The present disclosure relates to a steel appropriate as an automotive exterior material, and more particularly, to a cold-rolled steel sheet, a zinc-plated steel sheet obtained by galvanizing the cold-rolled steel sheet, and a method for manufacturing the same.

Automotive exterior materials, in particular, exterior panel materials, are required to have a baking hardening characteristic at or above a certain level, and a baking hardening phenomenon refers to increasing yield strength, a phenomenon in which yield strength is increased by fixation of carbon and nitrogen in a solid solution state which are activated when painting and baking on dislocation produced during steel pressing. Since a steel having an excellent baking hardening characteristic is easily formed before plating baking and has a characteristics of improved dent resistance in a final product, it is ideal as an automotive exterior panel material. Also, the automotive exterior panel material is required to have a certain level of room temperature aging resistance so that aging is guaranteed for a certain period of time or longer (Patent Document 1).

Meanwhile, manufacturers who produce parts for automotive exterior panels such as hoods and doors are applying strict requirements to such parts. One of the requirements relates to painted appearance of the parts to which paint is applied. Exterior panels having significantly good painted appearance are highly evaluated when the panels have a mirror-like surface on which the panels reflect light without distortion, leading to clear reflected images.

The painted appearance is influenced by the surface of the coated substrate, as well as paint quality, and the surface is formed of in-plane structures having various sizes and scale. When the surface structures are small, they may be identified as surface roughness, but large structures may be identified as so called surface waviness. Thereamong, it is well known that large surface structures are conducted by passing through painted layers. Thus, the waviness of the coated substrate surface still exist to a certain part on the surface of the exterior paint layer.

Recently, since automobile manufacturers aim for energy and cost reduction through middle omission during a painting process, the surface waviness of automobiles is becoming increasingly important.

That is, the surface waviness may be measured after compression or forming is applied, the surface waviness in a formed part is important, and since a middle process is being omitted as described above, the importance of the surface characteristic of a substrate before coating, that is, a base steel sheet is increasing. That is to say, a manufacturing technology to allow the surface of a base steel sheet which is an initial substrate for manufacturing parts having a painted appearance to have a uniform and fine microstructure is required.

(Patent Document 1) Korean Patent Laid-Open Publication No. 10-2017-0012865

An aspect of the present disclosure is to provide a zinc-plated steel sheet having excellent distinctness of image as well as a baking hardening characteristic and aging resistance which are generally required physical properties, in providing a steel appropriate as an automotive exterior material, and a method for manufacturing the same.

Another aspect of the present disclosure is to provide a cold-rolled steel sheet which is a base steel sheet for obtaining the zinc-plated steel sheet, and a method for manufacturing the same.

Meanwhile, the object of the present disclosure is not limited to the above description. The object of the present disclosure will be understood from the entire content of the present specification, and a person skilled in the art to which the present disclosure pertains will understand an additional object of the present disclosure without difficulty.

According to an aspect of the present disclosure, a cold-rolled steel sheet includes, by weight: 0.0010 to 0.0050% of carbon (C), 0.050% or less (excluding 0%) of silicon (Si), 0.10 to 0.25% of manganese (Mn), 0.010 to 0.035% of phosphorus (P), 0.0100% or less of sulfur (S), 0.0050% or less of nitrogen (N), 0.100% or less (excluding 0%) of aluminum (Al), 0.0010 to 0.0100% of niobium (Nb), 0.0100% or less (excluding 0%) of copper (Cu), a reminder of Fe, and unavoidable impurities.

In an example embodiment of the present disclosure, the cold-rolled steel sheet may satisfy the following Relation 1:

$$\mathrm{Nb}\left(12/93\right)+\mathrm{S}\left(63/32\right)+\mathrm{Cu}\left(32/63\right)+\mathrm{d}/2\le 11$$
wherein d is an average crystal grain size (µm) of ferrite in an extreme surface part, and the extreme surface part is an ND surface (rolled surface) at a point within 100 µm in a thickness direction from a surface of the cold-rolled steel sheet.

In an example embodiment of the present disclosure, a microstructure of the base steel sheet may be ferrite at an area fraction of 95% or more.

In an example embodiment of the present disclosure, the ferrite may have an average crystal grain size of 20 µm or less.

According to the present disclosure, there is an effect of providing a base steel sheet (cold-rolled steel sheet) for providing a zinc-plated steel sheet having improved baking hardening characteristic and distinctness of image so as to be appropriate as an automotive exterior material, by limiting an alloy composition and optimizing a relationship between the alloy composition and the microstructure.

According to another aspect of the present disclosure, a method for manufacturing a cold-rolled steel sheet includes: preparing a steel slab; heating the steel slab to a temperature in a range of 1100 to 1300°C; finish hot rolling the heated steel slab at or above an Ar3 temperature to obtain a hot-rolled steel sheet; winding the hot-rolled steel sheet at a temperature in a range of 600 to 650°C; pickling the wound hot-rolled steel sheet and then cold rolling the steel sheet at a reduction rate of 70 to 83% to obtain a cold-rolled steel sheet; and annealing the cold-rolled steel sheet at a temperature in a range of 760 to 820°C.

In an example embodiment of the present disclosure, the steel slab may have the alloy composition described above, and the manufactured cold-rolled steel sheet may satisfy Relation 1.

According to another aspect of the present disclosure, a zinc-plated steel sheet includes: a base steel sheet; and a zinc-based plating layer provided on at least one surface of the base steel sheet.

In an example embodiment of the present disclosure, the base steel sheet may include, by weight: 0.0010 to 0.0050% of carbon (C), 0.050% or less (excluding 0%) of silicon (Si), 0.10 to 0.25% of manganese (Mn), 0.010 to 0.035% of phosphorus (P), 0.0100% or less of sulfur (S), 0.0050% or less of nitrogen (N), 0.100% or less (excluding 0%) of aluminum (Al), 0.0010 to 0.0100% of niobium (Nb), 0.0100% or less (excluding 0%) of copper (Cu), a reminder of Fe, and unavoidable impurities.

In an example embodiment of the present disclosure, the base steel sheet may satisfy Relation 1:

$$\mathrm{Nb}\left(12/93\right)+\mathrm{S}\left(63/32\right)+\mathrm{Cu}\left(32/63\right)+\mathrm{d}/2\le 11$$
wherein d is an average crystal grain size (µm) in an extreme surface part, and the extreme surface part is an ND surface (rolled surface) at a point within 100 µm in a thickness direction of the base steel sheet from an interface between the base steel sheet and the zinc-based plating layer.

According to the present disclosure, there is an effect of providing a zinc-plated steel sheet having improved distinctness of image so as to be appropriate as an automotive exterior material by optimizing an alloy component system. According to an example embodiment of the present disclosure, the zinc-plated steel sheet may have ΔWsa defined by the following Relation 2 of 0.15 µm or less: ΔWsa = surface waviness of steel sheet after 5% deformation - surface waviness of steel sheet before deformation

In an example embodiment of the present disclosure, the zinc-plated steel sheet may have a baking hardening amount of 30 MPa or more in a tensile test after a heat treatment at 170°C for 20 minutes.

In an example embodiment of the present disclosure, the base steel sheet may be the cold-rolled steel sheet described above.

In an example embodiment of the present disclosure, the zinc-plated steel sheet may have physical properties of a yield strength of 180 MPa or more, a tensile strength of 300 MPa or more, and an elongation rate of 33% or more.

According to still another aspect of the present disclosure, a method for manufacturing a zinc-plated steel sheet includes: preparing a steel slab; heating the steel slab to a temperature in a range of 1100 to 1300°C; finish hot rolling the heated steel slab at or above a Ar3 temperature to obtain a hot-rolled steel sheet; winding the hot-rolled steel sheet at a temperature in a range of 600 to 650°C; pickling the wound hot-rolled steel sheet and then cold rolling the steel sheet at a reduction rate of 70 to 83% to obtain a cold-rolled steel sheet; annealing the cold-rolled steel sheet at a temperature in a range of 760 to 820°C; hot galvanizing the annealed cold-rolled steel sheet to obtain a zinc-plated steel sheet; and temper rolling the zinc-plated steel sheet.

In an example embodiment of the present disclosure, the steel slab may have the same alloy composition as the base steel sheet and also may satisfy Relation 1 described above.

In an example embodiment of the present disclosure, the temper rolling treatment may be performed with a rolling force of 0.6 to 1.8% using a roll having a roughness (Ra) of 1.0 to 2.2 µm.

In an example embodiment of the present disclosure, the hot galvanizing may be performed in a zinc-based plating bath at 440 to 480°C.

In an example embodiment of the present disclosure, the temper rolling treatment may be performed by one or more methods selected from electro discharge texturing (EDT), shot blasting (SBT), and Topocrom Texturing (TCT) working.

According to the present disclosure, a zinc-plated steel sheet having excellent baking hardenability and aging resistance which are physical properties required as an automotive exterior material, and a cold-rolled steel sheet appropriate for obtaining the zinc-plated steel sheet may be provided.

Furthermore, according to the present disclosure, the zinc-plated steel sheet has improved distinctness of image and may be appropriately applied to the parts of an automotive exterior material having a painted appearance.

Since uniformity of a substrate (base steel sheet) surface becomes gradually important, in improving baking hardening characteristic and aging resistance of a steel applied as an automotive exterior material, while manufacturing parts having a painted appearance using the steel, the present inventors conducted an in-depth study on a method for achieving the surface uniformity.

As a result, they recognized that it is important to secure uniform and fine crystal grains on a surface part of the substrate (base steel sheet), and thus, intended to optimize the contents of certain elements of the alloy composition. In particular, according to an aspect of the present disclosure, it was confirmed that a steel having improved distinctness of image so as to be appropriate as an automotive exterior material may be provided, by controlling precipitate formation elements, while having an ultra-low carbon steel as a basic component in order to secure the baking hardening characteristic and the aging resistance, thereby completing the present disclosure.

Hereinafter, the present disclosure will be described in detail.

The cold-rolled steel sheet according to an aspect of the present disclosure may include, by weight: 0.0010 to 0.0050% of carbon (C), 0.050% or less (excluding 0%) of silicon (Si), 0.10 to 0.25% of manganese (Mn), 0.010 to 0.035% of phosphorus (P), 0.0100% or less of sulfur (S), 0.0050% or less of nitrogen (N), 0.100% or less (excluding 0%) of aluminum (Al), 0.0010 to 0.0100% of niobium (Nb), and 0.0100% or less (excluding 0%) of copper (Cu).

Hereinafter, the reasons of limiting the alloy composition of the cold-rolled steel sheet according to an example embodiment of the present disclosure will be described in detail. Meanwhile, unless otherwise particularly stated, the content of each element is by weight and the ratios of the structure are by area.

Carbon (C) is an intrusive solid solution element, and has a significant influence on formation of steel sheet texture in cold rolling and annealing processes. When a solid solution carbon amount in steel is increased, growth of crystal grains having {111} gamma (γ)-fiber textures favorable for drawing working is suppressed, and growth of crystal grains having {110} and {100} textures is promoted, thereby deteriorating the drawing characteristic of an annealed cold-rolled steel sheet. Thus, C may be included in an amount of 0.0050% or less, and when the content of C is more than 0.0050%, the aging resistance of a steel sheet may be deteriorated. Meanwhile, in terms of securing the baking hardenability of a steel sheet, C may be included in an amount of 0.0010% or more.

Therefore, according to an example embodiment of the present disclosure, C may be included in an amount of 0.0010 to 0.0050%. According to another example embodiment of the present disclosure, C may be included in an amount of 0.0011% or more or 0.0012% or more, and according to another example embodiment, C may be included in an amount of 0.0045% or less.

Silicon (Si) is an element contributing to strength increase by solid solution strengthening, but in the present disclosure, even when Si is not intentionally added, there is no difficulty in securing physical properties. However, 0% may be excluded, considering the inevitably added level during a steel sheet manufacturing process.

According to an example embodiment of the present disclosure, when the content of Si is more than 0.050%, scale defects are caused on the surface of a steel sheet to deteriorate plating surface characteristics, and thus, the content may be limited to 0.050% or less.

Therefore, according to an example embodiment of the present disclosure, Si may be included in an amount of 0.050% or less, excluding 0%, and according to another example embodiment, it may be included in an amount of 0.040% or less.

Manganese (Mn), which is a solid solution strengthening element, contributes to an increase in steel strength, and also has an effect of precipitating S present in steel as MnS to suppress brittleness occurrence caused by S.

In an example embodiment of the present disclosure, when the content of Mn is less than 0.10%, intended strength may not be secured, but when the content is more than 0.25%, surface defects may occur by an oxide.

Therefore, in an example embodiment of the present disclosure, Mn may be included in an amount of 0.10 to 0.25%, and according to another example embodiment, it may be included in an amount of 0.11% or more or 0.13% or more. According to another example embodiment, Mn may be included in an amount of 0.23% or less or 0.21% or less.

Phosphorus (P) has the best solid solution effect and is effective for securing strength without greatly impairing a drawing characteristic of steel.

In an example embodiment of the present disclosure, when the content of P is less than 0.010%, the effect described above may not be sufficiently obtained, but when the content is more than 0.035%, strength is excessively increased, or secondary brittleness and surface striped defects may occur due to P segregation.

Therefore, in an example embodiment of the present disclosure, the P may be included in an amount of 0.010 to 0.035%. According to another example embodiment of the present disclosure, P may be included in an amount of 0.015% or more, and according to another example embodiment, P may be included in an amount of 0.030% or less.

Sulfur (S) and nitrogen (N) are impurities present in steel and elements which are unavoidably added in a steel manufacturing process. In terms of securing the welding characteristic of steel, it is favorable to control the content of the elements as low as possible.

In an example embodiment of the present disclosure, S may be 0.0100% or less, and N may be 0.0050% or less. However, considering the unavoidably added level during the steel manufacturing process, the contents of S and N may be more than 0%.

Aluminum (Al) is bonded to N present in steel and precipitated as AlN, and the precipitate contributes to improvement of the drawing characteristic and ductility of steel.

In an example embodiment of the present disclosure, when the content of Al is more than 0.100%, an Al inclusion is excessively formed during a steelmaking operation, thereby causing internal defects in a steel sheet.

Therefore, in an example embodiment of the present disclosure, Al may be included in an amount of 0.100% or less, excluding 0%. According to another example embodiment of the present disclosure, Al may be included in an amount of 0.080% or less. According to another example embodiment of the present disclosure, Al may be included in an amount of 0.005% or more.

Niobium (Nb) is an element which is the most effective for forming very fine crystal grains in rolling and cooling processes, when an austenite unrecrystallization temperature range due to a solute drag and precipitate pinning effect during hot rolling expands to a high temperature.

In an example embodiment of the present disclosure, when the content of Nb is less than 0.0010%, the austenite unrecrystallization temperature range narrows, and the crystal grain refinement effect may not be expressed. However, when the content is more than 0.0100%, baking hardenability is deteriorated due to scavenging of C.

Therefore, in an example embodiment of the present disclosure, Nb may be included in an amount of 0.0010 to 0.0100%. According to another example embodiment of the present disclosure, Nb may be included in an amount of 0.0020% or more or 0.0030% or more. According to another example embodiment, Nb may be included in an amount of 0.0090% or less or 0.0085% or less.

Copper (Cu) is an element which is difficult to control when adjusting the composition of steel in a steelmaking process, and in an example embodiment of the present disclosure, when the content of cu is more than 0.0100%, a Cu₂S precipitate is formed to cause non-uniformity of a crystal grain size and occurrence of grain boundary embrittlement.

Therefore, in an example embodiment of the present disclosure, Cu may be included in an amount of 0.0100% or less, and according to another example embodiment, it may be included in an amount of 0.0095% or less, and according to sill another example embodiment, it may be included in an amount of 0.0090% or less.

In an example embodiment of the present disclosure, Cu may be included in an amount of more than 0%, and as an example, at 0.0010% or more, considering that it is not easy remove Cu in a steelmaking process.

The remaining component of the present disclosure is iron (Fe). However, since in a common manufacturing process, unintended impurities may be unavoidably incorporated from raw materials or the surrounding environment, it may not be excluded. Since these impurities are known to any person skilled in the common manufacturing process, the entire contents thereof are not particularly mentioned in the present specification.

In an example embodiment of the present disclosure, the cold-rolled steel sheet may have the alloy composition described above and may include 0.0050% or less of carbon in the alloy composition. Thus, in an example embodiment of the present disclosure, the microstructure of the cold-rolled steel sheet may be mainly formed of a ferrite phase. As an example, the ferrite phase may be included in an amount of an area fraction of 95% or more. As another example, the microstructure of the cold-rolled steel sheet may be formed of a ferrite single phase structure.

In an example embodiment of the present disclosure, the cold-rolled steel sheet may include 5% or less of unavoidably produced other structures, and as an example, may include 5% or less of pearlite.

In an example embodiment of the present disclosure, ferrite may have an average crystal grain size of 20 µm or less. When the average crystal grain size of the ferrite is more than 20 µm, the surface of the steel sheet becomes non-uniform during formation of a zinc-plated steel sheet obtained by galvanizing the cold-rolled steel sheet, and it may be difficult to secure distinctness of image. Herein, the average crystal grain size of the ferrite refers to an average value of a ferrite crystal grain size to the total thickness cross section of the cold-rolled steel sheet. That is to say, the average crystal grain size of ferrite is distinguished from an extreme surface part average crystal grain size (d) in the following Relation 1.

The cold-rolled steel sheet according to an example embodiment of the present disclosure may satisfy the following Relation 1 showing a relationship between the alloy composition and the microstructure (crystal grain size):

$$\mathrm{Nb}\left(12/93\right)+\mathrm{S}\left(63/32\right)+\mathrm{Cu}\left(32/63\right)+\mathrm{d}/2\le 11$$
wherein d is an average crystal grain size (µm) of ferrite in an extreme surface part, and the extreme surface part is an ND surface (rolled surface) at a point within 100 µm in a thickness direction from a surface of the cold-rolled steel sheet.

The inventors of the present disclosure found that it is important to control precipitation-type elements which affect texture recrystallization in an annealing process during a process of manufacturing the cold-rolled steel sheet, in securing uniform and fine crystal grains on the surface part of the cold-rolled steel sheet, and thus, derived Relation 1.

In an example embodiment of the present disclosure, the content of Nb constituting Relation 1 is excessive, Nb is bonded to C to deteriorate the baking hardenability of the cold-rolled steel sheet, and S and Cu form a Cu₂S precipitate in an annealing process during a steel manufacturing process to cause non-uniformity of structure. Thus, according to an example embodiment of the present disclosure, the relationship between the contents of Nb, S, and Cu and the average crystal grain size of ferrite in the extreme surface part may be controlled as Relation 1, thereby improving the baking hardenability of the cold-rolled steel sheet. Furthermore, the distinctness of image of the zinc-plated steel sheet obtained by galvanizing the cold-rolled steel sheet having an improved baking hardening characteristic may be improved.

In an example embodiment of the present disclosure, the meaning that the value of Relation 1, that is, the relationship between the contents of Nb, S, and Cu and the average crystal grain size of the extreme surface part of the cold-rolled steel sheet is more than 11, is non-uniformly formed surface of the cold-rolled steel sheet. Thus, the baking hardenability of the cold-rolled steel sheet may not be secured, and the distinctness of image of the zinc-plated steel sheet may not be secured.

In an example embodiment of the present disclosure, since the average crystal grain size (d) in the extreme surface part of Relation 1 is distinguished from the average crystal grain size of ferrite mentioned above, it is acceptable for the value of d to be outside of the average crystal grain size range of ferrite described above.

The average crystal grain size mentioned in the present disclosure refers to the size of the circle equivalent diameter of each crystal grain, and the average value of these diameter.

Hereinafter, the method for manufacturing a cold-rolled steel sheet according to another aspect of the present disclosure will be described in detail. The following manufacturing method corresponds to an example for manufacturing the cold-rolled steel sheet according to an example embodiment of the present disclosure.

According to an example embodiment of the present disclosure, the cold-rolled steel sheet may be manufactured through processes of [hot rolling - cold rolling - annealing] of a heated steel slab, and each process step will be described in detail below.

After preparing a steel slab according to an example embodiment of the present disclosure, the steel slab may be heated. The heating process of the steel slab is a process for performing the hot rolling process described later well. As an example, since the steel slab may have the same alloy composition as the cold-rolled steel sheet according to an example embodiment of the present disclosure, the description of the alloy element is replaced with the above description.

In an example embodiment of the present disclosure, the heating of the steel slab may be performed at a temperature in a range of 1100 to 1300°C. When the heating temperature is lower than 1100°C, a rolling load may occur in the subsequent hot rolling process, but when the temperature is higher than 1300°C, surface scale defects may occur.

The heated steel slab may be hot rolled to obtain a hot-rolled steel sheet.

In an example embodiment of the present disclosure, finish hot rolling may be performed at or above Ar3 during the hot rolling, and when the temperature is lower than Ar3, two-phase region rolling may be performed to cause texture non-uniformity.

In an example embodiment of the present disclosure, in terms of securing fine crystal grains on the surface of a steel sheet in finish hot rolling, the finish hot rolling may be performed at a temperature in a range of 880 to 950°C.

The hot-rolled steel sheet obtained by the hot rolling may be wound.

In an example embodiment of the present disclosure, the winding may be performed at a temperature in a range of 600 to 650°C. When the temperature during winding is lower than 600°C, a large amount of solid solubilized Nb and the like are present in steel to adversely affect the recrystallization and particle growth suppression in the subsequent annealing process, but when the temperature is higher than 650°C, secondary scale may be produced to deteriorate the surface of the steel sheet.

The wound hot-rolled steel sheet may be cold rolled with uncoiling to obtain a cold-rolled steel sheet. Herein, the rolling reduction rate may be controlled so that an intended thickness may be obtained.

In an example embodiment of the present disclosure, the cold rolling may be controlled to 70 to 83% based on a cumulative rolling reduction rate. When the reduction rate during the cold rolling is less than 70%, {111} texture does not sufficiently grow to deteriorate formability, but when it is more than 83%, the load of a rolling roll becomes severe to deteriorate the shape.

According to another example embodiment of the present disclosure, the cold rolling may be performed at a cumulative rolling reduction rate of 74% or more, and according to still another example embodiment, it may be performed at a cumulative rolling reduction rate of 80% or less.

In an example embodiment of the present disclosure, before performing the cold rolling, a pickling process may be further performed in order to remove surface scale of the wound hot-rolled steel sheet. Since the pickling process depends on common conditions, the conditions are not particularly defined.

The cold-rolled steel sheet obtained by the cold rolling may be annealed.

In an example embodiment of the present disclosure, in order to remove deformation caused by the rolling in the annealing treatment and perform softening to promote improvement of processability, annealing may be performed at a recrystallization temperature or higher.

In an example embodiment of the present disclosure, the annealing may be performed at a temperature in a range of 760 to 820°C. During the annealing treatment, when the temperature is lower than 760°C, a sufficient recrystallization driving force may not be secured, but when the temperature is higher than 820°C, crystal grains may be coarsened.

Hereinafter, the zinc-plated steel sheet according to another aspect of the present disclosure will be described in detail.

According to an example embodiment of the present disclosure, the zinc-plated steel sheet may include a base steel sheet; and a plating layer provided on at least one surface of the base steel sheet.

In an example embodiment of the present disclosure, the plating layer may be a zinc-based plating layer including zinc as a main component, and the constituents of the plating layer commonly applied in the art may be identically applied to the zinc-based plating layer.

In an example embodiment of the present disclosure, the base steel sheet for providing the plating layer may be the cold-rolled steel sheet according to an example embodiment of the present disclosure. As described above, the cold-rolled steel sheet according to an example embodiment of the present disclosure secures surface uniformity as well as baking hardenability by optimizing a relationship between an alloy composition and microstructure, as well as controlling the alloy composition and the microstructure.

The zinc-plated steel sheet according to an example embodiment of the present disclosure providing the plating layer, as an example, the zinc-based plating layer on at least one surface of the cold-rolled steel sheet may have excellent distinctness of image.

In an example embodiment of the present disclosure, the zinc-plated steel sheet may have a characteristic of ΔWsa defined by the following Relation 2 of 0.15 µm or less. That is, since the zinc-plated steel sheet according to an example embodiment of the present disclosure is obtained by using the cold-rolled steel sheet having improved surface uniformity as the base steel sheet, the surface change amount after deformation may be minimized. In an example embodiment of the present disclosure, the ΔWsa value according to Relation 2 being more than 0.15 µm means that the change amount after deformation is relatively large, which is unfavorable for securing distinctness of image. ΔWsa = surface waviness of steel sheet after 5% deformation - surface waviness of steel sheet before deformation

In Relation 2 according to an example embodiment of the present disclosure, ΔWsa, which is a Wsa measurement value of a plated steel sheet, represents a difference between a Wsa value before working (deformation) and a Wsa value after working (deformation) of the plated steel sheet. As an example of the working (deformation) may be imparted through machine forming, but is not limited thereto.

In an example embodiment of the present disclosure, the zinc-plated steel sheet may have an excellent baking hardening characteristic, and specifically, a baking hardening amount (L-BH, tensile test after a heat treatment at 170°C for 20 minutes) of 30 MPa or more.

In addition, in an example embodiment of the present disclosure, since the zinc-plated steel sheet may have the physical properties of a yield strength of 180 MPa or more, a tensile strength of 300 MPa or more, and an elongation rate of 33% or more, it may be appropriately applied as an automotive exterior material.

Hereinafter, a method for manufacturing a zinc-plated steel sheet according to another aspect of the present disclosure will be described in detail. The following manufacturing method corresponds to an example for manufacturing the zinc-plated steel sheet according to an example embodiment of the present disclosure.

According to an example embodiment of the present disclosure, the zinc-plated steel sheet may be manufactured by preparing a base steel sheet; hot galvanizing the base steel sheet to obtain a zinc-plated steel sheet having a zinc-based plating layer on at least one surface of the base steel sheet; and temper rolling the zinc-plated steel sheet. Each process step will be described in detail in the following.

First, a base steel sheet for performing the zinc plating process according to an example embodiment of the present disclosure. In an example embodiment of the present disclosure, the base steel sheet may be a cold-rolled steel sheet, and the cold-rolled steel sheet may be the cold-rolled steel sheet according to an example embodiment of the present disclosure. That is, since it may be the cold-rolled steel sheet as described above, the description of the base steel sheet will be replaced with the above description of the cold-rolled steel sheet.

The prepared base steel sheet, that is, the cold-rolled steel sheet is hot-dip galvanized in a continuous hot-dip galvanizing line, thereby obtaining a zinc-plated steel sheet having a zinc-based plating layer formed on at least one surface of the cold-rolled steel sheet.

In an example embodiment of the present disclosure, the hot galvanizing may be performed by dipping the base steel sheet in a plating bath including zinc as the main component, and the component in the plating bath is not particularly limited. That is to say, it may depend on common conditions which are applied to manufacture of the zinc-plated steel sheet by the hot galvanizing process.

In an example embodiment of the present disclosure, the hot galvanizing may be performed at a temperature in a range of 440 to 480°C. The temperature range refers to the temperature of the plating bath.

The zinc-plated steel sheet may be temper rolled.

In an example embodiment of the present disclosure, the temper rolling may be performed with a rolling force of 0.6 to 1.8% using a roll having a roughness (Ra) of 1.0 to 2.2 µm.

In an example embodiment of the present disclosure, when the roughness (Ra) of the roll during the temper rolling is less than 1.0 µm, the targeted surface may not be secured due to low roughness working, but when it is more than 2.2 µm, a subsequent forming process, for example, a press process may not be performed well.

In an example embodiment of the present disclosure, when temper rolling is performed using a roll having a controlled surface roughness, the rolling force is less than 0.6%, baking hardenability may be deteriorated, but when the rolling force is more than 1.8%, yield strength may be excessively increased.

In an example embodiment of the present disclosure, the temper rolling treatment may be performed by one or more methods selected from electro discharge texturing (EDT), shot blasting (SBT), and Topocrom Texturing (TCT) working. As an example, the Topocrom texturing (TCT) working is a method of forming unevenness on a chromium coating layer itself by adjusting the temperature of a coating solution and current density in a chromium (Cr) coating process, without a process of mechanically and physically working roughness

The zinc-plated steel sheet manufactured according to an example embodiment of the present disclosure may have an excellent baking hardening characteristic and aging resistance, and also excellent distinctness of image by uniformly securing surface crystal grains.

Hereinafter, the present disclosure will be specifically described through the following examples. However, it should be noted that the following examples are only for describing the present disclosure by illustration, and not intended to limit the scope of right of the present disclosure. The reason is that the rights scope of the present disclosure is determined by the matters described in the claims and reasonably inferred therefrom.

A steel slab having the alloy composition shown in the following Table 1 and a thickness of 250 mm was prepared, heated at 1300°C or lower, and then hot rolled, wound, cold rolled, and annealed under the conditions shown in the following Table 2 to manufacture a cold-rolled steel sheet. Each cold-rolled steel sheet was dipped into a hot galvanizing bath at 455±5°C to perform plating, thereby obtaining a zinc-plated steel sheet. Thereafter, each zinc-plated steel sheet was temper rolled using a roll according to the conditions of the following Table 2.

The mechanical properties, the baking hardening characteristic, and deep drawing workability of the zinc-plated steel sheet manufactured according to the above were evaluated, and the results are shown in the following Table 3.

The tensile physical properties of yield strength (YS), tensile strength (TS), and elongation rate (T-El) were measured using a universal tensile tester in accordance with the standard of ISO6892, after collecting a specimen in accordance with the standard of JIS 5.

The same specimen as the specimen for evaluating the tensile physical properties was baked at 170°C for 20 minutes after 2% pre-strain, and then lower yield stress (L-BH) was measured to evaluate a baking hardening characteristic. At this time, only when the L-BH value was 30 MPa or more, it was determined as a pass.

In order to measure a r value which is an indicator of the deep drawing working, JIS 5 tensile specimens in a total of 3 direction of a parallel direction, a 45° direction, and a perpendicular direction to the rolling direction were collected on each zinc-plated steel sheet, and the r value of each specimen was measured. The r value was derived by measuring a change value of a sheet thickness and a change value of a sheet width when a tensile deformation of about 15% was performed in the previously performed tensile test, and determining a ratio of the change value of the sheet width to the sheet thickness. At this time, when the r value in the direction parallel to the rolling direction was r₀, the r value in the 45° direction was r₄₅, and the r value in the perpendicular direction was r₉₀, each value was substituted into the following (equation) to determine a final r value, and when the value is 1.0 or more, it was determined as a pass.$$\mathrm{r}\mathrm{value}={\mathrm{r}}_0+\left(2\times {\mathrm{r}}_{45}\right)+\left({\mathrm{r}}_{90}/4\right)$$

Meanwhile, in order to confirm the crystal grain distribution in the extreme surface part of the cold-rolled steel sheet which is the base steel sheet of the zinc-plated steel sheet, the average crystal grain size of the annealed cold-rolled steel sheet was measured using an Orientation imaging microscopy (OIM) analysis software available from Te×SEM Laboratories (TSL) through electron backscattered diffraction (EBSD) analysis. In addition, as a result of confirming the microstructure of each cold-rolled steel sheet with an optical microscope, ferrite at an area fraction of 95% or more was observed in all steel types (Inventive Steels 1 to 9 and Comparative Steels 1 to 6). At this time, residual structure other than ferrite was a pearlite phase.

Further, in order to measure the surface waviness of the zinc-plated steel sheet, a blank of 225 mm×225 mm was manufactured, and then the blank was compressed in a compressor having the force of a hollow punch having a diameter of 75 mm and a blank holder so that movement of any material of the blank was completely suppressed between the blank holder and the die, thereby manufacturing a cup. At this time, deformation of the cup was performed at a punch pull depth of about 17 to 18 mm so that a thickness strain of the bottom was about 5%±0.2%. Thereafter, the surface waviness before deformation and the surface waviness after deformation of the blank were measured, and a difference between the values (ΔWsa) was calculated. Steel type Alloy composition (wt%) C Si Mn P S Al Nb Cu N Inventive Steel 1 0.0016 0.025 0.13 0.020 0.0060 0.034 0.0030 0.0010 0.0015 Inventive Steel 2 0.0017 0.021 0.18 0.019 0.0046 0.035 0.0039 0.0080 0.0021 Inventive Steel 3 0.0021 0.035 0.19 0.022 0.0080 0.033 0.0030 0.0050 0.0018 Inventive Steel 4 0.0018 0.032 0.15 0.021 0.0043 0.035 0.0030 0.0080 0.0022 Inventive Steel 5 0.0023 0.018 0.15 0.020 0.0062 0.032 0.0048 0.0065 0.0019 Inventive Steel 6 0.0018 0.022 0.18 0.025 0.0054 0.035 0.0030 0.0024 0.0018 Inventive Steel 7 0.0019 0.024 0.15 0.020 0.0087 0.031 0.0050 0.0021 0.0025 Inventive Steel 8 0.0015 0.028 0.17 0.024 0.010 0.029 0.0030 0.0080 0.0023 Inventive Steel 9 0.0017 0.020 0.20 0.018 0.010 0.032 0.0035 0.0100 0.0015 Comparative Steel 1 0.0018 0.026 0.18 0.022 0.0088 0.035 0.0032 0.0050 0.0013 Comparative Steel 2 0.0018 0.030 0.14 0.023 0.0092 0.040 0.0054 0.1300 0.0022 Comparative Steel 3 0.0018 0.024 0.18 0.021 0.0090 0.039 0.0080 0.1500 0.0018 Comparative Steel 4 0.0018 0.028 0.15 0.020 0.0110 0.031 0.0011 0.1200 0.0016 Comparative Steel 5 0.0016 0.025 0.13 0.020 0.0060 0.034 0.0030 0.0010 0.0027 Comparative Steel 6 0.0017 0.021 0.18 0.019 0.0046 0.035 0.0120 0.0080 0.0024 In table 1, Inventive Steels 1 and 5 satisfied the present disclosure, but were indicated as comparative steels, since their process conditions of the following Table 2 were out of the scope of the present disclosure. Steel type Finish hot rolling temperature (°C) Winding temperature (°C) Cold rolling reduction rate (%) Annealing temperature (°C) Temper rolling Roll surface roughness (Ra, µm) Rolling force (%) Inventive Steel 1 910 611 78 788 1.8 1.52 Inventive Steel 2 915 620 79 790 2.0 1.62 Inventive Steel 3 905 613 80 810 2.1 1.3 Inventive Steel 4 921 618 78 820 2.1 1.31 Inventive Steel 5 899 625 80 791 2.0 1.51 Inventive Steel 6 912 610 81 800 1.9 0.8 Inventive Steel 7 916 605 79 795 2.1 1.27 Inventive Steel 8 925 619 80 816 2.0 1.4 Inventive Steel 9 890 624 80 811 2.0 1.31 Comparative Steel 1 911 621 80 839 2.0 1.54 Comparative Steel 2 905 613 80 810 1.9 1.3 Comparative Steel 3 899 625 80 791 2.1 1.51 Comparative Steel 4 912 610 81 800 2.1 1.6 Comparative Steel 5 910 620 60 790 2.0 1.52 Comparative Steel 6 908 615 80 835 2.0 1.4 Steel type d (µm) Relation 1 YS (MPa) TS (MPa) El (%) r value L-BH (MPa) ΔWsa (µm) Inventive Steel 1 17 8.5 208 316 42 1.5 66 0.07 Inventive Steel 2 18 9.0 199 311 45 1.5 40 0.06 Inventive Steel 3 20 10.0 194 323 46 1.4 38 0.08 Inventive Steel 4 19 9.5 192 308 41 1.8 50 0.13 Inventive Steel 5 18 9.0 200 324 43 1.6 32 0.05 Inventive Steel 6 21 10.5 212 317 42 1.5 45 0.08 Inventive Steel 7 15 7.5 211 309 40 1.5 55 0.09 Inventive Steel 8 20 9.0 193 313 46 1.8 47 0.11 Inventive Steel 9 19 9.5 205 327 43 1.6 39 0.10 Comparative Steel 1 25 12.5 191 339 48 1.8 35 0.17 Comparative Steel 2 23 11.6 201 318 45 1.5 42 0.19 Comparative Steel 3 24 12.1 198 308 43 1.6 49 0.16 Comparative Steel 4 23 11.6 208 328 42 1.5 48 0.18 Comparative Steel 5 25 12.5 232 340 40 0.9 28 0.16 Comparative Steel 6 18 9.0 178 301 48 1.7 31 0.07 In Table 3, d is an average crystal grain size of ferrite in an extreme surface layer part of the annealed cold-rolled steel sheet and is an average size of crystal grains measured on an ND surface (rolled surface) at a point within 100 um in the thickness direction from the surface of the cold-rolled steel sheet. Relation 1 represents a value derived from [Nb(12/93) + S(63/32)+ Cu(32/63) + d/2].

As shown in Tables 1 to 3, Inventive Steels 1 to 9 which all satisfied the alloy compositions and the manufacturing conditions suggested in the present disclosure had the surface crystal grains of the base steel sheet (cold-rolled steel sheet) which were uniform and finely formed (satisfying Relation 1). As a result, since all of Inventive Steels 1 to 9 had excellent baking hardening characteristic and aging resistance, with L-BH which is the indicator of the baking hardenability of 30 MPa or more and the r value which is the indicator of deep drawing working of 1.0 or more, and secured the value of difference (ΔWsa) between the surface waviness before/after deformation as 0.15 µm or less, they were confirmed to have excellent distinctness of image.

However, Comparative Steels 1 to 6 which did not satisfy the alloy compositions or manufacturing conditions suggested in the present disclosure had the physical properties at least one of which was poor.

Comparative Steel 1 which satisfied the alloy composition of the present disclosure, but had an excessively high annealing temperature during the manufacturing conditions had a non-uniform surface crystal grains of the base steel sheet (cold-rolled steel sheet), did not satisfy Relation 1, and thus, had poor distinctness of image.

Comparative Steels 2 to 4 having an excessive Cu content in steel showed the results of a difference (ΔWsa) in surface waviness before/after deformation of more than 0.15 µm by having the value of Relation 1 of more than 11. That is, the distinctness of image was poor.

In addition, Comparative Steel 5 which satisfied the alloy composition of the present disclosure, but had an excessively low reduction rate during cold rolling was not able to uniformly secure the crystal grains on the surface part of the base steel sheet (cold-rolled steel sheet) so that Relation 1 was satisfied, and as a result, the distinctness of image was poor, and the workability and baking hardenability were also poor.

Meanwhile, Comparative Steel 6 satisfied Relation 1, but had an excessive Nb content in steel, and had poor yield strength by performing annealing at a high temperature.

Though not shown in Tables 1 to 3, since Inventive Steels 1 to 9 and Comparative Steels 1 to 6 contained carbon within a range of 0.001 to 0.005%, the ferrite phase was formed at 95% by area or more in the microstructure.