Method for manufacturing galvanized steel sheet

Abstract

A method for manufacturing a galvanized steel sheet includes heating a base steel sheet in a heating zone such that the surface of the base steel sheet is heated at a temperature of 600 C. or higher and 790 C. or lower while a furnace temperature T C. in the heating zone of an annealing furnace is controlled based on the water vapor partial pressure P.sub.H2O.sup.in Air of air fed into the heating zone, the base steel sheet having a chemical composition consisting of, by mass %, C: 0.05% or more and 0.25% or less, Si: 0.1% or more and 3.0% or less, Mn: 0.5% or more and 3.0% or less, P: 0.001% or more and 0.10% or less, Al: 0.01% or more and 3.00% or less, S: 0.200% or less, and the balance being Fe and inevitable impurities, heating the base steel sheet in the heating zone such that the surface of the base steel sheet is heated at a temperature of 630 C. or higher and 850 C. or lower in an atmosphere containing hydrogen gas having a partial pressure P.sub.H2O of 1000 Pa or more and 50000 Pa or less, water vapor gas having a partial pressure P.sub.H2O of 610 Pa or less, and the balance being N.sub.2 and inevitable impurities, and galvanizing the base steel sheet.

Claims

1. A method for manufacturing a galvanized steel sheet, the method comprising; heating a base steel sheet in a heating zone such that a surface of the base steel sheet is heated at a temperature of 600 C. or higher and 790 C. or lower, the base steel sheet having a chemical composition containing, by mass %, C: 0.05% or more and 0.25% or less, Si: 0.1% or more and 3.0% or less, Mn: 0.5% or more and 3.0% or less, P: 0.001% or more and 0.10% or less, Al: 0.01% or more and 3.00% or less, S: 0.200% or less, and the balance being Fe and inevitable impurities, during the heating, controlling a furnace temperature T C. in the heating zone of an annealing furnace based on the water vapor partial pressure P.sub.H2O.sup.in Air of air fed into the heating zone, subsequently, heating the base steel sheet in the heating zone such that the surface of the base steel sheet is heated at a temperature of 630 C. or higher and 850 C. or lower in an atmosphere containing hydrogen gas having a partial pressure P.sub.H2 of 1000 Pa or more and 50000 Pa or less, water vapor gas having a partial pressure P.sub.H2O of 610 Pa or less, and the balance being N.sub.2 and inevitable impurities, and galvanizing the base steel sheet.

2. The method for manufacturing a galvanized steel sheet according to claim 1, wherein the furnace temperature T C. is controlled so as to satisfy the following relationships:
6900.03P.sub.H2O.sup.in AirT7900.03P.sub.H2O.sup.in Air in the case where P.sub.H2O.sup.in Air3000 Pa, or
600T700 in the case where 3000 Pa<P.sub.H2O.sup.in Air20000 Pa.

3. The method for manufacturing a galvanized steel sheet according to claim 2, wherein the chemical composition further contains Mo: 0.01% or more and 1.00% or less and/or Cr: 0.01% or more and 1.00% or less.

4. The method for manufacturing a galvanized steel sheet according to claim 3, wherein alloying treatment is performed after galvanizing.

5. The method for manufacturing a galvanized steel sheet according to claim 2, wherein alloying treatment is performed after galvanizing.

6. The method for manufacturing a galvanized steel sheet according to claim 1, wherein the chemical composition further contains Mo: 0.01% or more and 1.00% or less and/or Cr: 0.01% or more and 1.00% or less.

7. The method for manufacturing a galvanized steel sheet according to claim 6, wherein alloying treatment is performed after galvanizing.

8. The method for manufacturing a galvanized steel sheet according to claim 1, wherein alloying treatment is performed after galvanizing.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

(1) FIG. 1 is a correlation diagram illustrating the relationship between manufacturing conditions (the furnace temperature T and the water vapor partial pressure P.sub.H2O.sup.in Air of air fed into the furnace) and the evaluation results of surface appearance.

DETAILED DESCRIPTION OF EMBODIMENTS OF THE INVENTION

(2) Embodiments of the present invention will be specifically described hereafter.

(3) First, a preferable chemical composition of a base steel sheet used in an embodiment of the present invention will be described. Here, % used when describing the content of an element represents mass %, unless otherwise noted.

(4) C: 0.05% or more and 0.25% or less

(5) It is beneficial that the C content be 0.05% or more in order to increase the strength of steel sheet. On the other hand, in the case where the C content is more than 0.25%, there is a decrease in weldability. Therefore, the C content is set to be 0.05% or more and 0.25% or less.

(6) Si: 0.1% or more and 3.0% or less

(7) Since Si is an element which is useful for improving the mechanical properties of high-strength steel sheet, it is desirable that the Si content be 0.1% or more. However, in the case where the Si content is more than 3.0%, it is difficult to prevent the formation of oxide layer, which results in a decrease in coating adhesiveness. Therefore, the Si content is set to be 0.1% or more and 3.0% or less.

(8) Mn: 0.5% or more and 3.0% or less

(9) Since Mn is an element for solid solution hardening and is effective for increasing the strength of steel sheet, it is useful that the Mn content be 0.5% or more. On the other hand, in the case where the Mn content is more than 3.0%, there is a decrease in weldability and coating adhesiveness, and it is difficult to achieve a good balance between strength and ductility. Therefore, the Mn content is set to be 0.5% or more and 3.0% or less.

(10) P: 0.001% or more and 0.10% or less

(11) Since P delays the progress of phase transformation by delaying the precipitation of cementite, it is useful that the P content be 0.001% or more. On the other hand, in the case where the P content is more than 0.10%, there is a decrease in weldability and coating adhesiveness, and in addition, since alloying is delayed, it is desirable to increase an alloying temperature, which results in a decrease in ductility. Therefore, the P content is set to be 0.001% or more and 0.10% or less.

(12) Al: 0.01% or more and 3.00% or less

(13) Al and Si are elements which are added in a complementary manner. Since Al is inevitably mixed into steel in a refining process, the lower limit of the Al content is 0.01%. On the other hand, in the case where the Al content is more than 3.00%, it is difficult to prevent the formation of oxide layer, which results in a decrease in coating adhesiveness. Therefore, the Al content is set to be 0.01% or more and 3.00% or less.

(14) S: 0.200% or less

(15) S is an element which is inevitably added in a refining process. However, in the case where the S content is large, there is a decrease in weldability. Therefore, the S content is set to be 0.200% or less.

(16) In embodiments of the present invention, in addition to the elements described above, Mo and/or Cr may further be added.

(17) Mo: 0.01% or more and 1.00% or less

(18) Since Mo is an element which achieves the good balance between strength and ductility, Mo may be added in an amount of 0.01% or more. In addition, since Mo promotes, like Cr, the inner oxidation of Si and Al, Mo is effective for preventing the surface concentration of Si and Al. On the other hand, in the case where the Mo content is more than 1.00%, there may be an increase in cost. Therefore, in the case where Mo is added, it is preferable that the Mo content be 0.01% or more and 1.00% or less.

(19) Cr: 0.01% or more and 1.00% or less

(20) Since Cr is an element which achieves the good balance between strength and ductility, Cr may be added in an amount of 0.01% or more. In addition, since Cr promotes the inner oxidation of Si and Al, Cr is also effective for preventing the surface concentration of Si and Al. On the other hand, in the case where the Cr content is more than 1.00%, Cr is concentrated on the surface of steel sheet, which results in a decrease in coating adhesiveness and weldability. Therefore, in the case where Cr is added, it is preferable that the Cr content be 0.01% or more and 1.00% or less.

(21) In embodiments of the present invention, in addition to the elements described above, the following elements may be added in accordance with desired properties.

(22) Nb: 0.005% or more and 0.20% or less

(23) Since Nb is an element which achieves the good balance between strength and ductility, Nb may be added in an amount of 0.005% or more. On the other hand, in the case where the Nb content is more than 0.20%, there may be an increase in cost. Therefore, in the case where Nb is added, it is preferable that the Nb content be 0.005% or more and 0.20% or less.

(24) Ti: 0.005% or more and 0.20% or less

(25) Since Ti is an element which achieves the good balance between strength and ductility, Ti may be added in an amount of 0.005% or more. On the other hand, in the case where the Ti content is more than 0.20%, there may be a decrease in coating adhesiveness. Therefore, in the case where Ti is added, it is preferable that the Ti content be 0.005% or more and 0.20% or less.

(26) Cu: 0.01% or more and 0.50% or less

(27) Since Cu is an element which promotes the formation of residual phase, Cu may be added in an amount of 0.01% or more. On the other hand, in the case where the Cu content is more than 0.5%, there may be an increase in cost. Therefore, in the case where Cu is added, it is preferable that the Cu content be 0.01% or more and 0.50% or less.

(28) Ni: 0.01% or more and 1.00% or less

(29) Since Ni is an element which promotes the formation of residual phase, Ni may be added in an amount of 0.01% or more. On the other hand, in the case where the Ni content is more than 1.00%, there may be an increase in cost. Therefore, in the case where Ni is added, it is preferable that the Ni content be 0.01% or more and 1.00% or less.

(30) B: 0.0005% or more and 0.010% or less

(31) Since B is an element which promotes the formation of residual phase, B is added in an amount of 0.0005% or more. On the other hand, in the case where the B content is more than 0.010%, there may be a decrease in coating adhesiveness. Therefore, in the case where B is added, it is preferable that the B content be 0.0005% or more and 0.010% or less.

(32) The balance of the chemical composition other than the elements described above consists of Fe and inevitable impurities.

(33) Subsequently, the method for manufacturing a galvanized steel sheet according to aspects of the present invention will be described with reference to exemplary embodiments.

(34) A steel slab having the chemical composition described above is subjected to hot rolling followed by cold rolling and made into a steel sheet, and further, subjected to annealing and galvanizing using a continuous galvanizing line. In addition, an alloying treatment may be performed as needed after galvanizing. Here, at this time, one preferred aspect of the present invention is characterized in that the steel sheet is heated in the heating zone of an annealing furnace while a furnace temperature T in the heating zone of the annealing furnace is controlled based on the water vapor partial pressure P.sub.H2O.sup.in Air of air fed into the heating zone, subsequently heated to a temperature of 630 C. or higher and 850 C. or lower in an atmosphere containing hydrogen gas having a partial pressure P.sub.H2 of 1000 Pa or more and 50000 Pa or less, water vapor gas having a partial pressure P.sub.H2O of 610 Pa or less, and the balance being N.sub.2 and inevitable impurities, and subjected to galvanizing thereafter. This is an advantageous feature in embodiments of the present invention.

(35) Hot Rolling

(36) Hot rolling may be performed under commonly used conditions.

(37) Pickling

(38) It is preferable that pickling treatment be performed after hot rolling. After scale, which has been formed on the surface of steel sheet, is removed using a pickling process, cold rolling is performed. Here, there is no limitation on the pickling conditions.

(39) Cold Rolling

(40) It is preferable that cold rolling be performed at a reduction rate of 30% or more and 90% or less. In the case where the reduction rate is less than 30%, since recrystallization is delayed, there is a tendency for mechanical properties to deteriorate. On the other hand, in the case where the reduction rate is more than 90%, there is not only an increase in rolling cost but also a deterioration in coating performance due to an increase in surface concentration at annealing.

(41) Subsequently, the cold-rolled steel sheet is subjected to annealing and then to galvanizing. In embodiments of the present invention, by heating the steel sheet in the heating zone of an annealing furnace while controlling the furnace temperature T C. of the heating zone of the annealing furnace based on the water vapor partial pressure P.sub.H2O.sup.in Air of air fed into the furnace, since there is a decrease in variation in the amount of oxides formed on the surface of high-Si-containing steel sheet, it is possible to provide a method for manufacturing a galvanized steel sheet at a high product yield ratio.

(42) Heat Treatment Condition

(43) The heating which is performed using a combustion reaction in the heating zone of an annealing furnace is performed in order to form Fe-based oxides on the surface of steel sheet. Conventionally, it is known that the amount of oxides formed on the surface of steel sheet depends on the furnace temperature and the oxygen concentration in the heating zone of the annealing furnace. The present inventors found that the amount of oxides formed on the surface of steel sheet strongly depends on the amount of water vapor contained in air fed into the furnace in addition to the furnace temperature and the oxygen concentration. Specifically, in the case where the water vapor partial pressure P.sub.H2O.sup.in Air of air fed into the heating zone is 3000 Pa or less, an oxidation rate linearly increases with increasing water vapor partial pressure. This is thought to be because, in the case where P.sub.H2O.sup.in Air is 3000 Pa or less, there is an increase in defects in oxides due to the intrusion of water vapor into the oxides. On the other hand, it was found that, in the case where P.sub.H2O.sup.in Air is more than 3000 Pa, the oxidation rate hardly depends on the water vapor partial pressure and remains almost constant. This is thought to be because, in the case where P.sub.H2O.sup.in Air is more than 3000 Pa, since the intrusion of water vapor into the oxides is saturated, the defects do not increase further.

(44) On the basis of the findings described above, aspects of the present invention include that the surface of steel sheet is heated at a temperature of 600 C. or higher and 790 C. or lower while a furnace temperature T C. of the heating zone of the annealing furnace is controlled based on the water vapor partial pressure P.sub.H2O.sup.in Air of air fed into the heating zone of the annealing furnace. Here, the water vapor partial pressure of air fed into the furnace varies depending on the atmospheric temperature and humidity and the performance of a dehumidification and humidification device. It is preferable that P.sub.H2O.sup.in Air be 20000 Pa or less from the viewpoint of manufacturing costs and protection of the furnace inside.

(45) In embodiments of the present invention, it is preferable that the furnace temperature T C. in the heating zone of an annealing furnace be controlled to be within the following range:

(46) in the case where P.sub.H2O.sup.in Air3000 Pa; 690-0.03P.sub.H2O.sup.in AirT790-0.03P.sub.H2O.sup.in Air, and

(47) in the case where 3000 Pa<P.sub.H2O.sup.in Air20000 Pa; 600T700.

(48) In the case where P.sub.H2O.sup.in Air 3000 Pa, when T is lower than 690-0.03P.sub.H2O.sup.in Air since there is an insufficient oxidation amount, coating defects occur. In addition, when T is higher than 790-0.03P.sub.H2O.sup.in Air since there is an excessive oxidation amount, pressing flaws occur.

(49) In the case where 3000 Pa<P.sub.H2O.sup.in Air20000 Pa, if T is lower than 600 C., since there is an insufficient oxidation amount, coating defects occur. When T is higher than 700 C., since there is an excessive oxidation amount, pressing flaws occur.

(50) Here, it is possible to determine the water vapor partial pressure in the fed air using, for example, a mirror surface-type dew point meter or a capacitance-type dew point meter, and it is possible to decrease a variation in the oxidation amount formed on the surface of steel sheet by feedback controlling the furnace temperature within the ranges described above based on the determined water vapor partial pressure.

(51) Annealing conditions after heat treatment has been performed

(52) The annealing for a steel sheet after the heating is performed in order to perform a reduction treatment on the surface of steel sheet. In embodiments of the present invention, it is beneficial that the hydrogen partial pressure P.sub.H2 be 1000 Pa or more in order to obtain sufficient reduction capability. On the other hand, in the case where P.sub.H2 is more than 50000 Pa, there is an increase in operation cost. In addition, in the case where the water vapor partial pressure P.sub.H2O is more than 610 Pa, since oxides are less likely to be reduced, there is a decrease in coating performance. Therefore, after heating has been performed, annealing is performed in an atmosphere containing hydrogen gas having a partial pressure P.sub.H2 of 1000 Pa or more and 50000 Pa or less and water vapor gas having a partial pressure P.sub.H2O of 610 Pa or less, and the balance being N.sub.2 and inevitable impurities.

(53) In such an atmosphere, reduction annealing is performed by heating the steel sheet at a temperature of 630 C. or higher and 850 C. or lower. In the case where the temperature of the steel sheet is lower than 630 C., since recrystallization is delayed, there is a deterioration in mechanical properties. In the case where the temperature of the steel sheet is higher than 850 C., since surface concentration is promoted, coating defects occur.

(54) Galvanizing Treatment

(55) After annealing has been performed, galvanizing treatment is performed. In addition, after galvanizing treatment, alloying treatment may be performed as needed in order to manufacture a galvannealed steel sheet. It is preferable that the temperature of Zn bath be 440 C. or higher and 550 C. or lower when galvanizing treatment is performed. It is not appropriate that the bath temperature be lower than 440 C., because the solidification of Zn may occur due to a large variation in temperature inside the bath. On the other hand, in the case where the bath temperature is higher than 550 C., since the vaporization of the Zn bath becomes significant, there is an increase in operation cost or there is a deterioration in operation environment, and in addition, since alloying progresses at galvanizing, excessive alloying tends to occur.

(56) In the case where alloying treatment is not performed, it is preferable that Al concentration in the bath be 0.14 mass % or more and 0.24 mass % or less. In the case where the Al concentration is less than 0.14 mass %, FeZn alloying reaction progresses at galvanizing treatment, which results in a variation in surface appearance. On the other hand, in the case where the Al concentration is more than 0.24 mass %, since a thick FeAl alloy layer is formed at the interface of the coated layer and the base steel sheet at galvanizing treatment, there is a decrease in weldability, and in addition, since the Al concentration in the bath is high, a large amount of Al oxide layer attaches to the surface of steel sheet, there is a significant deterioration in surface appearance.

(57) In the case where alloying treatment is performed, it is preferable that the Al concentration in the bath be 0.10% or more and 0.20% or less. In the case where the Al concentration is less than 0.10%, since a hard and brittle FeZn alloy layer is formed at the interface of the coated layer and the base steel sheet at galvanizing treatment, there is a decrease in coating adhesiveness. On the other hand, in the case where the Al concentration is more than 0.20%, since a thick FeAl alloy layer is formed at the interface of the coated layer and the base steel sheet immediately after the dipping in the bath, there is a decrease in weldability.

(58) In addition, Mg may be added to the Zn bath in order to increase corrosion resistance.

(59) Subsequently, an alloying treatment is performed as needed. It is appropriate that the alloying temperature be 460 C. or higher and 570 C. or lower. In the case where the alloying temperature is lower than 460 C., alloying reaction is slow, while, in the case where the alloying temperature is higher than 570 C., since a hard and brittle thick FeZn alloy layer is formed at the interface of the coated layer and the base steel sheet, there is a decrease in coating performance. Coating weight is not specified in particular. It is preferable that the coating weight be 10 g/m.sup.2 or more from the viewpoint of corrosion resistance and coating weight control, and it is preferable that coating weight be 120 g/m.sup.2 or less from the viewpoint of formability and economic efficiency.

EXAMPLE 1

(60) Aspects of the present invention will be described based on examples hereafter.

(61) Slabs having chemical compositions given in Table 1 were heated at a temperature of 1260 C. for 60 minutes in a heating furnace, hot-rolled into a thickness of 2.8 mm, and then coiled at a temperature of 540 C. Subsequently, after scale had been removed by pickling, the coiled steel sheets were cold-rolled into a thickness of 1.6 mm. Then, a heat treatment was performed under the conditions given in Table 2 using a DFF-type CGL having divided heating zones. After heat treatment, the steel sheets were dipped in an Al-containing Zn bath having a temperature of 460 C. in order to obtain galvanized steel sheets (GI), and then the galvanized steel sheets were subjected to alloying treatment in order to obtain galvannealed steel sheets (GA). Here, the Al concentration in the bath was 0.10% to 0.20%, and the coating weight was controlled to be 45 g/m.sup.2 by using a gas wiping method. The alloying treatment was performed at a temperature of 550 C. to 560 C.

(62) TABLE-US-00001 TABLE 1 Chemical Composition/mass % Steel C Si Mn P Al S Mo Cr Nb Ti Cu Ni B Note A 0.10 1.0 1.0 0.01 0.03 0.003 within Scope of Invention B 0.08 1.4 1.2 0.05 0.03 0.003 within Scope of Invention C 0.15 1.5 2.5 0.01 0.03 0.008 0.02 within Scope of Invention D 0.12 1.1 0.5 0.05 0.60 0.008 0.05 within Scope of Invention E 0.12 3.0 0.7 0.05 1.00 0.008 0.07 0.03 within Scope of Invention F 0.09 0.5 0.4 0.03 0.50 0.002 0.10 0.01 0.05 within Scope of Invention G 0.06 0.1 1.0 0.05 0.80 0.010 0.30 0.04 0.02 within Scope of Invention H 0.13 0.2 1.5 0.01 0.05 0.003 0.02 0.08 0.03 0.20 within Scope of Invention I 0.18 0.5 0.6 0.08 0.20 0.023 0.06 0.06 0.10 0.01 0.50 within Scope of Invention J 0.07 0.8 2.2 0.02 0.08 0.001 0.15 0.20 0.10 0.001 within Scope of Invention K 0.10 0.8 1.0 0.04 0.40 0.015 0.25 0.50 0.01 0.15 0.05 0.02 0.001 within Scope of Invention L 0.30 3.5 0.8 0.06 0.30 0.026 0.50 0.02 out of Scope of Invention M 0.13 0.4 3.2 0.15 0.10 0.001 0.02 0.05 0.25 out of Scope of Invention N 0.50 0.6 0.7 0.08 3.50 0.300 0.05 0.08 0.07 0.02 out of Scope of Invention O 0.15 4.0 2.5 0.02 0.08 0.001 1.20 0.45 0.12 0.001 out of Scope of invention P 0.35 0.8 3.5 0.04 0.40 0.015 0.35 1.50 0.04 0.07 0.05 0.02 0.001 out of Scope of Invention

(63) The surface appearance and coating adhesiveness of the steel sheets obtained as described above were evaluated using the following methods.

(64) (1) Surface Appearance

(65) Surface appearance was evaluated based on the following, standard by performing a visual test on a region of 300300 mm of the steel sheet surface.

(66) : without coating defects nor pressing flaws

(67) : generally satisfactory, but with coating defects at low frequency

(68) .box-tangle-solidup.: generally satisfactory, but with pressing flaws at low frequency

(69) x: poor surface appearance with coating defects or pressing flaws

(70) (2) Coating Adhesiveness

(71) By sticking a cellophane tape to the steel sheet surface, and performing bending and unbending at a right angle on the steel sheet, the amount per unit length of Zn peeled was determined in terms of Zn count number using a fluorescent X-ray method. Then, coating adhesiveness was evaluated based on the following standard. Here, in this test, the mask diameter was 30 mm, the acceleration voltage of the fluorescent X-ray was 50 kV, the acceleration current of the fluorescent X-ray was 50 mA, and the measuring time was 20 seconds.

(72) : Zn count number was 0 to 5000

(73) : Zn count number was 5000 to 10000

(74) x: Zn count number was 10000 or more

(75) The obtained results are given in Table 2.

(76) TABLE-US-00002 TABLE 2 Annealing Condition Heat Treatment Condition after Heat Treatment Steel Temperature of Furnace Temperature of Surface Coating Sheet Steel Sheet Temperature T Steel Sheet Kind of Appear- Adhesive- No. Steel P.sub.H20.sup.in Air/Pa Surface/ C. of Invention/ C. P.sub.H2/Pa P.sub.H20/Pa Surface/ C. Coating ance ness Note 1 A 100 715 687-787 10000 80 820 GA Example 2 A 100 770 687-787 10000 610 820 GI Example 3 A 100 650 687-787 10000 30 820 GA Comparative Example 4 A 100 835 687-787 10000 20 820 GA x x Comparative Example 5 A 1000 750 660-760 10000 30 820 GA Example 6 A 1000 695 660-760 10000 200 820 GI Example 7 A 1000 815 660-760 10000 35 820 GI .box-tangle-solidup. x Comparative Example 8 A 1000 620 660-760 10000 150 820 GI Comparative Example 9 A 1000 580 660-760 10000 40 820 GA x x Comparative Example 10 A 2500 705 615-715 10000 20 820 GA Example 11 A 2500 650 615-715 10000 60 820 GA Example 12 A 2500 680 615-715 10000 20 820 GI Example 13 A 2500 750 615-715 10000 20 820 GA .box-tangle-solidup. Comparative Example 14 A 2500 780 615-715 10000 250 820 GA .box-tangle-solidup. x Comparative Example 15 A 2500 595 615-715 10000 40 820 GA Comparative Example 16 A 5000 610 600-700 10000 50 820 GA Example 17 A 5000 650 600-700 10000 300 820 GI Example 18 A 5000 550 600-700 10000 20 820 GA x Comparative Example 19 A 5000 750 600-700 10000 20 820 GA x x Comparative Example 20 A 10000 675 600-700 10000 15 820 GA Example 21 A 10000 620 600-700 10000 400 820 GA Example 22 A 10000 720 600-700 10000 15 820 GA .box-tangle-solidup. x Comparative Example 23 A 10000 570 600-700 10000 40 820 GA x Comparative Example 24 A 10000 735 600-700 10000 40 820 GI x x Comparative Example 25 B 100 720 687-787 10000 30 820 GA Example 26 B 100 650 687-787 10000 35 820 GA x x Comparative Example 27 C 1000 700 660-760 10000 25 820 GI Example 28 D 1000 710 660-760 10000 30 820 GA Example 29 E 2500 725 615-715 10000 50 820 GA .box-tangle-solidup. x Comparative Example 30 F 1000 680 660-760 10000 30 810 GA Example 31 G 1000 720 660-760 10000 15 810 GA Example 32 H 2000 700 630-730 10000 20 810 GI Example 33 I 2000 675 630-730 10000 120 810 GA Example 34 J 3000 680 600-700 10000 20 810 GI Example 35 K 3000 670 600-700 10000 140 810 GA Example 36 L 100 690 687-787 10000 20 810 GA x Comparative Example 37 M 1000 750 660-760 10000 150 820 GA Comparative Example 38 N 1000 665 660-760 10000 50 810 GI x x Comparative Example 39 O 2500 620 615-715 10000 80 810 GA x Comparative Example 40 P 2500 710 615-715 10000 100 810 GI x Comparative Example

(77) From the results given in Table 2, it is clarified that the surfaces of all the galvanized steel sheets according to embodiments of the present invention (examples in Table 2) have good surface appearance and excellent coating adhesiveness. That is, there is a significant increase in product yield ratio compared with conventional examples.

(78) FIG. 1 is a correlation diagram illustrating the relationship between the manufacturing conditions (the furnace temperature T and the water vapor partial pressure P.sub.H2O.sup.in Air of air fed into the furnace) and the evaluation results of surface appearance in the case of steel A given in Table 2. As FIG. 1 indicates, it is clarified that all the galvanized steel sheets according to aspects of the present invention have good surface appearance.

(79) In addition, the comparative examples of conventional techniques are also illustrated in FIG. 1. For example, in the case where the furnace temperature in the heating zone is controlled to be 750 C. (comparative example 1 of conventional technique), the satisfactory surface appearance can be obtained when P.sub.H2O.sup.in Air is 100 Pa or 1000 Pa. However, when P.sub.H2O.sup.in Air is 2500 Pa or 5000 Pa, pressing flaws occur. In the same way, in the case where the furnace temperature is controlled to be 650 C. (comparative example 2 of conventional technique), coating defects occur when P.sub.H2O.sup.in Air is 100 Pa. That is, in the case of the conventional technique, although unsatisfactory surface appearance occurs when the furnace temperature is simply controlled to be constant (, .box-tangle-solidup., and x on the dotted lines for comparative examples 1 and 2 of conventional technique), it is clarified that unsatisfactory surface appearance does not occur when water vapor partial pressure is controlled as is the case with embodiments of the present invention ( on the dotted lines for comparative examples 1 and 2 of conventional technique).

(80) As described above, according to aspects of the present invention, a galvanized steel sheet having good surface appearance and excellent coating adhesiveness is stably manufactured. That is, there is a significant increase in product yield ratio compared with the conventional manufacturing methods.

(81) Since the galvanized steel sheet according to aspects of the present invention is excellent in terms of surface appearance and coating adhesiveness as well as mechanical properties, it is expected that the galvanized steel sheet is used for wide applications mainly including the fields of automobile, domestic electric appliance, and building material.