Patent Application
20250003029
The present disclosure relates to a high-corrosion resistance plated steel sheet having excellent corrosion resistance and surface appearance and a method for manufacturing the same.
When a galvanized steel sheet is exposed to a corrosive environment, a galvanized steel sheet may have sacrificial properties in which zinc, having a lower redox potential than that of iron, is corroded first, such that corrosion of a steel material may be prevented. Also, as zinc in a plating layer oxidizes, dense corrosion products may be formed on the surface of a steel material, thereby blocking the steel material from the oxidizing atmosphere and improving corrosion resistance of the steel material. Due to the advantageous properties, the application of a galvanized steel sheet has been increased to include steel sheets for construction materials, home appliances, and automobiles.
However, the corrosion environment has gradually deteriorated due to an increase in air pollution due to industrial advancement, and due to strict regulations on resource and energy conservation, the need for the development of a steel material having improved corrosion resistance than a conventional galvanized steel material has been increased.
To address this issue, various studies have been conducted on the technique of manufacturing a galvanized alloy plated steel sheet, which may improve corrosion resistance of a steel material by adding elements such as aluminum (Al) and magnesium (Mg) to a galvanizing bath. As a representative example, a Zn-Mg-Al galvanized alloy steel sheet in which Mg is further added to a Zn-Al plating composition system has been used.
However, a Zn-Mg-Al based galvanized alloy plated steel sheet may be often processed, but a plating layer surface may be uneven and roughness may be high, such that image clarity may be poor after painting.
Also, spangle may be easily formed on a Zn-Mg-Al based zinc alloy plated steel sheet during slow cooling, such that surface appearance may be unattractive.
Accordingly, a level of technology which may satisfy the demand for high-end material having excellent corrosion resistance and also excellent image clarity after painting and surface appearance has not been developed.
(Cited document 1) Korean Laid-Open Patent Publication No. 2010-0073819
An aspect of the present disclosure is to provide a plated steel sheet having excellent corrosion resistance and surface appearance and a method for manufacturing the same.
Also, another aspect of the present disclosure is to provide a plated steel sheet having excellent corrosion resistance, image clarity after painting and surface appearance and a method for manufacturing the same. The purpose of present disclosure is not limited to
the above aspects. Anyone having ordinary knowledge in the technical field to which the present disclosure belongs may have no difficulty in understanding the additional purpose of the invention from the overall description of the present disclosure.
An aspect of the present disclosure provides a plated steel sheet comprising
(In the Relational expression 1, I(110) is X-ray diffraction integrated intensity of a (110) plane crystal peak of a MgZn2 phase, and I(103) is X-ray diffraction integrated intensity of a (103) plane crystal peak of a MgZn2 phase.)
Another aspect of the present disclosure provides a method for manufacturing a plated steel sheet comprising
(In the Relational expression 2, Wair is a spacing between air-knives, and a unit is mm. Pair is pressure of the air-knife, and a unit thereof is kPa. T is a temperature of the supplied inert gas, and a unit thereof is ° C. To is an average temperature of atmosphere and is determined as 25° C.)
According to an aspect of the present disclosure, a plated steel sheet having excellent corrosion resistance and surface appearance and a method for manufacturing the same may be provided.
Also, according to another aspect of the present disclosure, a plated steel sheet having excellent corrosion resistance, surface appearance and image clarity after painting and a method for manufacturing the same may be provided.
The various and beneficial advantages and effects of the present disclosure are not limited to the above, and will be more easily understood in the course of describing specific embodiments of the present disclosure.
The terms used in this specification are intended to describe specific embodiments and are not intended to limit the present disclosure. Also, an expression used in the singular encompasses the expression of the plural, unless it has a clearly different meaning in the context.
The term “comprise” used in the specification specifies components and does not exclude the presence or addition of other components.
Unless otherwise defined, the entirety of terms, including technical and scientific terms, used in this specification may refer to the same as those generally understood by those skilled in the art in the technical field to which the present disclosure belongs. Terms defined in the dictionary are interpreted to have meanings consistent with related technical document and current disclosure.
Hereinafter, [plated steel sheet] according to an aspect of the present disclosure will be described in detail. When indicating the content of each element in the present disclosure, unless specifically defined otherwise, the content may be indicated in weight %.
In a conventional Zn-Mg-Al-based galvanized alloy steel sheet related technology, Mg may be added to improve corrosion resistance. However, when excessive Mg is added, floating dross may increase in a plating bath, such that the dross may need to be removed frequently, which may be problematic, and an upper limit of Mg content may be limited to 3%.
Accordingly, research has been conducted to further improve corrosion resistance by increasing a Mg content from 3%, but as more Mg and Al are added, due to unevenness between phases, roughness may be high and image clarity after painting may not be assured.
In addition to the image clarity after painting problem, crystal growth of Zn-Mg-Al based galvanized alloy plated steel sheet may be accelerated during slow cooling during a manufacturing process, and surface appearance may not be attractive due to spangle, such that there may be a limitation in application to home appliances and automobiles.
Accordingly, in the prior art, it has been technically difficult to provide a plated steel sheet having assured corrosion resistance and also having excellent image clarity after painting and surface appearance.
Accordingly, the present inventors conducted intensive studies to solve the above-mentioned problems and to provide a plated steel sheet having excellent corrosion resistance and also excellent image clarity after painting and/or surface appearance, and founded that, in addition to a composition of the plating layer, a ratio between an X-ray diffraction integrated intensity of a (110) plane crystal peak of a MgZn2 phase obtained through XRD analysis on the surface of the plating layer and X-ray diffraction integrated intensity of (103) plane crystal of a MgZn2 phase may be an important factor, and completed the present disclosure.
Hereinafter, the configuration of a plated steel sheet having excellent corrosion resistance and also excellent image clarity after painting and/or surface appearance will be described in detail.
First, the plated steel sheet according to the present disclosure may comprise a base steel sheet; and a Zn-Mg-Al-based plating layer provided on at least one surface of the base steel sheet.
In the present disclosure, the type of base steel sheet may not be particularly limited. For example, the base steel sheet may be implemented as an Fe-based base steel sheet used as a base steel sheet of general galvanized steel sheet, that is, a hot-rolled steel sheet or a cold-rolled steel sheet, but an embodiment thereof is not limited thereto. Alternatively, the base steel sheet may be, for example, carbon steel, ultra-low carbon steel, or high manganese steel used as a material for construction, home appliances, and automobiles.
However, as an example, the base steel sheet may have a composition of, in weight %, C: more than 0% (more preferably, 0.001% or more) and 0.18% or less, Si: more than 0% (more preferably, 0.001% or more) and 1.5% or less, Mn: 0.01 to 2.7%, P: more than 0% (more preferably, 0.001% or more) and 0.07% or less, S: more than 0% (more preferably, 0.001% or more) and 0.015% or less, Al: more than 0% (more preferably, 0.001% or more) and 0.5% or less, Nb: more than 0% (more preferably, 0.001% or more) and 0.06% or less, Cr: more than 0% (more preferably, 0.001% or more) and 1.1% or less, Ti: more than 0% (more preferably, 0.001% or more) and 0.06% or less, B: more than 0% (more preferably, 0.001% or more) and 0.03% or less and a balance of Fe and inevitable impurities.
Although not particularly limited, according to an embodiment of the present disclosure, at least one surface of the base steel sheet may be provided with a Zn-Mg-Al-based plating layer consisted of a Zn-Mg-Al-based alloy. The plating layer may be formed on only one surface of the base steel sheet, or may be formed on both surfaces of the base steel sheet. In this case, the Zn-Mg-Al-based plating layer may refer to a plating layer comprising Mg and Al and mainly comprising Zn (comprising more than 50% of Zn).
Although not particularly limited, according to an embodiment of the present disclosure, a thickness of the Zn-Mg-Al-based plating layer may be 5 to 100 μm, more preferably 7 to 90 μm. When the thickness of the plating layer is less than 5 μm, the thickness of the plating layer may excessively decrease locally due to errors resulting from the thickness deviation of the plating layer, such that corrosion resistance may deteriorate. When the thickness of the plating layer exceeds 100 μm, cooling of the hot-dip plating layer may be delayed, a solidification defect such as a flow pattern, for example, may occur on the surface of the plating layer, and productivity of the steel sheet may decrease to solidify the plating layer.
Meanwhile, according to an embodiment of the present disclosure, although not particularly limited, an Fe-Al-based inhibition layer may be further comprised between the base steel sheet and the Zn-Mg-Al-based plating layer. The Fe-Al-based inhibition layer may mainly comprise an intermetallic compound of Fe and Al (e.g., more than 60%), and examples of the intermetallic compound of Fe and Al may comprise FeAl, FeAl3, and Fe2Al5. Also, some components derived from the plating layer, such as Zn and Mg, may be further comprised, for example, up to 40%. The inhibition layer may be formed due to alloying by Fe and plating bath components diffused from the base steel sheet at an initial stage of plating. The inhibition layer may improve adhesion between the base steel sheet and the plating layer, and may also prevent Fe diffusion from the base steel sheet to the plating layer. The inhibition layer may be formed continuously between the base steel sheet and the Zn-Mg-Al-based plating layer, or may be formed discontinuously. In this case, other than the above-mentioned description, regarding the inhibition layer, a commonly known description in the relevant technical field may be applied.
Although not particularly limited, according to an embodiment of the present disclosure, a thickness of the inhibition layer may be 0.1 to 1 μm. The inhibition layer may assure corrosion resistance by preventing alloying, but as the layer is brittle, the layer may affect processability, and accordingly, a thickness thereof may be determined to be 1 μm or less. However, to function as a inhibition layer, the thickness may be 0.1 μm or more. In terms of further improving the above-mentioned effect, preferably, an upper limit of the thickness of the inhibition layer may be 1.00 μm, or a lower limit of the inhibition layer thickness may be 0.15 μm.
In this case, the thickness of the inhibition layer may refer to a minimum thickness in the thickness direction with respect to the inhibition layer, obtained by manufacturing a cross-sectional sample cut from a plated steel sheet in the thickness direction (i.e., the direction perpendicular to the rolling direction) and imaging the cross-section using a scanning electron microscope (hereinafter referred to as ‘SEM’).
Also, according to the present disclosure, the plating layer may comprise, by weight %, Mg: 4.0 to 6.3%, Al: 11.0 to 19.5%, and a balance of Zn and inevitable impurities. In the description below, the reason for adding each component and the reason for content limitation will be described in detail.
Mg may improve corrosion resistance of a plated steel material. In the present disclosure, a Mg content in the plating layer may be controlled to 4.0% or more to assure desired excellent corrosion resistance. When Mg is added excessively, dross may occur. Accordingly, the Mg content may be controlled to 6.3% or less.
Generally, when Mg is added in an amount of 1% or more, the effect of improving corrosion resistance may be exhibited, but when Mg is added in an amount of 2% or more, floating dross may increase in a plating bath due to oxidation of Mg in the plating bath, such that dross may need to be frequently removed.
Due to this problem, in the prior art, by adding 1.0% or more of Mg in Zn-Mg-Al-based zinc alloy plating, corrosion resistance may be assured, and an upper limit of Mg content may be determined to be 3.0% for commercialization.
However, to further improve corrosion resistance, it may be necessary to increase the Mg content to 4% or more. However, when the plating layer comprises 4% or more of Mg, dross may occur due to oxidation of Mg in the plating bath, which may be problematic, such that it may be necessary to add 11.0% or more of Al.
When Al is added excessively to suppress dross, however, a melting point of the plating bath may increase and an operating temperature may thus increase excessively, such that problems caused by high-temperature work, such as erosion of the plating bath structure and deterioration of the steel material, may occur. Also, the Al content in the plating bath is excessive, Al may react with Fe of the base steel sheet and may not contribute to formation of the Fe-Al inhibition layer, and reaction between Al and Zn may occur rapidly, such that a lump-shaped outburst phase may be excessively formed, which may rather deteriorate corrosion resistance. Accordingly, it may be preferable to control an upper limit of Al content in the plating layer to 19.5%.
In addition to the composition of the plating layer described above, a balance of Zn and other inevitable impurities may be further comprised. Inevitable impurities may comprise components unintentionally mixed in a process of manufacturing general hot-dip galvanized steel sheet, and a person skilled in the relevant technical field may easily understand the addition.
Meanwhile, according to the present disclosure, the plated steel sheet may satisfy relational expression 1 as below in order to secure corrosion resistance and excellent image clarity after painting and beautified surface appearance properties at the desired level.
(In the Relational expression 1, I(110) is X-ray diffraction integrated intensity of a (110) plane crystal peak of a MgZn2 phase, and I(103) is X-ray diffraction integrated intensity of a (103) plane crystal peak of a MgZn2 phase.)
The present inventors found that a presence ratio of (110) plane crystal of the MgZn2 phase and a (103) plane crystal of the MgZn2 phase present in the plating layer may be an important factor in assuring image clarity after painting and beautified surface appearance properties of the plating layer. That is, by controlling a ratio between X-ray diffraction integrated intensity of the (110) plane crystal peak of a MgZn2 phase obtained by analyzing by XRD on the surface of the plating layer and X-ray diffraction integrated intensity of (103) plane crystal peak of MgZn2 phase to satisfy relational expression 1, excellent corrosion resistance may be assured and image clarity after painting and surface appearance may also improve.
Specifically, in the present disclosure, when the amount of (103) plane crystals are large in the MgZn2 phase, it may indicate that a great deal of crystals are formed in the vertical direction, which prevents the crystals from growing in the lateral direction, thereby preventing the formation of spangle.
However, in the component system according to the present disclosure, the (110) plane crystal of the MgZn2 phase and the (103) plane crystal of the MgZn2 phase, which affect the properties of the present disclosure, may be essentially present, such that by harmonizing the two types of crystal planes, image clarity after painting and surface appearance properties may be determined.
Accordingly, when the I(110)/I(103) value defined from relational expression 1 is less than 0.1, a great deal of crystal mismatch may occur, such that adhesion of the plating layer may be reduced, which may be problematic. When the I(110)/I(103) value defined from relational expression 1 above exceeds 0.25, the presence ratio between the (110) plane crystal of the MgZn2 phase and the (103) plane crystal of the MgZn2 phase may be excessive, such that image clarity after painting or surface appearance properties may become inadequate. During rapid cooling, the (110) plane of the MgZn2 phase may be present below the plating layer, may promote the formation of (002) plane crystal of the Zn phase upwardly of the plating layer, and may be in contact with the (103) plane of the MgZn2 phase such that surface may be beautified.
In other words, the (110) plane crystal of the MgZn2 phase and the (103) plane crystal of the MgZn2 phase may be present in a mixed manner to satisfy the above relational expression 1, and as a great deal of the (103) plane crystal of the MgZn2 phase, which has a smaller interplanar spacing than the (002) plane crystal of the Zn phase, is present in as compared to the (110) plane crystal of the MgZn2 phase, by adding Mg, corrosion resistance as compared to conventional technology may improve, and a plated steel sheet having low surface roughness and beautified surface appearance may be assured.
Meanwhile, although not particularly limited, according to an embodiment of the present disclosure, in terms of maximizing the above-described effect, more preferably, a lower limit of the I(110)/I(103) value defined from relational expression 1 may be 0.11, or an upper limit of the I(110)/I(103) value may be 0.15.
In this case, as for the (110) plane crystal peak of the above-described MgZn2 phase and the (103) plane crystal peak of the MgZn2 phase, the (110) plane crystal peak and (103) plane crystal peak may be distinguished using methods known in the art from the X-ray diffraction integrated intensity obtained by analyzing the surface of the plating layer with XRD, which may thus not be separately defined in this specification.
Meanwhile, the method of measuring the X-ray diffraction integrated intensity may not be particularly limited, and a method known in the art may be applied. For example, the surface of the plating layer may be analyzed by XRD to measure the X-ray diffraction integrated intensity, and a RINT2000 diffractometer may be used as a device to measure the X-ray diffraction integrated intensity, and X-ray diffraction integrated intensity measurement conditions may comprise Cu target, voltage: 40 kV, current: 200 mA, and the X-ray diffraction angle (20) may be from 10 to 100°. As a representative example, when a Cu target is used, I(110) may be defined as the integrated intensity of the peak between 2θ=34.0° to 34.6°, and I(103) may be defined as integrated intensity of the peak between 20=37.0° to 37.5°. However, when the target material is changed to Mo, or the like, the value of 2θ may change depending on the type of target material, such that the range of 2θ is not particularly limited in the present disclosure.
Also, in this specification, the MgZn2 crystal having the (110) plane may refer to a structure in which the (110) plane appears among hexagonal crystals of the MgZn2 phase on the surface of a steel sheet. Also, the MgZn2 crystal having the (103) plane may refer to a structure in which the (103) plane appears among hexagonal crystals of the MgZn2 phase on the surface of a steel sheet.
Meanwhile, although not particularly limited, according to an embodiment of the present disclosure, the plated steel sheet may optionally satisfy the value of I (110) of 85 or less. As the value of I(110) satisfies 85 or less, the presence ratio of the (103) plane crystal of the MgZn2 phase may be increased as compared to the (110) plane crystal of the MgZn2 phase, within the range satisfying relational expression 1. Accordingly, by suppressing spangle in the plating layer, the influence of the (103) plane crystal of the MgZn2 phase, which contributes to assurance of beautified surface appearance properties, may be further increased.
Accordingly, more preferably, in terms of maximizing the above-mentioned effect, an upper limit of the value of I(110) may be 80, or a lower limit of the value of I(110) may be 50.
Alternatively, although not particularly limited, according to an embodiment of the present disclosure, the plated steel sheet may optionally have a value of I(103) of 525 or more. As the value of I(103) satisfies 525 or more, the presence ratio of the (103) plane crystal of the MgZn2 phase may be increased as compared to the (110) plane crystal of the MgZn2 phase, within the range satisfying relational expression 1. Accordingly, by suppressing spangle in the plating layer, the influence of the (103) plane crystal of the MgZn2 phase, which contributes to assurance of beautified surface appearance properties, may be further increased.
Accordingly, more preferably, in terms of maximizing the above-mentioned effect, a lower limit of the value of I (103) may be 530, or an upper limit of the value of I(103) may be 600.
In this case, although not particularly limited, the value of I(110) and the value of I(103) may be measured using a RINT2000 diffractometer under the conditions of a Cu target, voltage: 40 kV and current: 200 mA.
Meanwhile, although not particularly limited, according to an embodiment of the present disclosure, optionally, surface roughness of the plated steel sheet may satisfy the range of Ra: 0.3 to 0.6 μm and Rpc: 40 to 90 (/10 mm). By adjusting surface roughness of the plated steel sheet to satisfy the above-mentioned range, the effect of suppressing spangle may be further improved and more beautified surface appearance properties may be assured.
In the description below, the [method of manufacturing plated steel sheet] according to another aspect of the present disclosure will be described in detail. However, the plated steel sheet in the present disclosure may need to be manufactured by the manufacturing method below.
According to an embodiment of the present disclosure, preparing a base steel sheet may be further comprised, and the type of the base steel sheet is not particularly limited. A Fe-based base steel sheet used as the base steel sheet of the general galvanized steel sheet may be a hot-rolled steel sheet or a cold-rolled steel sheet, but an embodiment thereof is not limited thereto. Also, the base steel sheet may be, for example, carbon steel, ultra-low carbon steel, or high manganese steel used as a material for construction, home appliances, and automobiles, but an embodiment thereof is not limited thereto. In this case, the above description may be applied to the base steel sheet.
Thereafter, hot-dip galvanizing may be performed by immersing the base steel sheet in a plating bath comprising, by weight %, Mg: 4.0 to 6.3%, Al: 11.0 to 19.5%, and a balance of Zn and inevitable impurities.
In this case, according to an embodiment of the present disclosure, as for the reason for adding components and limiting content in the plating bath described above, excluding the small amount of Fe content which may flow from the base steel sheet, the description of the components of the plating layer described above may be applied.
Meanwhile, to manufacture a plating bath of the above-described composition, a composite ingot comprising predetermined Zn, Al and Mg or a Zn-Mg or a Zn-Al ingot comprising individual components may be used. To replenish the plating bath consumed by hot-dip plating, the ingot may be further melted and supplied. In this case, the ingot may be dissolved by being directly immersed in a plating bath, or the ingot may be melted in a separate pot and the molten metal may be added to the plating bath.
According to the present disclosure, during the hot-dip galvanizing, an immersing temperature of the base steel sheet may be controlled to satisfy an immersing temperature of TB−10° C. to TB−40° C. based on a plating bath temperature (TB). When an immersing temperature of the base steel sheet is less than TB−10° C., a problem may occur in which a crystal phase is not dense, and when the immersing temperature of the base steel sheet exceeds TB−40° C., a problem may occur in plating adhesion.
In this case, although not particularly limited, the aforementioned plating bath temperature (TB) may range from 440 to 500° C. Meanwhile, more preferably, a lower limit of the plating bath temperature (TB) may be 455° C., or an upper limit of the plating bath temperature (TB) may be 490° C.
Thereafter, air-wiping may be performed by supplying an inert gas cooled to 1 to 20° C. to the hot-dip galvanized steel sheet. The present inventors conducted extensive research and found that, differently from conventional methods, by performing air-wiping by supplying inert gas cooled to a specific temperature range, the effect of rapid cooling may be obtained without the problem of surface oxidation.
In other words, when the temperature of the inert gas supplied during air-wiping is less than 1° C., water droplets may form on peripheral devices, such that wiping may be uneven. When the temperature of the inert gas supplied during air-wiping exceeds 20° C., the effect of rapid cooling may be reduced and a beautified surface appearance may not be formed. In terms of maximizing the above-mentioned effect, more preferably, a lower limit of the temperature of nitrogen gas supplied during the air-wiping may be 1.0° C., or an upper limit of the temperature of nitrogen gas supplied during the air-wiping may be 5.0° C.
Although not particularly limited, according to an embodiment of the present disclosure, as the inert gas, argon (Ar) gas, nitrogen (N2) gas, or a mixed gas of argon and nitrogen may be used, and nitrogen gas may be used more preferably.
Also, according to the present disclosure, the air-wiping may be controlled to satisfy relational expression 2. By controlling the conditions of air-wiping to satisfy relational expression 2 below, a formation ratio between the (110) plane crystal of the MgZn2 phase and the (103) plane crystal of the MgZn2 phase may be optimized. Also, the surface may have beautified roughness properties exhibiting milky appearance, such that surface appearance may be smooth. In this case, relational expression 2 below may be a value obtained empirically, and thus, the unit thereof may not be specifically determined, and it may be sufficient to satisfy the Wair unit mm, Pair unit kPa, and T and To unit ° C. defined below.
(In the Relational expression 2, Wair is a spacing between air-knives, and a unit is mm. Pair is pressure of the air-knife, and a unit thereof is kPa. T is a temperature of the supplied inert gas, and a unit thereof is ° C. T. is an average temperature of atmosphere and is determined as 25° C.)
Also, although not particularly limited, according to an embodiment of the present disclosure, in the above-described air-wiping, a spacing between air-knives may range from 10 to 30 mm (more preferably, 10 to 20 mm). Alternatively, pressure of the air-knife may be in the range of 5 to 30 kPa (more preferably, 15 to 23 kPa). Alternatively, the temperature of the supplied gas may be in the range of 1 to 20° C. (more preferably, 1 to 5° C.). By adjusting the air-wiping conditions to satisfy the above-mentioned range, the plated steel sheet having excellent corrosion resistance, image clarity after painting and surface appearance may be effectively manufactured.
According to the present disclosure, after the air-wiping, primary cooling may be performed on the air-wiped steel sheet at an average cooling rate of 10 to 15° C./s to 420° C., and secondary cooling may be performed on the primary cooled steel sheet at an average cooling rate of 5 to 8° C./s in a temperature range of less than 420° C. and 300° C. or more. In this case, the average cooling rate may be based on the surface temperature of the steel sheet.
The present inventors conducted research and found that, by precisely controlling the cooling rate by dividing the cooling into two steps, and performing rapid cooling during primary cooling, the formation ratio between the (110) plane crystal of the MgZn2 phase and the (103) plane crystal of the MgZn2 phase may be more optimized, and surface appearance properties may further improve, and also that the effect of obtaining a uniform surface structure in the width direction of the steel sheet may be assured.
In other words, during the primary cooling, when the average cooling rate is less than 10.0° C./s, the effect of rapid cooling may be weak, which may be problematic, and when the rate exceeds 15.0° C./s during the primary cooling, the surface may be uneven in the width direction of the steel sheet. Also, during the secondary cooling, when the average cooling rate is less than 5.0° C./s, surface roughness may increase, which may be problematic, and when the average cooling rate exceeds 8.0° C./s during the secondary cooling, the surface of the steel sheet may be uneven in the width direction.
Meanwhile, although not particularly limited, according to an embodiment of the present disclosure, optionally, cooling conditions may be controlled to satisfy relational expressions 3 and 4 below during the cooling. By controlling the relationship between the average cooling rate during the primary cooling and the secondary cooling as in relational expressions 3 and 4 below, spangle may be further suppressed in the plated steel sheet and appearance properties may be further improved. In this case, since relational expressions 3 and 4 below are values obtained empirically, the units thereof may not be specifically determined, and it is sufficient to satisfy each unit of C1 and C2 defined below.
(In the Relational expression 3, C1 is an average cooling rate [° C./s] during the primary cooling, and C2 is an average cooling rate [° C./s] during the secondary cooling.)
Meanwhile, although not particularly limited, according to an embodiment of the present disclosure, optionally, surface roughness of the plated steel sheet obtained by the secondary cooling may be controlled to be in the range of Ra: 0.3 to 0.6 μm and Rpc: 40 to 90 (/10 mm). By controlling the surface roughness Ra and Rpc of the plated steel sheet to satisfy the above range, the surface may be beautified and excellent appearance may be assured.
As described above, by precisely controlling the plating composition and manufacturing conditions, a plated steel sheet having excellent corrosion resistance and also excellent bendability and surface appearance may be effectively provided.
Hereinafter, the present disclosure will be described in greater detail through embodiments. However, it may be important to note that the embodiments may be only intended to describe the present disclosure through examples and is not intended to limit the scope of rights of the present disclosure. This is because the scope of rights in present disclosure is determined by matters stated in the claims and matters reasonably inferred therefrom.
A base steel sheet having a composition of C: 0.018%, Si: 0.01%, Mn: 0.2%, P: 0.009%, S: 0.005%, Al: 0.1%, Nb:
0.02%, Cr: 0.2%, Ti: 0.02%, B: 0.015%, and a balance of Fe and inevitable impurities and having a thickness of 1.5 mm and a width of 1200 mm may be prepared. The prepared base steel sheet was hot-dip galvanized by being immersed in a plating bath under the conditions as in Table 1 below.
Thereafter, an air-wiping treatment was performed on the hot-dip galvanized steel sheet using nitrogen (N2) gas under the conditions as in Table 1 below, and primary cooling and secondary cooling were performed under the conditions as in Table 2 below. Thereafter, the steel sheet obtained by the secondary cooling was controlled to have surface roughness in Table 2 below.
A sample of the plated steel sheet obtained by the method in Tables 1 to 2 was prepared, the plating layer was dissolved in a hydrochloric acid solution, the dissolved liquid was analyzed by wet analysis (ICP) to measure the composition of the plating layer, and was listed in Table 3 (a balance of Zn and inevitable impurities are comprised).
Also, a cross-sectional sample cut in the direction perpendicular to the rolling direction of the steel sheet was manufactured such that an interfacial surface between the plating layer and the base steel sheet was able to observed, the sample was imaged using an SEM, and it was confirmed that a Fe-Al-based inhibition layer was formed between the base steel sheet and the Zn-Mg-Al-based plating layer. Using the SEM, the thickness of the Fe-Al-based inhibition layer was measured in the direction perpendicular to the rolling direction of the steel sheet and is listed in Table 3 below.
Also, to measure X-ray diffraction integrated intensity of the plating layer, a diffraction peaks MgZn2 (110) and MgZn2 (103) was measured at 2θ=34.0° to 38.0° under the conditions of a Cu target, voltage: 40 kV, and current: 200 mA using a RINT2000 diffractometer, and integrated intensity of the corresponding peak was calculated. Integrated intensity I(110) may be a value obtained by integrating the peak from 34° to 34.6°, and integrated intensity I(103) may be a value obtained by integrating the peak from 37° to 37.5° (unit is integrated intensity, corresponding to cps*2θ), and the values were listed in Table 3 below.
As for each inventive example and comparative example, properties were evaluated based on the criteria as below, and the evaluation results of each properties were listed in Table 4 below.
In order to evaluate corrosion resistance, corrosion resistance was evaluated according to the criteria as below using a salt spray tester (SST) using a test method in accordance with ISO14993.
To evaluate image clarity after painting, the material was cut into 75 mm×150 mm, the steel sheet is degreased and treated with phosphate, electrodeposition painting was performed and the Wsa (image clarity index) (um) value was measured.
To evaluate the size of spangle, images were taken at 100× magnification using an optical microscope, the sizes of the spangle were measured in two dimensions, the longitudinal axis and the horizontal axis, were averaged for 10 samples, and were evaluated according to the criteria as below.
As indicated in the experimental results in Table 4 above, in inventive examples 1 to 9 satisfying the plating composition and manufacturing conditions specified in the present disclosure, corrosion resistance, image clarity after painting and appearance properties were excellent.
In particular, among the inventive examples, in inventive examples 7 to 9 satisfying the cooling rates of relational expressions 3 and 4 specified in the present disclosure, surface appearance was more excellent than that of inventive examples 1 to 6. This may be because an appropriate ratio of (110) plane crystal of the MgZn2 phase and (103) plane crystal of the MgZn2 phase were formed around the (002) plane crystal of the Zn phase, and also the presence ratio of (103) plane crystals in the MgZn2 phase, which greatly contributes to the presence or absence of spangle, was improved.
In comparative examples 1 to 17, not satisfying the entirety of the plating compositions and manufacturing conditions specified in the present disclosure, one or more of corrosion resistance, image clarity after painting and appearance properties was deteriorated as compared to inventive examples 1 to 9.
| Number | Date | Country | Kind |
|---|---|---|---|
| 10-2021-0130131 | Sep 2021 | KR | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/KR2022/014541 | 9/28/2022 | WO |
