Surface-treated steel sheet

Abstract

This surface-treated steel sheet has a base material steel sheet, a plating layer, a first coating, and a second coating. The plating layer has a Zn concentration of 40%-100% and a Mg concentration of 0% or more and less than 4.0%. The following items satisfy a predetermined relationship: the maximum concentration of Ti, the maximum concentration of Zr, and the maximum concentration of V in the interval from a first interface to the center of the the first coating film in the thickness direction of the first interface and a second interface; the average concentration of C in the central section of the first coating; the average concentration of C in the central section of the second coating; the maximum concentration of Mg in a border area of the first coating; the average concentration of Mg in the central section of the first coating; the maximum concentration of F in the border area of the first coating; the average concentration of F in the central section of the first coating; the average concentration of Si in the central section of the first coating; the average concentration of Zn in the central section of the first coating; and the average concentration of Zn in the central section of the second coating.

Description

[Technical Field]

[0001] The present invention relates to a surface-treated steel sheet. This application claims priority based on Japanese Patent Application No. 2022-161691 filed on October 6, 2022, and Japanese Patent Application No. 2022-161692 filed on October 6, 2022, the contents of which are incorporated herein by reference. [Background technology]

[0002] Conventionally, plated steel sheets (zinc-based plated steel sheets), in which a zinc-based plating layer is formed on the surface of steel sheets, have been used in a wide range of applications, including automobiles, building materials, and home appliances. Furthermore, for the purpose of imparting corrosion resistance, paint adhesion, etc. to the surface of such zinc-based plated steel sheet, methods such as chromate treatment using a treatment solution containing chromic acid, dichromic acid, or a salt thereof as a main component, treatment using a metal surface treatment agent that does not contain chromium, phosphate treatment, treatment with a silane coupling agent alone, and organic resin coating treatment are generally known and in practical use.

[0003] In particular, in recent years, various legal restrictions have been imposed on hexavalent chromium compounds, which can have adverse effects on the environment and human health, and efforts are being made to develop chromium-free metal surface treatment agents.One example of chromium-free metal surface treatment agents is technology that uses oxides or hydroxides of Group 4 metals such as Ti and Zr. For example, Patent Document 1 discloses a chromate-free chemically treated steel sheet having a substrate of zinc-plated steel sheet or zinc alloy-plated steel sheet, on the surface of which is formed a chemically treated coating film containing a fluoride and an oxide or hydroxide of a valve metal whose oxide exhibits high insulation resistance. Patent Document 2 discloses a hot-dip zinc alloy-plated steel sheet with excellent corrosion resistance, in which a chemical conversion coating containing one or more of a hydroxide, oxide, oxyacid, oxyacid salt, and fluoride of a valve metal as a main component is formed on a Mg-containing zinc alloy plating layer through an interfacial reaction layer containing one or more selected from magnesium fluoride, magnesium phosphate, and composite compounds of magnesium and a valve metal oxyacid salt. In Patent Document 2, by using a zinc alloy plating layer containing Mg as a base, an interfacial reaction layer containing Mg is formed, thereby achieving high white rust resistance (corrosion resistance). Furthermore, Patent Document 3 discloses a hot-dip zinc alloy plated steel sheet having excellent corrosion resistance, in which a composite chemical conversion coating of Ti and V is formed on a Zn-Al alloy plated layer via an Al-F interfacial reaction layer. In Patent Document 3, by using a zinc alloy plated layer containing Al as a base, an Al-F reaction layer is formed, thereby achieving high white rust resistance. [Prior art documents] [Patent documents]

[0004] [Patent Document 1] Japanese Patent Publication No. 2002-194558 [Patent Document 2] Japanese Patent Publication No. 2007-23309 [Patent Document 3] Japanese Patent Publication No. 2003-306777 Summary of the Invention [Problem to be solved by the invention]

[0005] The technologies disclosed in Patent Documents 1 to 3 are excellent technologies that have been put to practical use as surface-treated steel sheets that have undergone chromate-free surface treatments with excellent corrosion resistance. To improve the corrosion resistance of chromate-free treatments, technologies for forming a reaction layer containing the metal elements contained in the plating layer have been used, as described in Patent Documents 2 and 3. However, due to the increasing sophistication of customer needs in recent years, it has become clear that these prior art technologies sometimes lack sufficient corrosion resistance. For example, in the case of a galvanized steel sheet using a plating that does not contain Mg or Al, it is difficult to form the reaction layer as described in Patent Document 2 or 3, resulting in insufficient corrosion resistance in flat portions (planar portions) and processed portions. Also, in the case of a galvanized steel sheet using a plating that contains Mg or Al in the plating layer, when a chemical conversion coating (film) is formed in a continuous hot-dip galvanized steel sheet production line, from the viewpoint of productivity, the time from applying a chemical conversion treatment solution to the surface of the galvanized steel sheet to forming the chemical conversion coating by drying is extremely short, within 5 seconds. Therefore, since the Zn phase of the zinc alloy plating contains only small amounts of Mg and Al, it is difficult to form the reaction layer on the Zn phase of the plating, resulting in insufficient corrosion resistance. For these reasons, there is a demand for surface-treated steel sheets that have excellent corrosion resistance (white rust resistance) in both processed and flat areas. Furthermore, in order to facilitate processing of the surface-treated steel sheet into a complex shape, the surface-treated steel sheet preferably has excellent lubricity.

[0006] An object of the present invention is to provide a surface-treated steel sheet having excellent corrosion resistance and lubricity, based on the premise that the surface of a zinc-based plated steel material has a plating layer containing zinc or a zinc alloy on the surface of the steel material, and a chromate-free coating on the surface of the zinc-based plated steel material. [Means for solving the problem]

[0007] The corrosion resistance of surface-treated steel with a coating improves with the coating's barrier properties (its ability to block the penetration of corrosion factors such as moisture and chloride ions). Also, in areas where the coating is damaged by scratches or other defects, the greater the inhibitor effect, which prevents corrosion of the plating layer by dissolving substances (mainly metal elements) in the coating when moisture adheres to the coating, the better the corrosion resistance, including white rust resistance. As described above, the chemical conversion coatings disclosed in Patent Documents 1 to 3 are coatings that have both barrier properties and inhibitor effects. However, in environments where higher white rust resistance than conventional coatings is required, these properties are not sufficient, and there is a concern that the plating layer may corrode, resulting in the early formation of white rust. In view of these circumstances, the present inventors have investigated methods for improving the barrier properties and inhibitor effect of the coating. As a result, they discovered that when a coating is formed on the surface of a zinc-plated layer or zinc alloy-plated layer in a short time, the barrier properties of the coating can be improved and its corrosion resistance can be dramatically increased by controlling the concentration of each element from near the interface between the Zn phase of the zinc-plated layer or zinc alloy-plated layer and the coating to the surface of the coating, and by forming multiple areas where specific elements are concentrated.

[0008] The present invention has been made in light of the above findings. [1] A surface-treated steel sheet according to one aspect of the present invention is A base steel plate; a plating layer formed on the surface of the base steel sheet; a first coating formed on the surface of the plating layer; a second coating formed on the surface of the first coating and having a thickness of 0.6 μm or more; A surface-treated steel sheet having the Zn concentration of the plating layer is 40% by mass or more and 100% by mass or less, and the Mg concentration is 0% by mass or more and less than 4.0% by mass, When the concentrations of C, O, F, Mg, Al, Si, P, Ti, V, Zn, and Zr were continuously measured by line analysis in the thickness direction from the plating layer toward the surface of the coated steel sheet, a position where the Zn concentration first becomes 35.0 mass% or less is defined as a first interface, which is an interface between the plating layer and the first coating; a boundary region is a region including the first interface, the region being located between a range of 10 nm from the first interface toward the plating layer and a range of 15 nm from the first interface toward the first coating in the thickness direction; a second interface between the first coating and the second coating is defined as the position where the Zn concentration first becomes 3.0 mass % or less, and a range of 10 nm from the center between the first interface and the second interface in the thickness direction toward the second interface is defined as a central part of the first coating; When a region of the second coating between a position 400 nm and a position 410 nm from the second interface in the thickness direction is defined as a central portion of the second coating, One or more of the following formulas (1) to (3) and formulas (4) to (15) are satisfied. Dti≧5.0 (1) Dzr≧5.0 (2) Dv≧5.0 (3) Dti+Dzr+Dv≦25.0 (4) B1c<10.0 (5) B2c≧40.0 (6) 5.0 / M≦Amg≦25.0 (7) 0.5≦B1mg≦5.0 (8) 15.0 / M≦Af≦40.0 (9) 0.5≦B1f≦15.0 (10) Amg / B1mg≧2.0 (11) Af / B1f≧2.0 (12) B1si<5.0 (13) B1zn≧0.5 (14) B2zn<3.0 (15) wherein Dti is the maximum concentration of Ti in mass % in the first coating from the first interface to the center in the thickness direction between the first interface and the second interface, Dzr is a maximum concentration of Zr in mass % in the first coating from the first interface to the center in the thickness direction between the first interface and the second interface, Dv is the maximum concentration of V in mass % in the first coating from the first interface to the center in the thickness direction between the first interface and the second interface, B1c is the average concentration of C in mass % in the central portion of the first coating, B2c is the average concentration of C in mass % in the central portion of the second coating, A mg is the maximum concentration of Mg in mass % in the boundary region of the first coating, B1mg is the average concentration of Mg in mass% in the central portion of the first coating, Af is the maximum concentration of F in mass % in the boundary region of the first coating; B1f is the average concentration of F in mass % in the central portion of the first coating, B1si is the average concentration of Si in mass % in the central portion of the first coating, B1zn is the average concentration of Zn in mass % in the central portion of the first coating, B2zn is the average concentration of Zn in mass % in the central portion of the second coating, The M is a constant that is 1 when the Mg concentration of the plating layer is 0 mass % or more and less than 1.0 mass %, and is 2 when the Mg concentration is 1.0 mass % or more and less than 4.0 mass %. [2] The surface-treated steel sheet according to [1] may further satisfy the following formula (16): 0≦Cmg<5.0 (16) Here, Cmg is the Mg concentration in mass % at a position 10 nm from the first interface toward the plating layer in the thickness direction of the plating layer. [3] The surface-treated steel sheet according to [1] or [2] may further satisfy the following formulas (17) to (19). 5.0≦Aal≦20.0 (17) 0.2≦B1al≦5.0 (18) Aal / B1al≧5.0 (19) where Aal is the maximum concentration of Al in wt % in the boundary region; The B1al is the average concentration of Al in mass % in the central portion of the first coating. [4] The surface-treated steel sheet according to any one of [1] to [3] may further satisfy the following formulas (20) to (21). 10.0≦Ap≦25.0 (20) 0.5≦B1p≦8.0 (21) where Ap is the maximum concentration of P in the boundary region, B1p is the average concentration of P in mass % in the central portion of the first coating. [5] The surface-treated steel sheet according to any one of [1] to [4] may further satisfy the following formula (22): 1.0≦B1zn≦30.0 (22) [6] The surface-treated steel sheet according to any one of [1] to [5] may further satisfy the following formula (23): X2si / Y2si≧1.1 (23) where X2si is the maximum concentration, in mass %, of Si in a region extending from the surface of the second coating to 100 nm toward the second interface, The Y2si is the average concentration of Si in mass % in a region of the second coating that is 300 to 310 nm from the surface toward the second interface. [7] The surface-treated steel sheet according to any one of [1] to [6] may further satisfy the following formula (24): Af / B1f≧2.5 (24) [Effects of the Invention]

[0009] According to the above aspect of the present invention, it is possible to provide a surface-treated steel sheet having excellent corrosion resistance and lubricity. [Brief explanation of the drawings]

[0010] [Figure 1] 1 is a schematic diagram showing an example of a cross section of a surface-treated steel sheet according to an embodiment of the present invention. [Figure 2] FIG. 1 shows an example of the results of elemental analysis in the thickness direction obtained using an FE-TEM equipped with an energy dispersive X-ray analyzer. DETAILED DESCRIPTION OF THE INVENTION

[0011] A surface-treated steel sheet according to one embodiment of the present invention (a surface-treated steel sheet according to this embodiment) will be described. In the following numerical ranges defined by "to" (to be described later), the values ​​at both ends are included as the lower and upper limits of the range. On the other hand, values ​​indicated as "greater than" or "less than" are not included in the numerical range. Furthermore, all ratios (for example, Amg / B1mg, which is the ratio of Amg to B1mg described later) are dimensionless units. As shown in FIG. 1, the surface-treated steel sheet 1 according to this embodiment has a base steel sheet 10, a plating layer 20 formed on the surface of the base steel sheet 10, a first coating 30 formed on the surface of the plating layer 20, and a second coating 40 formed on the surface of the first coating 30. In the surface-treated steel sheet 1 according to this embodiment, the plating layer 20 is a zinc plating layer or a zinc alloy plating layer containing 0% by mass or more and less than 4.0% by mass of Mg (the Mg concentration is 0% by mass or more and less than 4.0% by mass). In addition, in the present embodiment, when the concentrations (concentration distribution) of C, O, F, Mg, Al, Si, P, Ti, V, Zn, and Zr are continuously measured by line analysis in the thickness direction from the plating layer toward the surface of the surface-treated steel sheet, the position where the Zn concentration first becomes 35.0 mass% or less is defined as the first interface 25, which is the interface between the plating layer and the first coating 30. Furthermore, the region including the first interface 25 and extending from the first interface 25 in the thickness direction between a range of 10 nm on the plating layer 20 side and a range of 15 nm on the first coating 30 side is defined as boundary region A. In other words, boundary region A is a 25 nm region in the thickness direction spanning both the plating layer 20 and the first coating 30 across the interface. Furthermore, the position where the Zn concentration first becomes 3.0 mass % or less as a result of the above line analysis is defined as the second interface 35, which is the interface between the first coating 30 and the second coating 40. The plating layer 20, the first coating 30, and the second coating 40 may be formed on one side or both sides of the base steel sheet 10. The first coating 30 and the second coating 40 are, for example, chemical conversion coatings.

[0012] The X-ray analysis is carried out using a FE-TEM (Field Emission-Transmission Electron Microscope) equipped with an energy dispersive X-ray analyzer, for example, under the following conditions. Test specimens were cut from the coated steel sheets using the cryo-FIB (Focused Ion Beam) method, and the cross-sectional structure of the cut specimens was observed using a transmission electron microscope (TEM) at a magnification (100,000 to 1,000,000 times) that allowed the entire coating and part of the Zn phase of the coating layer to be seen within the observation field. To identify the constituent elements of each layer, TEM-EDS (Energy Dispersive X-ray Spectroscopy) was used to perform elemental analysis of the entire field of view in the thickness direction by line analysis, and the concentrations of C, O, F, Mg, Al, Si, P, Ti, V, Zn, and Zr were continuously measured at each position from the coating layer to the surface of the coated steel sheet. An accelerating voltage of 200 kV was used for observation and EDS analysis. When observed with FE-TEM, the plating layer is clearly different from the coating, so it can be observed with FE-TEM and a position that is clearly different from the coating can be determined to be the plating layer. The starting point for line analysis can be, for example, any position on the plating layer observed with FE-TEM. Furthermore, even if the plating layer cannot be clearly identified by FE-TEM observation, if, for example, the Zn concentration is 85 mass% or more and both the Mg concentration and the Al concentration are 1.0 mass% or less at the starting point of EDS line analysis, that starting point is definitely the plating layer, so there is no need to repeat FE-TEM observation or EDS line analysis. The end point for line analysis is the surface of the coating (the surface of the coated steel sheet).

[0013] Line analysis is also possible using EPMA, but since EPMA does not allow observation at a higher magnification than TEM, it may not be possible to analyze with high precision the concentration distribution of each element in the coating of the surface-treated steel sheet according to this embodiment. Therefore, in this embodiment, line analysis is performed using an FE-TEM equipped with an energy dispersive X-ray analyzer.

[0014] The base steel sheet 10, the plating layer 20, the first coating 30, and the second coating 40 will be described below.

[0015] <Base material steel plate> The surface-treated steel sheet according to this embodiment has excellent corrosion resistance due to the plating layer and coating. Therefore, the base steel sheet is not particularly limited. The base steel sheet may be determined based on the product to which it is applied, the required strength, plate thickness, etc. For example, hot-rolled mild steel sheets and steel strips, or hot-rolled steel sheets and steel strips for automotive structures (sometimes collectively referred to as hot-rolled steel sheets) described in JIS G 3131:2018 or JIS G 3113:2018, or cold-rolled steel sheets and steel strips, or automotive workable cold-rolled high-tensile steel sheets and steel strips (sometimes collectively referred to as cold-rolled steel sheets) described in JIS G 3141:2021 or JIS G 3135:2018, may be used.

[0016] <Plating layer> The coating layer of the surface-treated steel sheet according to this embodiment has a chemical composition in which the zinc (Zn) concentration (content) is 40% by mass or more and 100% by mass or less, and the Mg concentration (content) is 0% by mass or more and less than 4.0% by mass. The coating layer is a zinc coating layer or a zinc alloy coating layer. The elements other than Zn and Mg are not limited, but for example, in mass %, Al: 0% or more, less than 25.0% Sn: 0% or more, 20% or less, Bi: 0% or more, less than 5.0% In: 0% or more, less than 2.0% Ca: 0% or more, 3.0% or less, Y: 0% or more, 0.5% or less, La: 0% or more, less than 0.5% Ce: 0% or more, less than 0.5% Si: 0% or more, less than 2.5% Cr: 0% or more, less than 0.25% Ti: 0% or more, less than 0.25% Ni: 0% or more, less than 0.25% Co: 0% or more, less than 0.25% V: 0% or more, less than 0.25% Nb: 0% or more, less than 0.25% Cu: 0% or more, less than 0.25% Mn: 0% or more, less than 0.25% Fe: 0% or more, 5.0% or less, Sr: 0% or more, less than 0.5% Sb: 0% or more, less than 0.5% Pb: 0% or more, less than 0.5% B: 0% or more and less than 0.5%, and Remainder: impurities may be. All elements other than Zn, including Mg and Al, are optional, with the lower limit being 0%. In other words, the chemical composition of the coating layer may consist only of Zn and impurities. If necessary, the Mg concentration may be 0.1% or more, 0.5% or more, or 1.0% or more, and the Mg concentration may be 3.5% or less, 3.0% or less, or 2.5% or less. If necessary, the Al concentration may be 0.1% or more, 0.2% or more, 1.0% or more, or 4.0% or more, and the Al concentration may be 21.0% or less, 17.0% or less, or 12.0% or less. If necessary, the Zn concentration may be 50% or more, 60% or more, 70% or more, 80% or more, or 85% or more, and the Zn concentration may be less than 100%, less than 99%, less than 97%, or less than 95%. The total concentration of impurities is preferably less than 1.0%.

[0017] The chemical composition of the plating layer can be determined by dissolving the plating layer in, for example, a 10% HCl aqueous solution containing an inhibitor that suppresses corrosion of the base steel (base steel sheet) (for example, IBIT manufactured by Asahi Chemical Industry Co., Ltd.), and then performing composition analysis using ICP atomic emission spectrometry.

[0018] There is no limit to the amount of plating applied, but to improve corrosion resistance, it is recommended that the coating weight be 10 g / m per side. 2 On the other hand, the amount of adhesion per side is preferably 200 g / m or more. 2 If the coating weight exceeds 200g / m, the corrosion resistance will saturate and it will be economically disadvantageous. 2 It is preferable that:

[0019] The type of the plated layer is not limited, and may be, for example, a hot-dip plated layer or an electroplated layer.

[0020] <First coating> In the surface-treated steel sheet according to this embodiment, the first coating is present on the plating layer (the surface opposite to the base steel sheet), i.e., between the plating layer and the second coating. The first coating is also sometimes called a surface treatment coating or an underlayer coating. In this embodiment, the range in the thickness direction starting from the center position between the interface (first interface) between the plating layer and the first coating and the interface (second interface) between the first coating and the second coating and ending at a position 10 nm toward the second interface is referred to as the central portion B1 of the first coating. As will be described later, the first coating is a coating formed by applying a chemical conversion treatment liquid prepared by adding phosphoric acid and nitric acid to an aqueous solution containing any of Ti, Zr, and V, Mg, and F, and drying the solution. The first coating contains any of Ti, Zr, and V, Mg, and F, and may also contain P and Si.

[0021] In the first coating provided on the surface-treated steel sheet according to this embodiment (first coating according to this embodiment), in the region from the first interface to the center between the first and second interfaces, when the maximum concentration in mass% of Ti is Dti (unit: mass%), the maximum concentration in mass% of Zr is Dzr (unit: mass%), and the maximum concentration in mass% of V is Dv (unit: mass%), one or more selected from Dti, Dzr, and Dv are 5.0% or more, and the total of one or more is 25.0% or less. In this case, the barrier property of the coating is improved. If each value becomes too high, the coating becomes brittle and the barrier properties deteriorate, so the total of Dti, Dzr, and Dv is preferably 20.0% or less. That is, the surface-treated steel sheet according to this embodiment satisfies one or more of formulas (1) to (3) and also formula (4). Dti≧5.0 (1) Dzr≧5.0 (2) Dv≧5.0 (3) Dti+Dzr+Dv≦25.0 (4)

[0022] In the first coating according to this embodiment, the average C concentration B1c (unit: mass %) in the central portion B1 of the first coating described above is less than 10.0%. If B1c is 10.0% or more, the barrier properties of the coating are reduced, resulting in poor corrosion resistance. Furthermore, the first coating is substantially free of organic resin (1 mass % or less). There is no simple measurement method for confirming that the organic resin content is 1 mass % or less through analysis of the first coating. However, as the amount of organic resin in the surface treatment solution increases, the C concentration in the coating increases. For this reason, in this embodiment, B1c is set to less than 10.0% as an indicator that the organic resin content is 1 mass % or less. That is, the surface-treated steel sheet according to this embodiment satisfies the following formula (5). B1c<10.0 (5) To obtain excellent corrosion resistance, B1c is preferably 6.0% or less, 4.5% or less, or 3.0% or less. Since there is no lower limit for B1c, the lower limit for Bc is 0%. If necessary, B1c may be 0.5% or more, 1.0% or more, or 1.5% or more.

[0023] Furthermore, in the first coating according to this embodiment, the maximum Mg concentration Amg (unit: mass %) in the boundary region A is 2.5 to 25.0%, the average Mg concentration B1mg (unit: mass %) in the central portion B1 of the first coating is 0.5 to 5.0%, and the ratio of Amg to B1mg, Amg / B1mg, is 2.0 or greater. In other words, Mg is concentrated near the first interface. Having a predetermined amount of Mg contained and Mg concentrated near the first interface improves the barrier properties of the coating and improves corrosion resistance. If Amg is less than 2.5%, B1mg is less than 0.5%, or Amg / B1mg is less than 2.0, the effect of improving corrosion resistance cannot be sufficiently obtained. However, if the Mg concentration of the coating layer is less than 1.0 mass%, an Amg of less than 5.0% will not be effective. This is thought to be because, since the volume ratio of Zn in the coating structure is large, in order to suppress the occurrence of white rust, it is necessary to form a Mg-enriched layer that is stronger than a coating layer containing more Mg. Therefore, when the Mg concentration of the coating layer is 0 mass% or more and less than 1.0 mass%, Amg is 5.0 to 25.0%. On the other hand, if Amg exceeds 25.0%, the adhesion between the plating layer and the first coating decreases, resulting in a decrease in corrosion resistance.If Bmg exceeds 5.0%, Mg-enriched areas are not formed, resulting in a decrease in corrosion resistance. That is, the surface-treated steel sheet according to this embodiment satisfies the following formulas (7), (8), and (11). 5.0 / M≦Amg≦25.0 (7) 0.5≦B1mg≦5.0 (8) Amg / B1mg≧2.0 (11) Here, M is a constant that is 1 (i.e., M=1) when the Mg concentration in the chemical composition of the plating layer is 0% or more and less than 1.0% by mass, and is 2 (i.e., M=2) when the Mg concentration is 1.0% or more and less than 4.0% by mass. If necessary, Amg may be set to 20.0% or less, 15.0% or less, 12.0% or less, 10.0% or less, or 8.0% or less. In particular, only when the Mg concentration in the chemical composition of the plating layer is 1.0% by mass or more and less than 4.0% by mass, the upper limit of Amg may be limited, for example, to 12.0% or less, 10.0% or less, 8.0% or less, or 6.0% or less. Furthermore, B1mg may be set to 4.0% or less, 3.0% or less, or 2.0% or less, as needed. There is no particular need to set an upper limit for A mg / B mg, but A mg / B mg may be 20.0 or less, 15.0 or less, or 10.0 or less. If necessary, A mg / B mg may be 2.5 or more, 3.5 or more, or 4.5 or more.

[0024] F is also an element that enhances the barrier properties of the coating, and like Mg, it is contained in a predetermined amount in the first coating and concentrated near the first interface. Specifically, in the first coating, the maximum F concentration Af (unit: mass %) in the boundary region A is 7.5 to 40.0%, the average F concentration B1f (unit: mass %) in the central portion B1 of the first coating is 0.5 to 15.0%, and the ratio of Af to B1f, Af / B1f, is 2.0 or greater. Preferably, Af / B1f is 2.5 or greater. If Af is less than 7.5%, B1f is less than 0.5%, or Af / B1f is less than 2.0, the effect of improving corrosion resistance cannot be sufficiently obtained. However, when the Mg concentration of the coating layer is less than 1.0 mass%, no effect can be obtained if Af is less than 15.0%. This is thought to be because, since the volume ratio of Zn in the coating structure is large, in order to suppress the occurrence of white rust, it is necessary to form a stronger F-enriched layer than a coating layer with a higher Mg content. Therefore, when the Mg concentration of the coating layer is 0 mass% or more and less than 1.0 mass%, Af is 15.0 to 40.0%. On the other hand, if Af exceeds 40.0%, excess F impairs the barrier properties and reduces corrosion resistance, and if B1f exceeds 15.0%, no F-enriched areas are formed, and excellent corrosion resistance cannot be obtained. That is, the surface-treated steel sheet according to this embodiment satisfies the following formulas (9), (10), and (12). 15.0 / M≦Af≦40.0 (9) 0.5≦B1f≦15.0 (10) Af / B1f≧2.0 (12) Here, M is a constant that is 1 (i.e., M=1) when the Mg concentration in the chemical composition of the plating layer is 0% or more and less than 1.0%, and is 2 (i.e., M=2) when the Mg concentration is 1.0% or more and less than 4.0%. Preferably, the following formula (24) is satisfied. Af / B1f≧2.5 (24) If necessary, Af may be set to 38.0% or less, 35.0% or less, 30.0% or less, 25.0% or less, or 20.0% or less. In particular, only when the Mg concentration in the chemical composition of the plating layer is 1.0 mass% or more and less than 4.0 mass%, the upper limit of Af may be limited, for example, Af may be set to 25.0% or less, 20.0% or less, 16.0% or less, or 12.0% or less. Furthermore, B1f may be set to 12.0% or less, 10.0% or less, or 7.5% or less, as required. There is no particular need to set an upper limit for Af / B1f, but Af / B1f may be 50.0 or less, 30.0 or less, 20.0 or less, or 10.0 or less. If necessary, Af / B1f may be 3.0 or more, 3.5 or more, or 4.5 or more.

[0025] In the first coating according to this embodiment, the average Si concentration B1si (unit: mass %) in the central portion B1 of the coating is less than 5.0%. If B1si is 5.0% or more, a coating with barrier properties will not be formed and corrosion resistance will decrease. From the viewpoint of improving corrosion resistance, B1si is more preferably 2.0% or less. That is, in the first coating according to this embodiment, when the average concentration of Si in the central portion B1 of the first coating is Bsi (unit: mass %), the following formula (13) is satisfied. B1si<5.0 (13) If necessary, B1si may be set to 1.5% or less, 1.0% or less, or 0.5% or less. Although the lower limit of B1si is 0%, B1si may be set to 0.1% or more.

[0026] The first coating film contains Zn, which improves corrosion resistance. In the first coating film according to this embodiment, if B1zn (unit: mass %), which is the average concentration of Zn in the central portion B1 of the first coating film, is less than 0.5%, the effect of improving corrosion resistance due to Zn is not sufficiently obtained. Therefore, in the first coating film according to this embodiment, B1zn is 0.5% or more. In other words, the surface-treated steel sheet according to this embodiment satisfies the following formula (14). B1zn≧0.5 (14) B1Zn is preferably 1.0% or more. On the other hand, if B1Zn exceeds 30.0%, corrosion resistance is slightly reduced, so B1Zn is preferably set to 30.0% or less. If necessary, B1Zn may be set to 25.0% or less, 21.0% or less, or 18.0% or less, or may be set to 1.0% or more, 2.0% or more, 3.5% or more, or 5.0% or more.

[0027] In the surface-treated steel sheet according to this embodiment, it is preferable that the maximum Al concentration in mass % in the boundary region A, Aal (unit: mass %), is 5.0 to 20.0%, the average Al concentration in mass % in the central portion B1 of the first coating, B1al (unit: mass %), is 0.2 to 5.0%, and the ratio of Aal to B1al, Aal / B1al, is 5.0 or more. That is, the surface-treated steel sheet according to this embodiment preferably satisfies the following formulas (17) to (19). 5.0≦Aal≦20.0 (17) 0.2≦B1al≦5.0 (18) Aal / B1al≧5.0 (19) In this case, the corrosion resistance (white rust resistance) is improved. Although there is no upper limit for Al, taking into consideration the Al concentration in the plating layer, Al may be set to 20.0% or less or 15.0% or less, or may be set to 0.5% or more, 1.0% or more, 3.0% or more, 7.0% or more, or 10.0% or more. B1al may be set to 3.0% or less, 2.0% or less, or 1.0% or less, and B1al may be set to 0.1% or more, or 0.3% or more. There is no particular need to set an upper limit for Aal / Bal, but Aal / Bal may be 80.0 or less, 60.0 or less, or 30.0 or less. If necessary, Aal / Bal may be 7.0 or more, 10.0 or more, or 15.0 or more.

[0028] It is also preferable that the maximum concentration of P in the boundary region A, Ap (unit: mass %), is 10.0 to 25.0%, and the average concentration of P in the central portion B1 of the first coating, B1p (unit: mass %), is 0.5 to 8.0%. That is, the surface-treated steel sheet according to this embodiment preferably satisfies the following formulas (20) and (21). 10.0≦Ap≦25.0 (20) 0.5≦B1p≦8.0 (21) In this case, the corrosion resistance is improved.

[0029] The amount of the first coating is 150 to 800 mg / m 2 The coating amount is preferably 150 mg / m 2 If the coating weight is less than 800 mg / m, corrosion resistance may decrease. 2 If it exceeds 10 ...

[0030] Furthermore, it is preferable that the Mg concentration in mass % Cmg at the position in the boundary region A closest to the plating layer (a position 10 nm from the first interface toward the plating layer in the thickness direction) is 0% or more and less than 5.0%. That is, the surface-treated steel sheet according to this embodiment preferably satisfies the following formula (16). 0≦Cmg<5.0 (16) In this case, cracks in the plating caused by processing are reduced, improving the corrosion resistance of the processed portion.

[0031] <Second coating> The second coating film (second coating film according to the present embodiment) provided on the surface-treated steel sheet according to the present embodiment is present on the surface of the first coating film (the surface opposite to the plating layer). The second coating film is also called a resin coating film, an organic resin coating film, a coating film, or the like. The second coating film can also be called an upper layer coating film. In the surface-treated steel sheet according to this embodiment, the region of the second coating between positions 400 nm and 410 nm from the second interface in the thickness direction is referred to as a central portion B2 of the second coating. In the second coating according to this embodiment, the average concentration B2c (unit: mass %) of C in the central portion B2 of the second coating is 40.0% or more. That is, the surface-treated steel sheet according to this embodiment satisfies the following formula (6). B2c≧40.0 (6) If B2c is less than 40.0%, corrosion resistance and lubricity cannot be obtained. If necessary, B2c may be 45.0% or more, 50.0% or more, or 55.0% or more. There is no upper limit for B2c, but from the viewpoint of lubricity, B2c may be 90.0% or less, 85.0% or less, 80.0% or less, or 75.0% or less.

[0032] In the second coating according to this embodiment, the amount of Zn diffused from the plating layer is small, and the average Zn concentration B2zn (unit: mass %) in the central portion B2 of the second coating is less than 3.0%. That is, the surface-treated steel sheet according to this embodiment satisfies the following formula (15). B2zn<3.0 (15)

[0033] Furthermore, in the second coating, when the maximum Si concentration in the region from the surface to a depth of 100 nm is X2si (unit: mass %) and the average Si concentration in the region from the surface of the second coating to a depth of 300 to 310 nm is Y2si (unit: mass %), it is preferable that the ratio of X2si to Y2si, X2si / Y2si, be 1.1 or greater. Increasing the Si concentration near the surface of the second coating (i.e., near the surface of the coated steel sheet) improves the barrier properties of the coating, improving corrosion resistance, and also increases the surface hardness, improving lubricity. That is, the surface-treated steel sheet according to this embodiment preferably satisfies the following formula (23). X2si / Y2si≧1.1 (23) There is no need to set an upper limit for X2si / Y2si, but X2si / Y2si may be set to 10.0 or less, 5.0 or less, 3.0 or less, 2.0 or less, or 1.5 or less. X2si / Y2si may be set to 1.2 or more, or 1.3 or more.

[0034] The thickness of the second coating (film thickness) is 0.6 μm or more. If the film thickness is less than 0.6 μm, the target corrosion resistance and lubricity will not be achieved. Preferably, it is 0.7 μm or more or 0.8 μm or more, and more preferably 1.0 μm or more. There is no upper limit, but a thickness exceeding 5.0 μm is not preferred because it increases costs. Therefore, the thickness of the second coating may be 5.0 μm or less, and may be 4.0 μm or less, 3.0 μm or less, or 2.0 μm or less, as necessary.

[0035] The above-mentioned B1c, B2c, Amg, B1mg, Af, B1f, B1si, Cmg, Aal, B1al, Ap, B1p, B1zn, B2zn, X2si, Y2si, Dti, Dzr, Dv, etc. are determined from the results of measurement by line analysis using the above-mentioned FE-TEM equipped with an energy dispersive X-ray analyzer.

[0036] <Manufacturing method> Next, a preferred method for producing the surface-treated steel sheet according to this embodiment will be described. The surface-treated steel sheet according to this embodiment can obtain the effects as long as it has the above-mentioned characteristics regardless of the manufacturing method, but the manufacturing method described below is preferred because it can be manufactured stably.

[0037] That is, the surface-treated steel sheet according to this embodiment can be produced by a production method including the following steps. (I) a plating step of forming a plating layer containing zinc or a zinc alloy on the surface of a steel sheet; (II) a first coating formation step of applying a chemical conversion treatment solution to a steel sheet having a plating layer, and heating and drying the solution to form a first coating; (III) A second coating formation step of applying a chemical conversion treatment solution to the surface of the steel sheet having the plating layer and the first coating, and then heating and drying the solution to form a second coating.

[0038] [Plating process] In the plating process, a steel material such as a steel sheet is immersed in a plating bath containing Zn or a Zn alloy, or is electroplated to form a plating layer on the surface. The method for forming the plating layer is not particularly limited; it may be performed by a conventional method that ensures sufficient plating adhesion. The steel sheet to be subjected to the plating step and its manufacturing method are not limited. For example, the steel sheet to be immersed in the plating bath may be a hot-rolled mild steel sheet and steel strip described in JIS G 3131:2018 or JIS G 3113:2018, or a hot-rolled steel sheet and steel strip for automotive structures, or a cold-rolled steel sheet and steel strip described in JIS G 3141:2021 or JIS G 3135:2018, or a workable cold-rolled high-tensile steel sheet and steel strip for automotive use. The composition of the plating bath may be adjusted depending on the chemical composition of the plating layer to be obtained. After the steel material is pulled out of the plating bath, the coating weight of the plating layer can be adjusted by wiping, if necessary. When Cmg is set to 0% or more and less than 5.0%, the Mg concentration in the plating layer is preferably set to 0% by mass or more and 3.0% by mass or less. When Aal / B1al is set to 5.0 or more, the Al concentration in the plating layer is preferably set to 0.1 mass % or more.

[0039] [First film formation process] In this process, a treatment liquid (chemical conversion treatment liquid) is applied to a steel sheet having a plating layer, and then heated and dried to form a first coating. When forming the first coating according to this embodiment, the chemical conversion treatment liquid is an aqueous solution containing any one of Ti, Zr, and V, Mg, and F, and optionally containing Si, to which phosphoric acid and nitric acid are further added. By applying such a treatment solution, it is possible to concentrate specific elements at the interface between the plating layer and the chemical conversion coating. Specifically, the concentrations of each element and the concentrations of phosphoric acid and nitric acid in the treatment solution are set as follows: Here, the concentrations of phosphoric acid and nitric acid do not include the concentrations of phosphates, nitrates, etc. By simultaneously including phosphoric acid and nitric acid within the above ranges, the dissolution of the plating proceeds and specific substances become concentrated at the interface between the coating and the plating, greatly improving the effect of improving adhesion. One or more of Ti, V, and Zr: 5.0 to 20.0 g / L Mg: 0.7-7.0g / L F: 14.4-46.1g / L P: 6.8-32.9g / L Si: 0.0 to 0.4 g / L Phosphoric acid: 10.0 to 80.0 g / L Nitric acid: 5.0~40.0g / L When Ap and B1p are to be within the predetermined ranges, it is preferable that the P concentration in the chemical conversion treatment solution be 10.0 g / L or more.

[0040] Furthermore, when B1zn is set to 1.0 to 30.0% to improve corrosion resistance, it is preferable to control the contact time between the chemical conversion treatment solution and the plated steel sheet when applying the chemical conversion treatment solution using a roll coater, thereby setting the Zn concentration in the treatment solution to 0.5 to 5.0 g / L by mass. The Zn concentration can be adjusted by immersing the plated steel sheet in the treatment solution or by adding Zn powder. To increase B1zn, Zn powder or a Zn compound may be added to the chemical conversion treatment solution. Even when Zn powder or a Zn compound is not added to the chemical conversion treatment solution, Zn diffuses from the plating layer, so B1zn often does not reach 0%.

[0041] Examples of magnesium that can be contained in the chemical conversion treatment solution include magnesium fluoride, magnesium nitrate, magnesium sulfate, magnesium chloride, and magnesium acetate.

[0042] Examples of F contained in the chemical conversion treatment solution include fluorine compounds such as hydrofluoric acid HF, fluoroboric acid BF4H, hydrosilicic acid H2SiF6, fluorozirconic acid H2ZrF6, and hydrofluoric titanic acid H2TiF6. One or more compounds may be used. Among these, hydrofluoric acid is more preferred. When hydrofluoric acid is used, better corrosion resistance and paintability can be obtained.

[0043] When Zr is contained in the chemical conversion treatment solution, examples of Zr compounds include ammonium zirconium carbonate, hexafluorozirconic acid, and ammonium hexafluorozirconium. When V is contained, examples of V compounds include vanadium pentoxide VO, metavanadate HVO, ammonium metavanadate, sodium metavanadate, vanadium oxytrichloride VOCl, vanadium trioxide VO, vanadium dioxide VO, vanadium oxysulfate VOSO, vanadium oxyacetylacetonate VO(OC(=CH)CHCOCH)), vanadium acetylacetonate V(OC(=CH)CHCOCH), vanadium trichloride VCl, and vanadomolybdic acid. It is also possible to use a pentavalent vanadium compound reduced to a tetravalent or divalent vanadium compound using an organic compound having at least one functional group selected from the group consisting of a hydroxyl group, a carbonyl group, a carboxyl group, primary to tertiary amino groups, an amide group, a phosphate group, and a phosphonate group. When Ti is contained, examples of Ti compounds include ammonium hexafluorotitanate, titanium hydrofluoric acid, and titanium nitrate.

[0044] There are no limitations on the method for applying the chemical conversion treatment solution, and it can be applied using, for example, a roll coater, a bar coater, a sprayer, or the like.

[0045] After the chemical conversion treatment liquid is applied, it is heated to the maximum heating temperature (maximum temperature reached (PMT)) within 5 seconds after application and dried. The average heating rate until it reaches (PMT - 10°C) is preferably 5 to 50°C / s. To achieve an Aal / B1al ratio of 5.0 or greater, it is preferable to use two-stage heating, with the rate of temperature rise in the latter half being faster than the rate of temperature rise in the first half. Specifically, if the time from the start of heating to the temperature reaching a temperature 10°C lower than the maximum heating temperature (PMT) (PMT-10°C) is defined as t, then the average rate of temperature rise V2 in the latter half from the start of heating to 0.5t to 1.0t is preferably 1.25 times or greater than the average rate of temperature rise V1 in the first half from the start of heating to 0.5t, i.e., V2 / V1≧1.25. Furthermore, when two-stage heating is used to achieve an Aal / B1al ratio of 5.0 or greater, it is preferable that the rate of temperature rise V1 in the first half be 5°C / s or greater. Furthermore, if the furnace time for heating and drying is long, F tends to concentrate near the interface, resulting in a larger Af / B1f. For example, if the furnace time is set to 15 seconds or longer, the Af / B1f can be set to 2.5 or higher. Furthermore, when heating, it is preferable to spray the paint onto the steel plate through a punched metal (a steel plate having a plurality of through holes).

[0046] [Second film formation process] In this step, a chemical conversion treatment liquid is further applied to the surface of the steel sheet on which the first coating has been formed, and the surface is heated and dried to form a second coating. In this process, a treatment liquid containing 70.0% or more of an organic resin is used so that B2c is 40.0% or more. The organic resin is, for example, a urethane resin. In addition, to improve lubricity, 2.0 to 10.0% of colloidal silica is added. Furthermore, 0.1 to 2.0% of wax may be contained.

[0047] There are no limitations on the method for applying the chemical conversion treatment solution, and it can be applied using, for example, a roll coater, a bar coater, a sprayer, or the like.

[0048] After applying the treatment liquid, it is heated and dried. The PMT is set to 100 to 250°C. To increase the Si concentration at the outermost surface, it is preferable to set the PMT to 160° C. or higher and the heating rate to the PMT to 8° C. / sec or less. In this case, the colloidal silica contained in the treatment liquid is concentrated at the outermost surface of the coating, increasing the Si concentration at the outermost surface. [Example]

[0049] A metal sheet (plated steel sheet) having a plating layer composition shown in Table 1 was prepared. The coating weight of the plating layer was 70 g / m 2 Metal plate No. 1 was produced by electroplating, Nos. 2 to 8 by hot-dip galvanizing, and No. 4 by heat treatment (alloying treatment) after hot-dip galvanizing. In Table 1, for example, 99.6% Zn-0.2% Al indicates a composition containing 99.6% Zn and 0.2% Al, and similarly for other compositions. The remainder of the plating layer composition is impurities. The substrate of the plated steel sheet was a cold-rolled steel sheet satisfying JIS G3141:2021.

[0050] [Table 1]

[0051] These plated steel sheets were coated with chemical conversion treatment solutions having the compositions shown in Tables 4-1, 4-2, and 5. However, for No. 49 and No. 118, the chemical conversion treatment solution contained 1.1% by weight of polyurethane resin as the organic resin component. The element concentrations in the chemical conversion treatment solution are (NH4)2TiF6, (NH4)2ZrF6, V2O5, MgHPO4·3H2O, H3PO4, NH4F, HNO3, Ca(NO3)2·4H2O, C5H 12 The thickness was adjusted by mixing O3Si (vinyltrimethoxysilane) as needed. The chemical conversion treatment solution was applied using a roll coater. Within 5 seconds after applying the chemical conversion treatment solution, hot air was blown onto the steel plate through a punched metal (a steel plate with multiple through holes) to heat the steel plate to the dry plate temperature (PMT) shown in Tables 4-1, 4-2, and 5 under the conditions shown in Tables 4-1, 4-2, and 5, and then the steel plate was cooled to 20°C by air-cooling by blowing air through the punched metal or by water-cooling, thereby forming a first coating (chemical conversion treatment coating). The amount of the first coating was 600 mg / m for No. 41. 2 , No. 42 is 800 mg / m 2 and 400 mg / m 2 It was decided.

[0052] Then, a treatment solution containing 600 g / L of water-dispersed urethane resin (ADEKA BONTITOR HUX-830), 100 g / L of colloidal silica, and 10 g / L of polyethylene wax emulsion (HI-TEC E manufactured by Toho Chemical Industry Co., Ltd.) was applied to the first coating using a roll coater, and the first coating was heated to 160°C (drying temperature) at an average heating rate of 16°C / sec. After heating, the first coating was air-cooled to obtain surface-treated steel sheets Nos. 1 to 51 and 101 to 120, each of which had a second coating containing urethane resin. On the other hand, for No. 52 and No. 53, the above treatment was not carried out and the second coating was not formed.

[0053] [Table 2-1]

[0054] [Table 2-2]

[0055] [Table 3]

[0056] [Table 4-1]

[0057] [Table 4-2]

[0058] [Table 5]

[0059] Test specimens were cut out from the prepared chemical conversion coated steel sheets using a cooled focused ion beam (FIB) processing method, and the cross-sectional structure of the cut out test specimens was observed using a field emission-transmission electron microscope (FE-TEM) equipped with an energy dispersive X-ray analyzer at a magnification such that the entire first chemical conversion coating and the plating layer were visible in the observation field. Since Al, MgZn2, and Zn phases were present in the coating layer, the Zn phase was identified by contrast (the relatively bright portion of the dark-field image was determined to be the Zn phase). EDS analysis showed that the Zn concentration in the Zn phase was 85% by mass or more and both the Mg and Al concentrations were 1.0% by mass or less. The concentration distributions of C, O, F, Mg, Al, Si, P, Ti, V, Zn, and Zr from the position confirmed to be the coating layer to the surface of the coated steel sheet (the surface of the second chemical conversion coating) were measured using an energy dispersive X-ray analyzer. The results are shown in Tables 6-1 to 9. FIG. 2 shows the results of measuring the element distribution in the depth direction for Example Test No. 41.

[0060] [Table 6-1]

[0061] [Table 6-2]

[0062] [Table 7]

[0063] [Table 8-1]

[0064] [Table 8-2]

[0065] [Table 9]

[0066] The corrosion resistance of the flat surface, corrosion resistance of the processed portion, and lubricity of the prepared chemical conversion treated steel sheets were evaluated as follows. The results are shown in Tables 10-1, 10-2, and 11.

[0067] <Corrosion resistance on flat surfaces> A neutral salt spray test conforming to JIS Z 2371:2015 was conducted on flat test specimens (rectangular test specimens measuring 70mm x 150mm) at a salt concentration of 70g ± 5g / L for 120, 240, and 360 hours, and corrosion resistance was evaluated based on the occurrence of white rust (area ratio) on the test specimens after the test. The evaluation criteria for corrosion resistance are shown below. If the specimen was SS after 240 hours, it was determined to have sufficient corrosion resistance. (Corrosion resistance evaluation criteria) SS: 5% or less S: More than 5%, less than 10% A: More than 10%, less than 30% B: More than 30%, less than 50% C: More than 50%

[0068] <Corrosion resistance of processed parts (white rust resistance)> The center of a flat test piece (a rectangular test piece measuring 70 mm x 150 mm) was subjected to an Erichsen test (7 mm extrusion), and then a salt spray test according to JIS Z 2371:2015 was carried out for 72 hours, and the occurrence of white rust on the extruded part was observed. The evaluation criteria were the same as for the flat part corrosion resistance, and a result of SS or S was considered to have sufficient corrosion resistance. (Corrosion resistance evaluation criteria) SS: 5% or less S: More than 5%, less than 10% A: More than 10%, less than 30% B: More than 30%, less than 50% C: More than 50%

[0069] <Lubricity> Using a HEIDON-14 (manufactured by Shinto Scientific Co., Ltd.), a 10 mm diameter stainless steel ball was used as a slider, sliding across the surface of the flat test piece at a load of 1.0 N and a sliding speed of 150 mm / min. The coefficient of dynamic friction μ was calculated from the resulting stress to evaluate lubricity. The lubricity evaluation criteria are as follows: S and AA were considered to have sufficient lubricity. (Lubricity evaluation criteria) S: 0.1 or less AA: More than 0.1%, less than 0.2% A: More than 0.2%, less than 0.5% B: More than 0.5%

[0070] [Table 10-1]

[0071] [Table 10-2]

[0072] [Table 11]

[0073] As can be seen from Tables 1 to 11, when a zinc plating layer or zinc alloy plating layer containing a predetermined amount of Mg was included, a first coating, and a second coating, and Ti, V, Zr, C, Mg, F, and Si were present at predetermined concentrations and concentrated in predetermined regions from the plating layer to the second coating (invention examples), the corrosion resistance and lubricity were excellent. On the other hand, the comparative examples (Nos. 24 to 40, 44 to 50, 52, 53, 107 to 119) which did not have a second coating or in which the concentrations or enrichment states of Ti, V, Zr, C, Mg, F, and Si were outside the range of the present invention were inferior in one or more of corrosion resistance and lubricity. [Industrial Applicability]

[0074] INDUSTRIAL APPLICABILITY The present invention can provide a surface-treated steel sheet having excellent corrosion resistance and lubricity, and has high industrial applicability. [Explanation of symbols]

[0075] 1. Surface-treated steel sheet 10 Steel plate (base material steel plate) 20 Plating layer (galvanized layer or alloyed zinc plating layer) 25 First interface 30 First coating 35 Second interface 40 Second coating A boundary area B1 Center of the first coating B2 Center of the second coating

Claims

1. A base steel plate; a plating layer formed on the surface of the base steel sheet; a first coating formed on the surface of the plating layer; a second coating formed on the surface of the first coating and having a thickness of 0.6 μm or more; A surface-treated steel sheet having the Zn concentration of the plating layer is 40% by mass or more and 100% by mass or less, and the Mg concentration is 0% by mass or more and less than 4.0% by mass, When the concentrations of C, O, F, Mg, Al, Si, P, Ti, V, Zn, and Zr were continuously measured by linear analysis in the thickness direction from the plating layer toward the surface of the coated steel sheet, a position where the Zn concentration first becomes 35.0 mass% or less is defined as a first interface, which is an interface between the plating layer and the first coating; a boundary region includes the first interface and is located between a range of 10 nm from the first interface toward the plating layer and a range of 15 nm from the first interface toward the first coating in the thickness direction; a second interface between the first coating and the second coating is defined as the position where the Zn concentration first becomes 3.0 mass % or less, and a range of 10 nm from the center between the first interface and the second interface in the thickness direction toward the second interface is defined as a central part of the first coating; When a region of the second coating between a position 400 nm and a position 410 nm from the second interface in the thickness direction is defined as a central portion of the second coating, Satisfying one or more of the following formulas (1) to (3) and formulas (4) to (15): A surface-treated steel sheet characterized by: Dti≧5.0 (1) Dzr≧5.0 (2) Dv≧5.0 (3) Dti+Dzr+Dv≦25.0 (4) B1c<10.0 (5) B2c≧40.0 (6) 5.0 / M≦A mg≦25.0 (7) 0.5≦B1mg≦5.0 (8) 15.0 / M≦Af≦40.0 (9) 0.5≦B1f≦15.0 (10) Amg / B1mg≧2.0 (11) Af / B1f≧2.0 (12) B1si<5.0 (13) B1zn≧0.5 (14) B2zn<3.0 (15) wherein Dti is the maximum concentration of Ti in mass % in the first coating from the first interface to the center in the thickness direction between the first interface and the second interface, Dzr is a maximum concentration of Zr in mass % in the first coating from the first interface to a center between the first interface and the second interface in the thickness direction, Dv is the maximum concentration of V in mass % in the first coating from the first interface to the center in the thickness direction between the first interface and the second interface, B1c is the average concentration of C in mass % in the central portion of the first coating, B2c is the average concentration of C in mass % in the central portion of the second coating, A mg is the maximum concentration of Mg in mass % in the boundary region of the first coating, B1mg is the average concentration of Mg in mass% in the central portion of the first coating, Af is the maximum concentration of F in mass % in the boundary region of the first coating, B1f is the average concentration of F in mass % in the central portion of the first coating, B1si is the average concentration of Si in mass % in the central portion of the first coating, B1zn is the average concentration of Zn in mass % in the central portion of the first coating, B2zn is the average concentration of Zn in mass % in the central portion of the second coating, The M is a constant that is 1 when the Mg concentration of the plating layer is 0 mass % or more and less than 1.0 mass %, and is 2 when the Mg concentration is 1.0 mass % or more and less than 4.0 mass %.

2. Furthermore, the following formula (16) is satisfied: The surface-treated steel sheet according to claim 1 , 0≦Cmg<5.0 (16) Here, Cmg is the Mg concentration in mass % at a position 10 nm from the first interface toward the plating layer in the thickness direction of the plating layer.

3. Furthermore, the following formulas (17) to (19) are satisfied: The surface-treated steel sheet according to claim 1 or 2, characterized in that 5.0≦Aal≦20.0 (17) 0.2≦B1al≦5.0 (18) Aal / B1al≧5.0 (19) where Aal is the maximum concentration of Al in wt. % in the boundary region; The B1al is the average concentration of Al in mass % in the central portion of the first coating.

4. Furthermore, the following formulas (20) to (21) are satisfied: The surface-treated steel sheet according to claim 1 or 2, characterized in that 10.0≦Ap≦25.0 (20) 0.5≦B1p≦8.0 (21) where Ap is the maximum concentration of P in the boundary region, B1p is the average concentration of P in mass % in the central portion of the first coating.

5. Furthermore, the following formula (22) is satisfied: The surface-treated steel sheet according to claim 1 or 2, characterized in that 1.0≦B1zn≦30.0 (22)

6. Furthermore, the following formula (23) is satisfied: The surface-treated steel sheet according to claim 1 or 2, characterized in that X2si / Y2si≧1.1 (23) wherein X2si is the maximum concentration, in mass %, of Si in a region extending from the surface of the second coating to 100 nm toward the second interface, Y2si is the average concentration of Si in mass % in a region of the second coating between 300 and 310 nm from the surface toward the second interface.

7. Furthermore, the following formula (24) is satisfied: The surface-treated steel sheet according to claim 1 or 2, characterized in that Af / B1f≧2.5 (24)

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