared by continuous annealing but also the one prepared by cold rolling or continuous annealing followed by hot dip galvanizing or electrolytic zinc plating. Furthermore, the steel sheet of the present invention includes the one subjected to surface treatment applying at least one of organic coating and chemical conversion treatment. Zinc plating includes Zn-Alloy, Zn-Ni and Zn-A1 plating. Example Table 1(A) and 1(B) shows the composition of steels of the present invention, and Table 2 shows the composition of comparative steels. Table 3 lists the thickness of steels and the state of blister generation on them which are listed in Table 1(A) and 1(B) and Table 2. The basic manufacturing conditions are the following. The hot rolled steel sheets were prepared by two methods. The first method employed the continuous casting, direct hot rolling, cooling on a run-out table, and coiling. The second method employed the continuous casting, cooling to room temperature, re-heating to 1200 - 1300°C, hot rolling, cooling on a run-out table, and coiling. The obtained hot rolled steel sheets gave 2.8 - 4.5mm of thickness. The average finish temperature of the hot rolling was 900°C, and coiling temperature was 640°C. The obtained hot rolled steel sheets were subjected to pickling, cold rolling, continuous annealing at the temperature range of 760 - 870°C, and temper rolling with a reduction of 0.5%. After the treatment above described, blister generation was investigated. Regarding the material subjected to hot dip galvanizing, the material was treated by cold rolling, continuous annealing at 820°C, cooling to 460°C, hot dip galvanizing of 55g/m 2 of coating weight per side, and being alloyed at 500°C. The Zn plated material was further treated by temper rolling with a reduction of 1.0% and by zinc coating with 80%Fe-Zn alloy of 3g/m 2 of coating weight per side. As for the material subjected to electroplating steel sheet, the material was treated by temper rolling and electroplating with 88%Zn-Ni alloy of 30g/m 2 of coating weight per side. For the material subjected to electroplating - organic coating, the material was treated by electroplating, then by composite coating of chromate layer of 50g/m 2 of coating weight and resin layer of 1 µm of thickness. Except for Table 4 and Fig. 5, the heating rate during the continuous annealing or continuous hot dip galvanizing was 20°C/sec from room temperature to 700°C and 1°C/sec from 700°C to soaking temperature. As the parameter for the analysis of blister generation, the length of one blister was counted as 1.5m, and the total counted length for all the blisters was divided by the total coil length. The obtained value was taken as the percent defective caused by blistering. With the percent defective, the blister resistance was evaluated. The mark *1 at the top right of Table 1 designates [(48/14)N + (48/32)S], and the mark *2 designates [(48/14)N + (48/32)S + 4 x (48/12)C]. The steels No. 3, 10, and 15 in Table 1 are the material prepared by direct hot rolling, pickling, cold rolling, continuous annealing and temper rolling. The steels No. 4, 11, 17, 27, 31, and 34 are the material prepared by re-heating and hot rolling, pickling, cold rolling, continuous annealing, hot dip galvanizing and temper rolling. The steel No. 5 is the material prepared by re-heating and hot rolling, pickling, cold rolling, continuous annealing, temper rolling and organic coating. The steels No. 6 and 32 are the material prepared by re-heating and hot rolling, pickling, cold rolling, continuous annealing, temper rolling and electroplating. Materials other than the above described were prepared by re-heating and hot rolling, pickling, cold rolling and continuous annealing. The mark *1 at the top right of Table 2 designates [(48/14)N + (48/32)S], and the mark *2 designates [(48/14)N + (48/32)S + 4 x (48/12)C]. The figure with * mark indicates that the value does not satisfy the specified range of composition of the present invention. The steels No. 37, 48, and 51 in Table 2 are the material prepared by direct hot rolling, pickling, cold rolling, continuous annealing and temper rolling. The steels No. 40, 49, and 56 are the material prepared by re-heating and hot rolling, pickling, cold rolling, continuous annealing and hot dip galvanizing and temper rollilng. The steel No. 43 is the material prepared by re-heating, hot rolling, pickling, cold rolling, temper rolling, electroplating and organic coating. The steel No. 50 is the material prepared by re-heating and hot rolling, pickling, cold rolling, continuous annealing, temper rolling and elelctroplating. Materials other than the above described were prepared by re-heating and hot rolling, pickling, cold rolling, continuous annealing and temper rolling. From the reasons listed below, the comparative steels gave 0.12% or more percent defective caused by blistering. (a) The comparative steels No. 37 through 39 and No. 64 contained an increased amount of O which relates to Al 2 O 3 , the initiating point of blistering. (b) The comparative steels No. 40 through 53 and No. 61 through 63 contained not much TiN and TiS, both of which trap hydrogen. (c) The comparative steels No. 36, No. 54 through 60, and No. 65 lacked the solid solution of C and suffered with a weakened grain boundaries. To the contrary, the steels of the present invention showed 0.09% or lower percent defective. In particular, the steels No. 26 through 28 and No. 33 through 35, which included B, improved the percent defective to 0.05% or less. The percent defective caused by blistering was further investigated by changing the heating rate during continuous annealing or continuous hot dip galvanizing. Table 4 shows the heating rate at lower temperature zone and at higher temperature zone, and the inflection point of heating curve for both the steels of the present invention and the comparative steels. Table 5 lists the percent defective of the steels No. 20, 27, 29, and 33 at each heating rate. Fig. 4 shows the percent defective under various heating rates. The horizontal axis is the heating rate at high temperature zone, and the vertical axis is the heating rate at low temperature zone. The steels treated by the heating rate of 20°C/sec or more at low temperature zone and of 1 - 5°C/sec at higher temperature zone further reduced their percent defective, compared with the steels treated by the heating rate out of the above specific range, which validated the effect of the invention. Fig. 5 shows the relation between the steel sheet thickness of the present invention and percent defective caused by blistering. In the figure, the symbol ○ designates the steels No. 1 through 35 of the present invention, and the symbol  designates the comparative steels No. 36 through 65. The comparative steels increase the frequency of blister generation with the increase of sheet thickness. On the contrary, the steel sheets of the present invention keep the frequency of blister generation at a very low level even with a thick sheet. Thus, the remarkable effect of the present invention is confirmed. Steel sheet thickness t (mm) 0.002t 2 +0.003 Percent defective (%) Steel sheet thickness t (mm) 0.002t 2 +0.003 Percent defective (%) 1 1.2 0.0059 0.06 34 1.6 0.0081 0.05 2 0.6 0.0037 0.02 35 1.2 0.0059 0.03 3 0.7 0.0040 0.03 36 1.5 0.0075 0.32 4 1.8 0.0095 0.01 37 1.6 0.0081 0.28 5 1.4 0.0069 0.02 38 1.5 0.0075 0.16 6 1.2 0.0059 0.01 39 1.8 0.0095 0.14 7 1.5 0.0075 0.00 40 1.5 0.0075 0.14 8 0.8 0.0043 0.00 41 1.3 0.0064 0.18 9 1.0 0.0050 0.06 42 0.8 0.0043 0.12 10 0.9 0.0046 0.00 43 2.0 0.0110 0.33 11 1.6 0.0081 0.02 44 2.0 0.0110 0.13 12 1.2 0.0059 0.04 45 1.8 0.0095 0.21 13 0.8 0.0043 0.03 46 1.6 0.0081 0.40 14 0.8 0.0043 0.02 47 2.7 0.0176 0.48 15 0.4 0.0033 0.01 48 1.7 0.0088 0.14 16 1.6 0.0081 0.09 49 1.2 0.0059 0.12 17 0.8 0.0043 0.07 50 2.1 0.0118 0.23 18 1.8 0.0095 0.08 51 2.0 0.0110 0.13 19 1.4 0.0069 0.02 52 1.9 0.0102 0.15 20 1.6 0.0081 0.06 53 1.5 0.0075 0.18 21 1.0 0.0050 0.06 54 1.4 0.0069 0.25 22 1.9 0.0102 0.07 55 0.8 0.0043 0.15 23 1.5 0.0075 0.06 56 1.5 0.0075 0.17 24 1.2 0.0059 0.06 57 1.7 0.0088 0.12 25 1.3 0.0064 0.04 58 1.2 0.0059 0.13 26 0.7 0.0040 0.04 59 0.9 0.0046 0.18 27 1.2 0.0059 0.04 60 2.0 0.0110 0.52 28 2.8 0.0187 0.03 61 1.5 0.0075 0.18 29 2.0 0.0110 0.07 62 1.8 0.0095 0.19 30 1.5 0.0075 0.05 63 1.9 0.0102 0.17 31 1.2 0.0059 0.08 64 2.0 0.0110 0.16 32 1.8 0.0095 0.08 65 1.6 0.0081 0.22 33 1.4 0.0069 0.04 Condition Heating rate at lower temperature zone (°C/sec) Heating rate at higher temperature zone (°C/sec) Inflection point on heating speed curve (°C) Example of this invention A 20 1 700 B 20 2 650 C 20 5 680 D 30 2 720 E 50 1 700 F 50 2 700 G 50 5 700 H 75 2 700 Comparative example I 5 2 700 J 10 2 700 K 10 10 700 L 30 10 700 Condition Steel No. 20 Steel No. 27 Steel No. 29 Steel No. 33 Example of this invention A 0.06 0.04 0.07 0.04 B 0.06 0.04 0.06 0.03 C 0.06 0.05 0.06 0.04 D 0.04 0.03 0.04 0.02 E 0.04 0.03 0.04 0.03 F 0.03 0.03 0.04 0.02 G 0.06 0.05 0.06 0.05 H 0.03 0.03 0.04 0.02 Comparative example I 0.09 0.08 0.09 0.08 J 0.08 0.08 0.09 0.07 K 0.09 0.08 0.09 0.08 L 0.08 0.07 0.09 0.07

Claims: A method for producing a blister-resistant steel sheet comprising: (i) preparing a cold rolled steel sheet consisting of 0.0005 to 0.003wt.% C, 0.10 to 2.2wt.% Mn, 0.6wt.% or less Si, 0.07wt.% or less P, 0.025wt.% or less S, 0.02 to 0.06wt.% sol. A1, 0.0035wt.% or less N, 0.003wt.% or less O, [(48/14)N + (48/32)S + 4 x (48/12)C] wt.% or less Ti, optionally at least one element selected from the group consisting of 0.003 to 0.03wt.% Nb and 0.0003 to 0.0015wt.% B, and the balance being Fe and inevitable impurities; the smaller one of either Ti (wt.%) or [(48/14)N + (48/32)S] (wt.%) being [0.002 t 2 + 0.003] or more, where t is the thickness (mm) of the blister resistant steel sheet; (ii) continuously annealing the cold rolled steel sheet by heating the steel sheet from room temperature to a temperature in the range 650-720°C at a rate of 20°C/sec or more, and then continuing to heat the steel sheet to the soaking temperature, which is greater than the recrystallization temperature of the steel, at a rate of 1-5°C/sec; and (iii) temper rolling the continuously annealed steel sheet. A method for producing a blister-resistant zinc hot galvanizing steel sheet comprising: (i) preparing a cold rolled steel sheet according to step (i) of Claim 1; (ii) continuously hot dip galvanizing by heating the steel sheet from room temperature to a temperature in the range 650-720°C at a rate of 20°C/sec or more and then continuing to heat the steel sheet to the soaking temperature (which is greater than the recrystallization temperature of the steel) at a rate of 1-5°C/sec; and (iii) temper rolling the continuously hot dip galvanized steel sheet. A method for producing a blister-resistant electroplated steel sheet comprising: (i) preparing a blister-resistant steel sheet according to Claim 1, and (ii) electroplating the temper rolled steel sheet.

Inventors: HOSOYA YOSHIHIRO, KANETOH SHUJI, KOHIRA SATOSHI, KOYANAGI DAIJIRO, NAKAMURA HIROMI, TSUYAMA SEISHI, HOSOYA, YOSHIHIRO, KANETOH, SHUJI, KOHIRA, SATOSHI, KOYANAGI, DAIJIRO, NAKAMURA, HIROMI, TSUYAMA, SEISHI, Hosoya, Yoshihiro, c/o Intellectual Property Dept., Kanetoh, Shuji, c/o Intellectual Property Dept., Kohira, Satoshi, c/o Intellectual Property Dept., Koyanagi, Daijiro, c/o Intellectual Property Dept., Nakamura, Hiromi, c/o Intellectual Property Dept., Tsuyama, Seishi, c/o Intellectual Property Dept.
Applicants: NIPPON KOKAN KK, NKK CORPORATION
Application year: 1993
Main classification: C22C38
IPC codes: C22C38