Hot dip plated steel sheet having excellent corrosion resistance and workability

Abstract

Provided is a plated steel sheet applicable for various purposes as in construction materials, household electric appliances, automobiles, etc. and, more particularly, to a hot dip plated steel sheet having excellent corrosion resistance and workability and a manufacturing method therefor.

Claims

1. A hot-dip galvanized steel sheet having excellent corrosion resistance and workability, comprising: a base steel sheet; and a Zn—Al—Mg-based alloy plating layer formed on at least one surface of the base steel sheet, wherein the Zn—Al—Mg-based alloy plating layer comprises, by wt %, 20 to 30% of aluminum (Al), 3 to 5% of magnesium (Mg), and a balance of Zn and other inevitable impurities, and wherein the Zn—Al—Mg-based alloy plating layer comprises: a surface layer structure comprised of a Zn phase, a Zn—Al phase, a MgZn.sub.2 phase, and a Zn—Al—MgZn.sub.2 phase; and an internal structure formed between the surface layer structure and the base steel sheet, the internal structure comprising: an Fe—Al alloy phase, and wherein the surface layer structure of the Zn—Al—Mg-based alloy plating layer is a region from a surface of the Zn—Al—Mg-based alloy plating layer to ⅓t to ½t in a thickness direction where t is a thickness of the Zn—Al—Mg-based alloy plating layer.

2. The hot-dip galvanized steel sheet having excellent corrosion resistance and workability of claim 1, wherein, in the Zn—Al—Mg-based alloy plating layer, a sum of the aluminum (Al) and the magnesium (Mg) comprises 25% or more by wt %.

3. The hot-dip galvanized steel sheet having excellent corrosion resistance and workability of claim 1, wherein the Zn—Al—Mg-based alloy plating layer has a thickness of 3 to 40 μm.

Description

DESCRIPTION OF DRAWINGS

(1) FIG. 1 is a photograph illustrating an appearance of a plated steel sheet according to an embodiment of the present disclosure.

(2) FIG. 2 is a photograph of a cross-section of an alloy plating layer of the plated steel sheets of FIG. 1 observed by SEM.

(3) FIG. 3 is a photograph of a structure in the alloy plating layer of Comparative Example 1 (left) and Inventive Example 2 (right) according to an embodiment of the present disclosure observed by SEM.

BEST MODE FOR INVENTION

(4) In order to obtain a Zn—Al—Mg-based alloy plated steel sheet, when a Zn—Al—Mg alloy is plated, an initiation of solidification of the alloy plating layer is determined by the content of aluminum and magnesium, and at the end of solidification, as an eutectic phase finally containing Zn—Al—Mg is solidified, a solidification reaction of the plating layer is terminated. However, until the solidification of a Zn—Al—Mg ternary eutectic structure is terminated, flow patterning surface defects due to the strong oxidation of Mg are likely to occur, so there are restrictions on the use of Mg.

(5) Nevertheless, in order to improve the corrosion resistance of Zn—Al—Mg alloy plated steel sheet, it is necessary to add Mg in a certain content or more, and as the content of Mg increases, a problem in which flow pattern defects due to oxidation increase may be confirmed. The present inventors have studied in depth a method to ensure good surface quality while securing corrosion resistance by a certain amount of Mg.

(6) Specifically, in the case of Zn—Al—Mg-based alloy plating, it was confirmed that an erosion property was strong in the plating bath and the solidification zone was wide, and a structure of the alloy plating layer may be controlled by optimizing a cooling process as well as the alloy composition of the Zn—Al—Mg alloy plating system.

(7) As a result, it was confirmed that it was possible to provide a Zn—Al—Mg-based alloy plated steel sheet having excellent workability with good surface qualities as well as excellent corrosion resistance, thereby resulting in completion of the present disclosure.

(8) Hereinafter, the present disclosure will be described in detail.

(9) According to an aspect of the present disclosure, a hot-dip galvanized steel sheet may include: a base steel sheet; and a Zn—Al—Mg-based alloy plating layer on at least one surface of the base steel sheet, wherein the Zn—Al—Mg-based alloy plating layer may include, by wt %, 20 to 30% of aluminum (Al), 3 to 5% of magnesium (Mg), a balance of Zn and other inevitable impurities.

(10) The Zn—Al—Mg-based alloy plating layer may be formed from an alloy plating bath containing Al, Mg, and Zn having the alloy composition as described above.

(11) Specifically, Al in the alloy plating bath is a major element in securing high corrosion resistance of the hot-dip galvanized steel sheet, and if the content thereof is less than 20%, it is difficult to secure sufficient corrosion resistance of the Zn—Al—Mg-based alloy plating layer. On the other hand, if the content thereof exceeds 30%, dross generation in the plating bath increases, resulting in poor surface quality of a final product.

(12) Mg in the alloy plating bath is an element added to improve the corrosion resistance of the alloy plating layer and a cutting surface of the plating layer, and if the content thereof is less than 3%, the effect of improving corrosion resistance is insignificant, whereas if the content thereof exceeds 5%, there may be a problem that dross generation due to oxidation of the plating bath greatly increases.

(13) Both Al and Mg are elements improving the corrosion resistance of the plating layer, and as a sum of these elements increases, the corrosion resistance may be further improved, and thus the sum of the contents of Al and Mg may be limited to 25% or more in the present disclosure.

(14) Meanwhile, the composition in the alloy plating bath is substantially the same as the composition in the alloy plating layer.

(15) The Zn—Al—Mg-based alloy plating layer having the above-described alloy composition may have a fine and uniform structure, and specifically, it is preferable that a surface layer structure of the Zn—Al—Mg-based alloy plating layer is comprised of a Zn phase, a Zn—Al phase, a MgZn.sub.2 phase, and a Zn—Al—MgZn.sub.2 phase, and an internal structure includes an Fe—Al alloy phase.

(16) In the present disclosure, as a plating structure of the Zn—Al—Mg-based alloy plating layer, a fine Zn—Al phase, a MgZn.sub.2 phase, and a Zn—Al—MgZn.sub.2 phase may be formed on the surface (surface layer) of the alloy plating layer, thereby improving corrosion resistance.

(17) In addition, in the present disclosure, an Fe—Al intermetallic compound (Fe—Al alloy phase) formed at an interface of the existing Zn—Al—Mg-based alloy plated steel sheet (interface between the base steel sheet and the plating layer) may be uniformly generated inside the alloy plating layer (internal structure), such that there is an effect of ensuring a surface appearance satisfactory.

(18) Meanwhile, the Zn—Al—Mg-based alloy plating layer may have a thickness of 3 to 40 μm, and a surface structure within the Zn—Al—Mg-based alloy plating layer may correspond to a region from the surface of the alloy plating layer to ⅓t to ½t in a thickness direction (where t is the thickness (μm) of the alloy plating layer). The remainder, except for the surface structure corresponding to the above-described area may be referred to as an internal structure.

(19) In the hot-dip galvanized steel sheet of the present disclosure, the surface structure and the internal structure of the Zn—Al—Mg-based alloy plating layer may be formed differently, and in this case, as the surface structure is formed as described above, the hot dip galvanized steel sheet has advantages of having superior corrosion resistance, and having an attractive surface appearance, as compared to the existing hot-dip galvanized steel sheet.

(20) Hereinafter, a method of manufacturing a hot-dip galvanized steel sheet having excellent corrosion resistance and workability, another aspect of the present disclosure, will be described in detail.

(21) A method of manufacturing a hot-dip galvanized steel sheet having excellent corrosion resistance and workability may include operations of: preparing an alloy plating bath having the above-described alloy composition; immersing a base steel sheet in the alloy plating bath, and preparing a plated steel sheet by performing plating; and cooling the plated steel sheet.

(22) In performing plating by immersing the base steel sheet in an alloy plating bath satisfying the alloy composition proposed in the present disclosure, it is preferable to adjust a plating bath immersing temperature to 500 to 550° C., and a plating bath temperature to 480 to 550° C. to pass through a plating bath.

(23) If the immersing temperature of the plating bath is less than 500° C., non-plated portions may occur on the surface of the formed alloy plating layer or adhesion of the plating layer is deteriorated, whereas if it exceeds 550° C., there is a problem that the adhesion of the plating layer is deteriorated.

(24) It is preferable to cool the plated steel sheet obtained by plating according to the above, and the cooling is preferably performed to 300° C. or lower at a cooling rate of 8 to 30° C./s.

(25) When the cooling rate is less than 8° C./s, the plating layer cannot be uniformly solidified. On the other hand, when the cooling rate exceeds 30° C./s, there is a problem that flow streak defects may occur on the surface of the plating layer.

(26) In addition, the cooling may be performed in a gas atmosphere comprised of 4 vol % or less (including 0%) of hydrogen (H.sub.2) and residual nitrogen (N.sub.2), and may be performed using, for example, an air get cooler.

(27) By controlling the cooling process as described above, an primary Zn phase and a Zn—Al phase are first may be generated on a surface of the alloy plating layer, and a fine Zn—Al phase, and MgZn.sub.2 phase and Zn—Al—MgZn.sub.2 phase can be formed in a region below the surface (meaning a region between the surface and an internal alloy layer (internal structure)).

(28) Finally, by generating a uniform structure on a surface layer of the alloy plating layer, the corrosion resistance of a plane portion may be greatly improved, and in particular, it is possible to obtain an effect of improving sacrificial corrosion resistance of a cross-sectional portion by the Zn phase and the MgZn.sub.2 phase.

(29) Prior to cooling the plated steel sheet, an operation of gas wiping treatment may further be included, and an amount of plating adhesion may be adjusted from the gas wiping treatment.

(30) As the gas used in the gas wiping treatment, air or nitrogen may be used, of which nitrogen is more preferably used. This is because, when air is used, Mg oxidation preferentially occurs on the surface of the plating layer, thereby causing surface defects of the plating layer.

(31) Meanwhile, the base steel sheet may be a cold-rolled material such as general carbon steel (including low carbon steel), stainless steel, and the like, and is not particularly limited thereto.

(32) The cold-rolled material may be subjected to a degreasing process for cleaning rolling oil on the surface of the rolled steel sheet, and then an annealing heat treatment to recover a rolled structure and secure a material.

(33) The annealing heat treatment may be performed in a temperature range of 700 to 850° C., but generally, an annealing heat treatment may be performed in a temperature range of 700 to 800° C. for low carbon steel, and an annealing heat treatment may be performed in a temperature range of 800 to 850° C. for ultra-low carbon steel or high strength steel.

(34) The cold-rolled material may have a thickness of 0.3 to 1 mm, but is not limited thereto.

(35) Hereinafter, the present disclosure will be described in more detail through examples. However, it is necessary to note that the following examples are only intended to illustrate the present disclosure in more detail and are not intended to limit the scope of the present disclosure. This is because the scope of the present disclosure is determined by matters described in the claims and able to be reasonably inferred therefrom.

MODE FOR INVENTION

Embodiment 1

(36) A cold-rolled low-carbon steel (0.003% C-0.15% Mn-a balance of Fe and other unavoidable impurities) specimen (a thickness of 0.7 mm) was degreased and then subjected to an annealing heat treatment at 780° C. During the annealing heat treatment, a gas atmosphere in a furnace was controlled to 4 to 20% of the H.sub.2-balance of N.sub.2 as a reducing gas atmosphere, and a dew point temperature was −40° C. or lower.

(37) Thereafter, alloy melting plating was performed on the specimen under the conditions shown in Table 1 below. In this case, an alloy plating bath (0.027% of Fe) having a composition of 22.77% of Al, 3.6% of Mg, and a balance of Zn by weight % was used.

(38) TABLE-US-00001 TABLE 1 Immersing Immersing Plating bath Gas for Cooling Thickness of temperature time temperature cooling rate alloy plating Specimens (° C.) (sec.) (° C.) (l/min) (° C./s) layer (μm) Classifications 1 520 5 510 200/200 4.4 4.4 CE 1 2 520 5 510 400/400 6.2 6.0 CE 2 3 520 5 510 600/600 6.9 5.9 CE 3 4 520 5 510 700/700 8.1 6.0 IE 1 5 520 5 510 700/700 8.3 5.9 IE 2 6 540 5 530 200/200 4.3 4.5 CE 4 7 540 5 530 400/400 6.0 6.6 CE 5 8 540 5 530 600/600 6.8 5.2 CE 6 9 540 5 530 700/700 8.2 5.0 CE 7 10 540 5 530 700/700 8.1 6.6 CE 8 11 560 5 550 200/200 4.5 5.7 CE 9 12 560 5 550 400/400 6.1 5.5 CE 10 13 560 5 550 600/600 6.8 5.7 CE 11 14 560 5 550 700/700 8.0 5.4 CE 12 15 560 5 550 700/700 8.2 5.7 CE 13 *IE: Inventive example/CE: Comparative example

(39) As described above, results of observing a plating appearance for each plated steel sheet on which plating has been completed were shown in FIG. 1, and an image of a cross-section of an alloy plating layer observed by SEM is shown in FIG. 2.

(40) As shown in FIG. 2, it can be confirmed that a surface layer structure and an internal structure are separated and formed uniformly only in specimens 4 and 5 corresponding to Inventive Examples 1 and 2. In particular, it can be seen that an alloy phase is uniformly formed inside the plating layer.

(41) On the other hand, it can be seen that specimens of Comparative Examples 1 to 13 are formed by mixing an Fe—Al alloy phase with a Zn phase and a Zn—Al phase.

(42) In addition, FIG. 3 is a photograph of the structure of the alloy plating layer of Comparative Example 1 and Inventive Example 2 observed by SEM.

(43) As shown in FIG. 3, it can be seen that, in the case of Comparative Example 1, an alloy plating layer having the plating structure intended in the present disclosure is not uniformly formed on a surface of the plated steel sheet, whereas in Inventive Example 2, an Fe—Al alloy layer is formed inside the alloy plating layer, and a plating structure is formed uniformly above the alloy layer.

Embodiment 2

(44) The same specimen as in Example 1, that is, a cold-rolled carbon steel specimen (thickness of 0.7 mm) was degreased and then subjected to an annealing heat treatment at 750° C. During the annealing heat treatment, the gas atmosphere in the furnace was controlled to 4 to 20% of H.sub.2-balance of N.sub.2 as a reducing gas atmosphere, and a dew point temperature was −40° C. or lower.

(45) Thereafter, alloy hot-dip galvanizing was performed on the specimen under each condition shown in Table 2 below.

(46) TABLE-US-00002 TABLE 2 Composition of plating bath (balance of Immersing Immersing Plating bath Gas for Cooling Zn, %) temperature time temperature cooling rate Specimens Al Mg (° C.) (Sec.) (° C.) (l/min) (° C./s) Classifications 1 23 3.6 520 5 510 200/200 4.4 CE A 2 23 3.6 520 5 510 700/700 8.3 IE A *CE: Comparative example/*IE: Inventive example

(47) In order to evaluate corrosion resistance of a plated steel sheet, in which plating has been completed according to each condition, after performing a corrosion promotion test with a salt spray test (salt spray standard test in accordance with KS-C-0223), an elapsed time was measured until a red rust generation area on a surface of the plating layer became 5%.

(48) In addition, in order to evaluate plating adhesion, a 180-degree bending test was performed, and then a bending surface was visually observed to confirm occurrence of cracks.

(49) Each result was shown in Table 3 below. As shown in Table 3 below, it can be seen that Inventive Example A has superior corrosion resistance, compared to Comparative Example A, and no non-plated portion phenomenon is observed. In particular, bending adhesion of Inventive Example A was at the same level as that of a hot-dip galvanized material.

(50) TABLE-US-00003 TABLE 3 Crack occurrence of Classifications Salt spray test bending surface Comparative Red rust x Example A generation after 7 to 8 weeks Inventive Red rust x Example A generation after 11 to 12 weeks