Plated steel material

Description

/ 36 PLATED STEEL MATERIAL TECHNICAL FIELD

[001] The present invention relates to a sheeted steel material.

[002] Priority is claimed in Japanese Patent Application No. 2023-064064, filed on April 11, 2023, the contents of which are incorporated herein by reference. FUNDAMENTALS OF THE TECHNIQUE

[003] A steel material on whose surface a Zn-containing Al and Mg plating layer is formed (a Zn-Al-Mg based plating steel material) has exceptional corrosion resistance. Therefore, Zn-Al-Mg based plating steel materials are widely used, for example, as a material for structural members requiring corrosion resistance, such as building materials.

[004] For example, Patent Document 1 describes a plated steel sheet including: a steel sheet; and a plated layer formed on a surface of the steel sheet, wherein the plated layer contains Al: 0 to 90% by mass and Mg: 0 to 10% by mass in terms of average composition, and the remainder containing Zn and an impurity; and a patterned part, arranged so as to have a certain shape, and a non-patterned part are formed on the plated layer, the patterned part and the non-patterned part each include one or two of a first region and a second region, the absolute value of the difference between the area fraction of the first region in the patterned part and the area fraction of the first region in the non-patterned part is 30% or more, and the first region has an orientation ratio of 3.5 or more and the second region has an orientation ratio of less than 3.5.

[005] Patent Document 2 describes a Zn-Al-Mg plated steel sheet including: a steel sheet; and a plated layer containing Al in an amount of 4% by mass or more and 22% Petition 870250088812, dated 09 / 30 / 2025, page 11 / 50 / 36 by mass or less, Mg in an amount of 1% by mass or more and 5% by mass or less, and the remainder containing Zn and an unavoidable impurity, wherein the cross-section of the plated layer, which is parallel to the surface of the plated layer, has a diffraction intensity ratio I(200) / I(111) of 0.8 or more, which is the ratio of the XI(200) plane diffraction intensity of the Al phase to the XI(111) plane diffraction intensity of the Al phase.

[006] Moreover, steel-clad materials are placed in various environments and, in areas where volcanic gas is generated, industrial areas and the like, SOx gas in the atmosphere dissolves in rainwater and becomes acid rain, which can affect the corrosion resistance of steel-clad materials. However, in the related technique, the improvement in corrosion resistance in an acidic environment has been almost unstudied.

[007] Patent Document 1 describes that, where the first region means a region having an intensity ratio of 3.5 or more between the I0002 diffraction peak intensity of the (0002) plane and the I10-11 diffraction peak intensity of the (10-11) plane in the Zn phase, and the second region means a region having an intensity ratio that is less than 3.5, the difference between the area ratio of the first region in the patterned part and the area ratio of the first region in the non-patterned part is defined as 30% or more to intentionally express characters, designs and the like on the surface of the plated layer. However, Patent Document 1 did not study corrosion resistance in an acidic environment.

[008] Patent Document 2 describes that, by controlling the orientation of the Al phase in the plated layer, the plated layer has an appearance similar to that of a pear peel, which has a fine texture and many smooth and shiny parts. However, corrosion resistance in an acidic environment has not been examined. List of Citations Petition 870250088812, dated 09 / 30 / 2025, page 12 / 50 / 36 Patent Document

[009] Patent Document 1: Japanese Patent Application No. Examined, First Publication No. 2021-85086 Patent Document 2: International Publication PCT No. WO 2011 / 001662 SUMMARY OF THE INVENTION Technical Problem

[0010] The present invention was made in view of the above circumstances, and one objective thereof is to provide a sheeted steel material having exceptional resistance to sacrificial corrosion and resistance to corrosion in an acidic environment. Solution to the Problem

[0011] In order to achieve the above objective, the present invention adopts the constitutions described below.

[0012] [1] A plated steel material including: a steel material; and a plating layer on the steel material, wherein the plating layer has a chemical composition containing, in terms of % by mass, Al: 6.0 to 30.0% Mg: 3.0 to 15.0% Fe: 0.01 to 15.00% Yes: 0 to 2.0%, Ca: 0 to 2.00%, one or two or more elements selected from a group of elements; Sb: 0 to 0.50%, Pb: 0 to 0.50%, Cu: 0 to 1.00%, Sn: 0 to 1.00%, Ti: 0 to 1.00%, Cr: 0 to 1.00%, Nb: 0 to 1.00%, Zr: 0 to 1.00%, Ni: 0 to 1.000%, Mn: 0 to 1.00%, Mo: 0 to 1.00%, Ag: 0 to 1.00%, Li: 0 to 1.00%, La: 0 to 1.000%, Ce: 0 to 1.000%, B: 0 to 0.500%, Y: 0 to 0.50%, P: 0 to 0.50%, Mr: 0 to Petition 870250088812, dated 09 / 30 / 2025, p. 13 / 50 / 36 0.50%, Co: 0 to 0.500%, Bi: 0 to 0.500%, In: 0 to 0.50%, V: 0 to 0.500% and W: 0 to 0.50%, in a quantity of 0 to 5.0% in total, and the remainder: Zn and an impurity, and the plated layer has a diffraction intensity obtained from an X-ray diffraction measurement result, the diffraction intensity satisfying formula (1) below: 0.5 < I(002)Zn / {I(100)Zn + I(101)Zn} < 25.0 ••• (1) in formula (1), I(002)Zn represents a diffraction intensity of the η-Zn (002) phase, I(100)Zn represents a diffraction intensity of the η-Zn (100) phase and I(101)Zn represents a diffraction intensity of the η-Zn (101) phase.

[0013] [2] The steel plated material according to [1], wherein Al and Mg in the plated layer are Al: 10.0 to 25.0% and Mg: 4.5 to 15.0%, respectively.

[0014] [3] The steel plated material according to [1] or [2], wherein Al and Mg in the plated layer are Al: 15.0 to 22.0% and Mg: 5.5 to 15.0%, respectively.

[0015] [4] The steel plated material according to any of [1] to [3], wherein a diffraction intensity of the plated layer obtained from an X-ray diffraction measurement result satisfies formula (2) below: 1.5 < I(002)Zn / {I(100)Zn + I(101)Zn} < 25.0 ••• (2).

[0016] [5] The steel plated material according to any of [1] to [4], wherein a fraction of the area of ​​the [eutectic structure a / MgZn2 ] contained in a surface structure of the plated layer in a plan view is 5 to 70%.

[0017] [6] The steel plated material according to any of [1] to [5], wherein a fraction of the area of ​​the [eutectic structure of a / MgZn2] contained in a surface structure of the plated layer in a view Petition 870250088812, dated 09 / 30 / 2025, page 14 / 50 / 36, the flat rate is from 10 to 70%.

[0018] [7] Steel material plated according to any of [1] to [6], wherein The Sn content in the plated layer is 0.05 to 0.50% by mass, and an Mg2Sn phase is detected by the X-ray diffraction measurement of the plated layer.

[0019] [8] The steel plated material according to any of [1] to [7], in which 0.005 to 0.500% of the total of one or two of La and Ce are contained. Advantageous Effects of the Invention

[0020] According to the present invention, it is possible to provide a sheeted steel material having exceptional corrosion resistance in an acidic environment. BRIEF DESCRIPTION OF THE DRAWINGS

[0021] [Figure 1] A schematic cross-sectional view of a sheeted steel material according to an embodiment of the present invention. DESCRIPTION OF THE MODALITIES

[0022] Regarding the corrosion resistance in an acidic environment of a plated steel material, it is necessary to form a plating layer having exceptional corrosion resistance in an acidic environment, such as acid rain, on the surface of a steel material. In order to improve the corrosion resistance in an acidic environment of the plating layer, it is necessary that an element constituting the plating layer is not easily eluted, even in an acidic environment.

[0023] Therefore, the present inventors conducted intensive studies to improve the corrosion resistance in an acidic environment of a Zn-plated layer containing Al and Mg. An η-Zn phase contained in Petition 870250088812, dated 09 / 30 / 2025, page 15 / 50 / 36 The plated layer has a hexagonal crystal structure, and several crystal orientation planes are included within it. The corrosion resistance of these crystal orientation planes is not uniform across all orientation planes. For example, since the (002) plane of the η-Zn phase is a dense crystal orientation plane in which the atomic density of Zn is relatively high, Zn itself is considered not to dissolve easily, and the corrosion resistance of Zn itself is relatively high.On the other hand, since the (100) plane of the η-Zn phase is a crystalline orientation plane in which the atomic density of Zn is lower than that of the (002) plane, Zn itself dissolves relatively easily, and the corrosion resistance of Zn itself is low, but the corrosion of base metals is protected by a corrosion product generated along with the corrosion of Zn, and therefore the sacrificial corrosion resistance relative to the base metal is considered to be high. Therefore, it was considered that the corrosion resistance in an acidic environment of the Zn-plated layer containing Al and Mg can be improved by orienting the (002) plane of the η-Zn phase parallel to the surface of the plating layer.

[0024] Therefore, the present inventors attempted to orient the plane (002) of the η-Zn phase contained in the plated layer parallel to the surface of the plated layer. When the Zn-plated layer containing Al and Mg is solidified from a molten state, an α phase crystallizes first, then an MgZn2 phase or an η-Zn phase crystallizes, and furthermore, a ternary eutectic structure including the α phase, the MgZn2 phase, and the η-Zn phase is generated. The ternary eutectic temperature, which serves as an indicator of the onset of the generation of the ternary eutectic structure, can be approximately predicted based on the chemical composition of the plated layer, but it has been found that when a eutectic reaction is caused at a temperature lower than the predicted ternary eutectic temperature, the plane (002) of the η-Zn phase in the ternary eutectic structure is oriented to be parallel to the surface of the plated layer. Specifically, it was verified that a Petition 870250088812, dated 09 / 30 / 2025, page 16 / 50 / 36 eutectic reaction can be caused at a temperature lower than the predicted ternary eutectic temperature, and the (002) plane of the η-Zn phase can be oriented to be parallel to the surface of the plated layer by adjusting an infiltration temperature at the time of infiltration of the steel material into a plating bath and cooling conditions after the steel material is removed from the plating bath.

[0025] Hereafter, sheeted steel material according to an embodiment of the present invention will be described. A clad steel material of the present embodiment comprises a steel material and a clad layer disposed over a surface of the steel material, the clad layer having a chemical composition containing, in terms of % by mass, Al: 6.0 to 30.0%, Mg: 3.0 to 15.0%, Fe: 0.01 to 15.00%, Si: 0 to 2.0%, and Ca: 0 to 2.00%, and containing one or two or more elements selected from the group of elements of Sb: 0 to 0.50%, Pb: 0 to 0.50%, Cu: 0 to 1.00%, Sn: 0 to 1.00%, Ti: 0 to 1.00%, Cr: 0 to 1.00%, Nb: 0 to 1.00%, Zr: 0 to 1.00%, Ni: 0 to 1.000%, Mn: 0 to 1.00%, Mo: 0 to 1.00%, Ag: 0 to 1.00%, Li: 0 to 1.00%, La: 0 to 1.000%, Ce: 0 to 1.000%, B: 0 to 0.500%, Y: 0 to 0.50%, P: 0 to 0.50%, Sr: 0 to 0.50%, Co: 0 to 0.500%, Bi: 0 to 0.500%, In: 0 to 0.50%, V: 0 to 0.500% and W: 0 to 0.50%, in a quantity of 0 to 5.0% in total, and the remainder: Zn and an impurity.and the plated layer has a diffraction intensity obtained from an X-ray diffraction measurement result, the diffraction intensity satisfying the following formula (1). The steel material surface mentioned here refers to the interface between the plated layer and the steel material. 0.5 < I(002)Zn / {I(100)Zn + I(101)Zn} < 25.0 ••• (1)

[0026] In formula (1), I(002)Zn represents a diffraction intensity of the η-Zn (002) phase, I(100)Zn represents a diffraction intensity of the η-Zn (100) phase and I(101)Zn represents a diffraction intensity of the η-Zn (101) phase. Petition 870250088812, dated 09 / 30 / 2025, page 17 / 50 / 36

[0027] In the following description, the expression “%” of the content of each element in a chemical composition means “% by mass”. The content of an element in the chemical composition may be referred to as an element concentration (e.g., Zn concentration, Mg concentration, and the like). “Corrosion resistance in an acidic environment” refers to a property of the plating layer (specifically, ZnAl-Mg alloy layer) that is less likely to corrode in an acidic environment. “Corrosion resistance of flat portions” refers to a property of the plating layer (specifically, Zn-Al-Mg alloy layer) that is less likely to corrode."Sacrificial corrosion resistance" refers to a property of suppressing corrosion of steel material in a portion where the steel material is exposed (e.g., a portion of the end surface where the plated steel material is cut, a portion where the plated layer is cracked due to processing, and a portion where the steel material is exposed due to flaking of the plated layer). Furthermore, "plated layer" means a plating film produced by so-called hot-dip plating treatment.

[0028] As illustrated in Figure 1, a sheeted steel material 1 according to the present embodiment includes a steel material 11. The shape of the steel material 11 is not particularly limited, and an example of steel material 11 is a steel sheet. In addition, the steel material 11 may be, for example, a formed base steel material, such as a steel pipe, a civil engineering and construction material (fence manhole, corrugated pipe, drainage channel cover, splash prevention plate, screw, wire mesh, guardrail, water retaining wall and the like), a household appliance member (an outdoor unit casing of an air conditioner or the like) and a vehicle component (a suspension member or the like). A Petition 870250088812, dated 09 / 30 / 2025, page 18 / 50 / 36 forming is, for example, various deformation processing methods, such as pressing, roll forming and bending.

[0029] The material of steel 11 is not particularly limited. The material of steel 11 may be, for example, various steel materials, such as general steel, Al-killed steel, ultra-low carbon steel, high carbon steel, various high tensile strength steels and some high alloy steels (a steel containing a reinforcing element, such as Ni, Cr, etc.). The material of steel 11 may be a hot-rolled steel sheet, a hot-rolled steel strip, a cold-rolled steel plate, a cold-rolled steel strip and the like described in JIS G 3302: 2010. The manufacturing method of the steel sheet (hot rolling method, pickling method, cold rolling method or the like), the specific manufacturing conditions thereof and the like are also not particularly limited.

[0030] Steel material 11, which serves as an original plating sheet, may be a pre-plated steel material, pre-plated onto the surface of steel material 11. An example of pre-plated steel material is a Ni pre-plated steel material having a Ni plating on steel material 11. Pre-plated steel material is obtained, for example, by electrolytic treatment or displacement plating. Electrolytic treatment is carried out by immersing a base steel material in a sulfuric acid bath or a chloride bath containing metal ions of various pre-plating compositions to perform an electrolytic treatment. Displacement plating is carried out by immersing a base steel material in an aqueous solution containing metal ions of various pre-plating compositions and having a pH adjusted with sulfuric acid to replace and deposit the metal.

[0031] The plated steel material 1 according to the present embodiment includes a plated layer 12 on the steel material 11. No Petition 870250088812, dated 09 / 30 / 2025, page 19 / 50 / 36 According to the present embodiment, the plating layer 12 is mainly made of a Zn-Al-Mg alloy layer due to the chemical composition described below. Furthermore, the plating layer 12 of the plating material 1 according to the present embodiment may include an Fe-Al based interfacial alloy layer between the steel material 11 and the Zn-Al-Mg alloy layer. That is, the plating layer 12 may have a single-layer structure of the ZnAl-Mg alloy layer or a laminated structure including the Zn-Al-Mg alloy layer and the Fe-Al based interfacial alloy layer. Additionally, the Fe-Al based interfacial alloy layer may contain Ni.

[0032] The plating layer according to the present embodiment is made, as the chemical composition, of Zn and other alloying elements. The chemical composition of the plating layer will be described in detail below. Note that the elements whose concentration has a lower limit of 0% are not essential to solve the problem of the plating steel material according to the present embodiment, but are optional elements that can be included in the plating layer for the purpose of, for example, improving the characteristics. <Al: 6,0 a 30,0%>

[0033] Al forms an α phase which is a solid solution with Zn and contributes to improved corrosion resistance of flat surfaces, corrosion resistance in an acidic environment, and sacrificial corrosion resistance. Therefore, the Al concentration is defined as 6.0% or more. The Al concentration can be defined as 10.0% or more, 12.0% or more, or 15.0% or more. On the other hand, when there is an excess of Al, the Mg concentration and the Zn concentration decrease relatively, and the sacrificial corrosion resistance deteriorates. Therefore, the Al concentration is defined as 30.0% or less. The Al concentration can be defined as 28.0% or less, 25.0% or less, 22.0% or less, or 20.0% or less. Petition 870250088812, dated 09 / 30 / 2025, p. 20 / 50 / 36<Mg: 3,0 a 15,0%>

[0034] Mg is an essential element to ensure corrosion resistance of flat surfaces, corrosion resistance in an acidic environment, and sacrificial corrosion resistance. Therefore, the Mg concentration is defined as 3.0% or less. The Mg concentration can be defined as 4.5% or more, 5.5% or more, or 6.0% or more. On the other hand, when the Mg concentration is excessive, workability, particularly spray properties, can deteriorate, and corrosion resistance of flat surfaces can deteriorate even further. Therefore, the Mg concentration is defined as 15.0% or less. The Mg concentration can be defined as 12.0% or less, 10.0% or less, or 8.0% or less. <Fe: 0,01% a 15,00%>

[0035] Iron may be contained in the plating layer in an amount of 0.01% or more. It has been confirmed that when the iron concentration is 15.00% or less, the performance of the plating layer is not adversely affected. The iron concentration may be defined as, for example, 0.05% or more, 0.10% or more, 0.50% or more, or 1.00% or more. The iron concentration may be defined as, for example, 10.00% or less, 5.00% or less, 2.00% or less, or 1.00% or less. As iron may be mixed into the steel material, the iron concentration may be 0.05% or more. <Si: 0% a 2,0%>

[0036] The concentration of Si can be 0%. On the other hand, Si contributes to improving the corrosion resistance of flat surfaces and corrosion resistance in an acidic environment. Therefore, the Si concentration can be defined as 0.05% or more, 0.1% or more, 0.2% or more, or 0.5% or more. Conversely, when the Si concentration is excessive, the corrosion resistance of flat surfaces, corrosion resistance in an acidic environment, and sacrificial corrosion resistance deteriorate. Therefore, the Petition 870250088812, dated 09 / 30 / 2025, p. 21 / 50 / 36 Si concentration is defined as 2.0% or less. Si concentration can be defined as 1.5% or less, 1.0% or less, or 0.5% or less.<Ca: 0% a 2,00%>

[0037] The concentration of Ca can be 0%. On the other hand, Ca is an element capable of adjusting the ideal amount of Mg elution to confer corrosion resistance to flat surfaces and corrosion resistance in an acidic environment. Therefore, the concentration of Ca can be 0.05% or more, 0.10% or more, or 0.50% or more. Conversely, when the concentration of Ca is excessive, the corrosion resistance to flat surfaces and workability deteriorate. Therefore, the concentration of Ca is defined as 2.00% or less. The concentration of Ca can be defined as 1.00% or less, 0.50% or less, or 0.10% or less.

[0038] In addition, the plating layer according to the present embodiment may contain one or two or more elements selected from the group of elements: Sb: 0 to 0.50%, Pb: 0 to 0.50%, Cu: 0 to 1.00%, Sn: 0 to 1.00%, Ti: 0 to 1.00%, Cr: 0 to 1.00%, Nb: 0 to 1.00%, Zr: 0 to 1.00%, Ni: 0 to 1.000%, Mn: 0 to 1.00%, Mo: 0 to 1.00%, Ag: 0 to 1.00%, Li: 0 to 1.00%, La: 0 to 1.000%, Ce: 0 to 1.000%, B: 0 to 0.500%, Y: 0 to 0.50%, P: 0 to 0.50%, Sr: 0 to 0.50%, Co: 0 to 0.500%, Bi: 0 to 0.500%, In: 0 to 0.50%, V: 0 to 0.500%, and W: 0 to 0.50%. The sum of these elements is 0 to 5.0%. When the total exceeds 5.0%, the corrosion resistance of flat portions, the resistance to red rust, and the corrosion resistance of base metals may deteriorate. Furthermore, these elements are optional additive elements, and the total quantity may be 0%. <Sb, Pb: 0 a 0,50% cada>

[0039] The concentration of Sb and Pb can be 0%. On the other hand, Sb and Pb contribute to improved resistance to sacrificial corrosion. Therefore, the concentration of each of Sb and Pb can be defined as 0.05% or more, 0.10% or more, or 0.15% or more. On the other hand, when the Petition 870250088812, dated 09 / 30 / 2025, page 22 / 50 / 36. If the concentration of Sb and Pb is excessive, the corrosion resistance of flat portions deteriorates. Therefore, the concentration of each of Sb and Pb is defined as 0.50% or less. The concentration of each of Sb and Pb can be defined as 0.40% or less, 0.30% or less, or 0.25% or less. <Cu, Ti, Cr, Nb, Zr, Mn, Mo, Ag e Li: 0 a 1,00% cada>

[0040] The concentration of each of Cu, Ti, Cr, Nb, Zr, Mn, Mo, Ag, and Li can be 0%. On the other hand, they contribute to improved resistance to sacrificial corrosion. Therefore, the concentration of each of Cu, Ti, Cr, Nb, Zr, Mn, Mo, Ag, and Li can be defined as 0.05% or more, 0.08% or more, or 0.10% or more. Conversely, when the concentration of Cu, Ti, Cr, Nb, Zr, Mn, Mo, Ag, and Li is excessive, the corrosion resistance of flat portions deteriorates. Therefore, the concentration of each of Cu, Ti, Cr, Nb, Zr, Mn, Mo, Ag, and Li is defined as 1.00% or less. The concentration of each of the following elements: Cu, Ti, Cr, Nb, Zr, Mn, Mo, Ag, and Li can be defined as 0.80% or less, 0.70% or less, or 0.60% or less. <Ni: 0 a 1,000%>

[0041] The concentration of Ni can be 0%. On the other hand, they contribute to improved sacrificial corrosion resistance. Therefore, the concentration of Ni can be defined as 0.050% or more, 0.080% or more, or 0.100% or more. Conversely, when the concentration of Ni is excessive, the corrosion resistance of flat portions deteriorates. Therefore, the concentration of Ni is defined as 1.000% or less. The concentration of Ni can be defined as 0.800% or less, 0.700% or less, or 0.600% or less. <Sn: 0 a 1,00%>

[0042] The Sn concentration can be 0%. On the other hand, Sn is an element that forms an intermetallic compound with Mg and improves the sacrificial corrosion resistance of the plating layer. Therefore, the Petition 870250088812, dated 09 / 30 / 2025, page 23 / 50 / 36: Sn concentration can be defined as 0.01% or more, 0.05% or more, or 0.10% or more. However, when the Sn concentration is excessive, the corrosion resistance of flat portions deteriorates. Therefore, the Sn concentration is defined as 1.00% or less. The Sn concentration can be defined as 0.50% or less, 0.30% or less, or 0.20% or less. <La e Ce: 0 a 1,000% cada>

[0043] The concentration of each of La and Ce can be 0%. On the other hand, La and Ce contribute to improved sacrificial corrosion resistance. Therefore, the concentration of each of La and Ce can be defined as 0.100% or more, 0.150% or more, or 0.200% or more. Conversely, when the concentration of La and Ce is excessive, the corrosion resistance of flat portions deteriorates. Therefore, the concentration of each of La and Ce is defined as 1.000% or less. The concentration of each of La and Ce can be defined as 0.500% or less. Furthermore, the total of one or two of La and Ce can be defined as 0.010 to 0.500%. <B: 0 a 0,500%>

[0044] The concentration of B can be 0%. On the other hand, B contributes to improved sacrificial corrosion resistance. Therefore, the concentration of B can be defined as 0.100% or more, 0.150% or more, or 0.200% or more. Conversely, when the concentration of B is excessive, the corrosion resistance of flat portions deteriorates. Therefore, the concentration of B is defined as 0.500% or less. The concentration of B can be defined as 0.400% or less or 0.300% or less. <Y, P e Sr: 0 a 0,50% cada>

[0045] The concentration of each of Y, P, and Sr can be 0%. On the other hand, Y, P, and Sr contribute to improved resistance to sacrificial corrosion. Therefore, the concentration of each of Y, P, and Sr can be defined as 0.10% or more, 0.15% or more, or 0.20% or more. Conversely, when the concentration of Y, P, and Sr is excessive, the corrosion resistance Petition 870250088812, dated 09 / 30 / 2025, page 24 / 50 / 36 of flat portions deteriorates. Therefore, the concentration of each of Y, P, and Sr is defined as 0.50% or less. The concentration of each of Y, P, and Sr can be defined as 0.40% or less or 0.30% or less. <Co, Bi e V: 0 a 0,500% cada>

[0046] The concentration of each of Co, Bi, and V can be 0%. On the other hand, Co, Bi, and V contribute to improved resistance to sacrificial corrosion. Therefore, the concentration of each of Co, Bi, and V can be defined as 0.100% or more, 0.150% or more, or 0.200% or more, respectively. Conversely, when the concentration of Co, Bi, and V is excessive, the corrosion resistance of flat portions deteriorates. Therefore, the concentration of each of Co, Bi, and V is defined as 0.500% or less. The concentration of each of Co, Bi, and V can be defined as 0.400% or less or 0.300% or less. <In e W: 0 a 0,50% cada>

[0047] The concentration of each of In and W can be 0%. On the other hand, In and W contribute to improved sacrificial corrosion resistance. Therefore, the concentration of each of In and W can be defined as 0.10% or more, 0.15% or more, or 0.20% or more, respectively. Conversely, when the concentration of In and W is excessive, the corrosion resistance of flat portions deteriorates. Therefore, the concentration of each of In and W is defined as 0.50% or less. The concentrations of In and W can be defined as 0.40% or less and 0.30% or less, respectively. <Restante: Zn e impurezas>

[0048] The remainder of the plating layer components according to the present embodiment includes Zn and an impurity. Zn is an element that confers corrosion resistance to flat portions, corrosion resistance in an acidic environment, and sacrificial corrosion resistance to the plating layer. In the present embodiment, the impurity means a mixed impurity of a Petition 870250088812, dated 09 / 30 / 2025, page 25 / 50 / 36 manufacturing environment or similar and a permitted impurity up to a point where the characteristics of the plated steel material according to the present embodiment are not adversely affected. For example, in the plated layer, a small amount of components other than Fe may be mixed as the impurity due to mutual atomic diffusion between the base steel material and the plating bath.

[0049] The chemical components of the plating layer are measured by the following method. For example, the plating material is cut to a size of 30 mm x 30 mm to obtain a measurement sample. Then, an acidic solution is obtained by removing and dissolving the plating layer in the measurement sample using a 10% aqueous solution of hydrochloric acid to which 0.06% by mass of an inhibitor (manufactured by ASAHI Chemical Co., Ltd., IBIT 710K) has been added to suppress corrosion of the steel material. The resulting acidic solution is then subjected to ICP analysis. In this way, the chemical composition of the plating layer can be determined. When cutting the plating material, it is preferable to avoid the end portion and the weld of the plating material. The type of acid is not particularly limited, as long as the acid can dissolve the plating layer. For example, the acid is 10% by vol. HCl.The chemical composition is measured three times using the methods described above, and the average of these measurements is taken as the chemical composition of the plating layer.

[0050] A metallographic structure of the clad layer will be described next.

[0051] The plating layer contains an α phase and a MgZn2 phase. The α phase is a phase containing a fine Al phase and a fine Zn phase. Part of the α phase and the MgZn2 phase can form a lamellar binary eutectic structure ([α / MgZn2 phase eutectic structure]). When the [α / MgZn2 phase eutectic structure] is present, the corrosion resistance of flat portions of the plating layer improves even further. However, when the plating layer Petition 870250088812, dated 09 / 30 / 2025, page 26 / 50 / 36, contains a large amount of [eutectic structure of the α / MgZm phase] due to excessive precipitation of the α phase and the MgZn2 phase, the proportion of the η-Zn phase becomes relatively small, and the red rust resistance and corrosion resistance of the base metal deteriorate. Therefore, the [eutectic structure of the α / MgZm phase] is preferably in a range of 70% or less, or preferably in a range of 5 to 70%, and may be in a range of 10 to 70% in terms of area fraction. The [eutectic structure of the α / MgZn2 phase] may be 0% or more than 0%.

[0052] Furthermore, the plated layer of the present embodiment contains an η-Zn phase in addition to the α phase and the MgZn2 phase. At least part of the η-Zn phase forms a ternary eutectic structure together with the α phase and the MgZn2 phase. In addition, the η-Zn phase may be contained in the plated layer as a massive η-Zn phase.

[0053] Furthermore, when 0.05 to 0.5% of Sn is contained in the plating layer, the Mg2Sn phase is reliably contained in the plating layer. The Mg2Zn phase may be present even when the amount of Sn is 0.05% or less. Because the amount of Mg2Sn phase is small, its presence is confirmed by X-ray diffraction measurement. When the plating layer contains the Mg2Sn phase, the plating steel material has greater resistance to sacrificial corrosion.

[0054] When a peak is detected at 23.4 ± 0.3° in the Ka-ray X-ray diffraction measurement from a Cu tube, it is determined that the Mg2Sn phase is present. The X-ray diffraction measurement is performed using an X-ray diffractometer (manufactured by Rigaku Corporation (model number RINT-TTR III)) under the following conditions: X-ray output: 50 kV and 300 mA; copper target; TTR goniometer (horizontal goniometer); Ke filter slit width: 0.05 mm; longitudinal boundary slit width: 2 mm; light-receiving slit width: 8 mm; and light-receiving slit 2: open, and under the following velocity measurement conditions: Petition 870250088812, dated 09 / 30 / 2025, page 27 / 50 / 36 sweep: 5 degrees / min., step width: 0.01 degrees, and sweep geometric axis: 2Θ (5 to 90°).

[0055] The plated layer may contain a phase different from the phases described above as remaining. For example, an Al-Ca-Si phase or similar may be contained.

[0056] The crystal orientation of the η-Zn phase will be described next.

[0057] In the plated layer of the present embodiment, the X-ray diffraction intensity obtained from the X-ray diffraction measurement result of the plated layer must satisfy the relationship of the following formula (1). When the following formula (1) is satisfied, the (002) plane of the η-Zn phase is oriented to become parallel to the surface of the plated layer, and the corrosion resistance in an acidic environment improves. The X-ray diffraction intensity more preferably satisfies the following formula (2). When I(002)ζπ / {I(100)ζπ + I(101)zn is less than 0.5, the orientation of the (002) plane of the η-Zn phase is not sufficient and the corrosion resistance in an acidic environment becomes insufficient. Furthermore, when I(002)Zn / {I(100)Zn + I(101)Zn} exceeds 25.0, there is a concern that sacrificial corrosion resistance may deteriorate. 0.5 < I(002)zn / {I(100)zn + I(101)zn} < 25.0 ••• (1) 1.5 < I(002)zn / {I(100)zn + I(101)zn} < 25.0 ••• (2)

[0058] In formula (1) and formula (2), I(002)zn represents a diffraction intensity of the η-Zn (002) phase, I(100)zn represents a diffraction intensity of the η-Zn (100) phase and I(101)zn represents a diffraction intensity of the η-Zn (101) phase.

[0059] One method for measuring the area fraction of the [eutectic structure of the (vMgZii2| phase] is as follows. First, the surface of the plated layer is adjusted to be flat by mechanical polishing. Then, the surface of the plated layer is chemically polished by colloidal polishing, and polishing is continued until the surface becomes Petition 870250088812, dated 09 / 30 / 2025, page 28 / 50 / 36 a mirrored surface state.

[0060] The surface of the plated layer after polishing is observed by SEM. Specifically, an element distribution image is captured using SEM-EDS at a magnification of 5000 times (a region 200 μm long and 200 μm wide). In this element distribution image, a phase in which Mg and Zn coexist is specified as the MgZn2 phase. Additionally, a phase containing Al and Zn is specified as the α phase. Most of the α phase exhibits a dendritic shape. Furthermore, after the [eutectic structure of the AMgZii2 phase] containing the α phase and the MgZn2 phase is specified, the area fraction of the [eutectic structure of the AMgZii2 phase] contained in the visual field is calculated by binarization using image analysis software.

[0061] A method for measuring Ι(002)ζπ / {Ι(100)ζπ + I(101)zn} in formula (1) and in formula (2) is as follows. First, the surface of the plated layer is mechanically and chemically polished, as needed, to bring the surface of the plated layer to a mirror-like surface state. Next, for example, X-ray diffraction measurement is performed using an X-ray diffractometer (manufactured by Rigaku Corporation (model number RINT-TTR III)) under the following conditions: X-ray output: 50 kV and 300 mA; copper target; TTR goniometer (horizontal goniometer); filter slit width Ke: 0.05 mm; longitudinal boundary slit width: 2 mm; light receiving slit width: 8 mm; and light receiving slit 2: open, and under the following measurement conditions: scan speed: 5 degrees / min., step width: 0.01 degrees, and geometric scanning axis: 2Θ (5 to 90°).Next, for the η-Zn phase, the diffraction intensity (maximum intensity in the range of 38.993 ± 0.2°) of the (100) plane, the diffraction intensity (maximum intensity in the range of 36.297 ± 0.2°) of the (002) plane, and the diffraction intensity (maximum intensity in the range of 43.232 ± 0.2°) of the (101) plane are measured. The diffraction intensity is one. Petition 870250088812, dated 09 / 30 / 2025, page 29 / 50 / 36 intensity that excludes background intensity. From the diffraction intensity obtained, I(002)Zn / {I(100)Zn + I(101)z„J is determined.

[0062] The presence or absence of the Mg2Sn phase in the plated layer is determined by the appearance or not of a specific diffraction peak for Mg2Sn when X-ray diffraction measurement is performed.

[0063] The amount of adhesion of the plating layer per surface can be, for example, within a range of 20 to 300 g / m2. When the amount of adhesion per surface is defined as 20 g / m2 or more, the corrosion resistance of flat portions, the corrosion resistance in an acidic environment, and the sacrificial corrosion resistance of the plated steel material can be further improved. On the other hand, when the amount of adhesion per surface is defined as 300 g / m2 or less, the workability of the plated steel material can be further improved.

[0064] The method for producing a plated steel material according to the present embodiment will be described below, but the method for producing a plated steel material according to the present embodiment is not particularly limited. For example, according to the manufacturing conditions described below, the plated steel material according to the present embodiment can be obtained.

[0065] In the manufacturing method of the plating steel material of the present embodiment, the steel material is annealed in a reducing atmosphere, the temperature of the annealed steel material is adjusted to be (plating bath temperature - 20)°C or less, the steel material is then immersed in a hot-dip plating bath, and the steel material is pulled up from the hot-dip plating bath to form a plating layer on the surface of the steel material. Then, the plating layer is cooled at an average cooling rate of 15°C / s or more, while a cooling gas is sprayed at a flow rate of 5000 (L / min / m2) or less, until the temperature of the plating layer Petition 870250088812, dated 09 / 30 / 2025, p. 30 / 50 / 36 reach 320°C from the bath temperature and then cooled at an average cooling rate of 5°C / s or less in a range of 320 to 260°C, while a cooling gas is sprayed at a flow rate of 25000 (L / min / m2) or more.

[0066] The steel material that serves as the original plating sheet is annealed in a reducing atmosphere. The reducing atmosphere and annealing conditions are not particularly restrictive. With this annealing, the oxide present on the surface of the steel material is removed as much as possible.

[0067] Next, the steel material immediately after annealing is cooled with a cooling gas, such as nitrogen, until the temperature of the steel material reaches (plating bath temperature - 20)°C or less and then immersed in the hot-dip plating bath. The temperature of the steel material is adjusted to be 20°C or more lower than the plating bath temperature so that the surface roughness (surface roughness on the Zn-Al-Mg alloy layer side) of an Fe-Al based interface alloy layer, which is generated at the interface between the steel material and the plated layer, is adjusted to be small.

[0068] The chemical composition of the plating bath can be adjusted appropriately to obtain the chemical composition of the plated layer described above. The temperature of the plating bath is also not particularly limited. It is possible to appropriately select a temperature at which hot-dip plating can be performed. For example, the temperature of the plating bath can be set above the melting point of the plating bath by about 20°C or more.

[0069] Next, the steel material is removed from the hot-dip plating bath. The amount of adhesion of the layer Petition 870250088812, dated 09 / 30 / 2025, page 31 / 50 / 36. The adhesion of the plating layer can be controlled by controlling the traction speed of the steel material. If necessary, the steel material to which the plating layer is adhered can be cleaned to control the amount of adhesion of the plating layer. The amount of adhesion of the plating layer is not particularly limited and may be, for example, within the range described above.

[0070] Next, the plated layer is cooled. Regarding cooling, the plated layer is first cooled at an average cooling rate of 15°C / s or more until the plated layer temperature reaches 320°C from the bath temperature. The average cooling rate until the plated layer temperature reaches 320°C from the bath temperature can be 30°C / s or less. Cooling is carried out, for example, by spraying a cooling gas, but the vibration of the steel material is greatly reduced by setting the cooling gas flow rate at that time to 5000 (L / min / m2) or less. The cooling gas flow rate can be adjusted to 100 (L / min / m2) or more. When the cooling gas is sprayed for cooling, a plurality of blow nozzles for the cooling gas can be arranged along the transport path of the steel material, and the cooling gas can be sprayed through the nozzles.

[0071] In a bath temperature range up to 320°C, an α phase and a MgZn2 phase are crystallized; furthermore, a eutectic reaction between the α phase and the MgZn2 phase occurs, and the generation of a binary eutectic structure of the α phase and the MgZn2 phase ([α phase / MgZn2 eutectic structure]) is promoted. At this point, the plating layer is cooled at 15°C / s or more in the bath temperature range up to 320°C, while the vibration of the steel material is suppressed by suppressing the flow of the cooling gas, which makes the crystallization of the ternary eutectic structure from the surface of the plating layer less likely. Petition 870250088812, dated 09 / 30 / 2025, page 32 / 50 / 36

[0072] Subsequently, the plated layer is cooled in a range of 320 to 260°C at an average cooling rate of 5°C / s or less, while a cooling gas is sprayed at a flow rate of 25000 (L / min / m2) or higher. Also in this case, a plurality of blow nozzles for the cooling gas is arranged along the transport path of the steel material. Furthermore, when the flow rate is set to 25000 (L / min / m2) or higher, the plated layer is vibrated by the spray of the cooling gas. The cooling gas flow rate in the range of 320 to 260°C can be 80000 (L / min / m2) or less. As a result, the crystallization of the ternary eutectic structure that has been suppressed until now is initiated; However, at this moment, the (002) plane of the η-Zn phase contained in the ternary eutectic structure is oriented to be parallel to the surface of the plated layer.

[0073] In cooling in the bath temperature range up to 320°C and in the range from 320°C to 260°C, the cooling gas to be sprayed is not particularly limited and may be a non-oxidizing gas, such as nitrogen, an inert gas, such as argon or air, or a mixture of the same.

[0074] When the cooling gas flow is controlled, the shape of the gas nozzle from which the cooling gas is expelled is adjusted, for example, in a diameter range of 1 to 50 mm. The angle formed by the tip of the gas nozzle and the steel plate is adjusted, for example, in a range of 70 to 110°, more preferably 90° (perpendicular). The distance between the tip of the gas nozzle and the steel plate is defined in a range of 30 to 1000 mm. The shape, angle and distance of the gas nozzle are merely examples, and are not limited to the ranges above.

[0075] There is no need to particularly limit the cooling condition below 260°C, and the cooling can be air or natural.

[0076] When the plated layer is cooled to satisfy the above conditions, a plated layer that satisfies formula (1) is formed. The ratio is assumed as follows. Petition 870250088812, dated 09 / 30 / 2025, p. 33 / 50 / 36

[0077] In the manufacturing method described above, the temperature of the steel material at the time of infiltration into the plating bath is reduced by 20°C or more than the temperature of the plating bath, so that the surface roughness of the Fe-Al based interface alloy layer is reduced and the nucleation sites of the ternary eutectic structure are reduced. The temperature difference between the temperature of the steel material at the time of infiltration into the plating bath and the temperature of the plating bath is 40°C or less. When the temperature difference between the temperature of the steel material at the time of infiltration into the plating bath and the temperature of the plating bath exceeds 40°C, the appearance of the plating becomes poor.Furthermore, when the steel material immersed in the plating bath is pulled upwards, the plated layer is rapidly cooled in the bath's temperature range up to 320°C, while the vibration of the steel material is suppressed, so that an α phase and a MgZn2 phase are crystallized in the plated layer, but the crystallization of the ternary eutectic structure is suppressed to set the initial temperature of the eutectic reaction to a temperature lower than the initial eutectic temperature that is predicted by the plating composition.Next, the crystallization of the ternary eutectic structure is initiated by cooling the plated layer in the range of 320°C to 260°C under the above conditions, but the crystallization is crystallization from a temperature lower than the initial eutectic temperature that is predicted by the plating composition, and therefore the (002) plane of the η-Zn phase contained in the ternary eutectic structure is considered to be oriented to be parallel to the surface of the plated layer, and formula (1) above is satisfied. Examples

[0078] Examples of the present invention will be described below. However, the conditions in the examples are merely an example of a condition adopted to confirm the operability and effects of the present invention. Petition 870250088812, dated 09 / 30 / 2025, p. 34 / 50 / 36 invention. The present invention is not limited to this example of a condition. The present invention may adopt various conditions, provided that the object of the present invention is achieved without departing from the essence of the present invention.

[0079] As an original plating sheet, a hot-rolled steel sheet with a thickness of 1.6 mm was used. This original plating sheet was annealed. The annealing conditions were an immersion temperature of 800°C and an immersion time of 2 minutes in a N2-4%H2 atmosphere. The annealed original plating sheet was then air-cooled with N2 gas to adjust the temperature at the time of immersion in the plating bath to (plating bath temperature -20)°C or less, then immersed in several hot-dip plating baths and then lifted at a lifting rate of 20 to 200 mm / s. At the time of removal of the original plating sheet, the amount of plating adhesion was controlled with an N2 cleaning gas. After the steel material was removed from the plating bath, the steel material was cooled under the conditions shown in Table 2.

[0080] In the cooling in the bath temperature range up to 320°C and in the range from 320 to 260°C, a N2 gas was used as the cooling gas, and the gas flow was controlled as shown in the table. The shape of the gas nozzle, from which the cooling gas was expelled, had a diameter of 6 mm, the angle formed by the tip of the gas nozzle and the steel plate was perpendicular, and the distance between the tip of the gas nozzle and the steel plate was 35 mm.

[0081] In this way, the sheeted steel materials from No. 1 to 50 were manufactured.

[0082] The chemical composition of the plating layer was shown in Table 1. In addition, the metallographic structure of the plating layer was Petition 870250088812, dated 09 / 30 / 2025, page 35 / 50 / 36, was evaluated, and the results are shown in Table 3. Furthermore, the corrosion resistance in an acidic environment and the sacrificial corrosion resistance of the clad steel material were evaluated, and the results are shown in Table 3.

[0083] The chemical composition of the plated layer was measured by immersing a sample cut to a size of 30 mm x 30 mm in a 10% aqueous HCl solution to which an inhibitor was added for pickling and removal of the plated layer, and ICP analysis was then performed on elements eluted in the aqueous solution.

[0084] The area fraction of the [eutectic structure of the α / MgZn2 phase] was evaluated as follows. First, the surface of the plated layer was polished by mechanical polishing and colloidal polishing until a mirror-like surface state was formed. Then, the surface of the plated layer was observed at 5,000x magnification with a field emission scanning electron microscope (FE-SEM) equipped with an energy dispersive elemental analyzer (EDS) (a region 200 μm long and 200 μm wide), and an element distribution image was captured using EDS. In the element distribution image, a phase in which Mg and Zn coexisted was specified as an MgZn2 phase, a phase containing Al and Zn was specified as an α phase, and the [eutectic structure of the α / MgZn2 phase] in which these phases formed a lamellar shape was specified.Furthermore, the area fraction of the [eutectic structure of the α / MgZn2 phase] contained within the visual field was calculated by binarization using image analysis software.

[0085] One method for measuring (002)Zn / {I(100)Zn + I(101)Zn} in formula (1) was as follows. First, the surface of the plated layer was brought to a mirror-like surface state in the same manner described above. Then, the X-ray diffraction measurement was performed using an X-ray diffractometer (manufactured by Rigaku Corporation number no. Petition 870250088812, dated 09 / 30 / 2025, page 36 / 50 / 36 model RINT-TTR III) under the following X-ray output conditions: 50 kV and 300 mA; copper target; TTR goniometer (horizontal goniometer); filter slit width Ke: 0.05 mm; longitudinal limit slit width: 2 mm; light receiving slit width: 8 mm; and light receiving slit 2: open, and under the following measurement conditions: scan speed: 5 degrees / min., step width: 0.01 degrees, and geometric scan axis: 2θ (5 to 90°). Next, for the η-Zn phase, the diffraction intensity (maximum intensity in the range of 38.993 ± 0.2°) of the (100) plane, the diffraction intensity (maximum intensity in the range of 36.297 ± 0.2°) of the (002) plane, and the diffraction intensity (maximum intensity in the range of 43.232 ± 0.2°) of the (101) plane were measured. The diffraction intensity was an intensity that excluded the background intensity. From the diffraction intensity obtained, I(002)Zn / {I(100)Zn + I(101)Zn} was determined.

[0086] The presence or absence of the Mg2Sn phase in the plated layer was determined by the appearance or absence of a specific diffraction peak for Mg2Sn when X-ray diffraction measurement was performed.

[0087] Corrosion resistance in an acidic environment was evaluated as follows. A test specimen was produced by cutting a sheeted steel material to a size of 150 mm x 50 mm. A portion of the end surface of the test specimen was protected with polyester tape manufactured by Nitto Denko Technical Corporation so that the end surface was not exposed, and the area of ​​a flat portion, which would be a corrosion evaluation surface, was then measured.

[0088] In addition, the test specimen having its end surface protected with tape was subjected to an artificial acid rain cycle test defined in JIS H 8502:1999. In the artificial acid rain cycle test, one cycle included spraying with the acidic test solution (spraying time: 2 h, temperature: 35°C, pH: 3.5), drying (drying time: 4 h, temperature: 60°C, humidity: 20 to 30% RH) and wetting (time of Petition 870250088812, dated 09 / 30 / 2025, p. 37 / 50 / 36 wetting: 2 h, temperature: 50°C, humidity: 95% RH), and this cycle was performed repeatedly. The acidic test solution used was produced by adding 5% NaCl and adding NaOH to adjust the pH to 3.5.

[0089] After performing the artificial acid rain cycle test, the tape protecting the end surface of the specimen was removed, and the specimen was immersed in a 30% chromic acid (VI) solution at 25°C for 10 minutes to remove a corrosion product generated on the sample surface. The weight of the specimen after immersion in the chromic acid (VI) solution was measured, the difference from the weight before the start of the test was calculated and then divided by the evaluation surface area to convert the difference into corrosion loss, and the corrosion resistance was evaluated. The evaluation criteria were as follows: “AAAA”, “AAA”, “AA”, and “A” were considered acceptable.

[0090] AAAA: Corrosion loss of 20 g / m2 or less after 60 cycles

[0091] AAA: Corrosion loss of more than 20 g / m2 and 40 g / m2 or less after 60 cycles

[0092] AA: Corrosion loss of more than 40 g / m2 and 60 g / m2 or less in 60 cycles

[0093] A: Corrosion loss of more than 60 g / m2 and 100 g / m2 or less in 60 cycles

[0094] B: Corrosion loss of more than 100 g / m2 in 60 cycles

[0095] Sacrificial corrosion resistance (corrosion resistance of simulated end surfaces) was evaluated as follows. Plated steel material was cut into 100 mm x 100 mm pieces to produce a specimen. In a region centered on the intersection point of the specimen's diagonal lines and having a diameter of 25 mm, the layer Petition 870250088812, dated 09 / 30 / 2025, page 38 / 50 / 36. The sheet metal was removed by milling to expose the steel sheet (base metal). The region with a diameter of 25 mm, in which the base metal was exposed, was subjected to the neutral salt spray test specified in JIS Z 2371: 2015, and the sacrificial corrosion resistance was evaluated based on the state of red rust generation in the region where the base metal was exposed. The evaluation criteria for sacrificial corrosion resistance are shown below. “AAA”, “AA” and “A” were considered acceptable.

[0096] AAA: Red rust area ratio of 5% or less in 2,200h

[0097] AA: Red rust area ratio of more than 5% and 10% or less in 1800 h

[0098] A: Red rust area ratio of more than 10% and 15% or less in 1000 h

[0099] B: Red rust area ratio of more than 15% in 1,000h

[00100] In Nos. 1 to 32, 42 to 45, 47, 48 and 50 (Examples) according to the present invention, the chemical composition and metallographic structure of the plating layer were adequately controlled, and both the corrosion resistance in an acidic environment and the sacrificial corrosion resistance were exceptional.

[00101] In Comparative Example No. 33, the amount of Al was insufficient in the plated layer. Therefore, in No. 33, the corrosion resistance in an acidic environment was insufficient.

[00102] In Comparative Example No. 34, the amount of Al was excessive in the plated layer. Therefore, in No. 34, the α-phase dendrites were generated excessively, and the dendrites functioned as nucleation sites for the η-Zn phase, which made it impossible to guarantee the orientation of the η-Zn phase and rendered both the corrosion resistance in an acidic environment and the sacrificial corrosion resistance insufficient. Petition 870250088812, dated 09 / 30 / 2025, pages 39 / 50 / 36

[00103] In Comparative Example No. 35, the amount of Mg was insufficient in the plated layer. Therefore, in No. 35, the orientation of the ηZn phase could not be guaranteed, and both the corrosion resistance in an acidic environment and the sacrificial corrosion resistance were insufficient.

[00104] In Comparative Example No. 36, the amount of Mg was excessive in the plated layer. Therefore, in No. 36, the MgZn2 phase became excessive, the orientation of the η-Zn phase could not be guaranteed, and the corrosion resistance in an acidic environment was insufficient.

[00105] In Comparative Example No. 37, the cooling gas flow was excessive in the bath temperature range up to 320°C. Therefore, in Comparative Example No. 37, the η-Zn phase orientation could not be guaranteed, and corrosion resistance in an acidic environment was insufficient.

[00106] In Comparative Example No. 38, the cooling gas flow was insufficient during cooling in the range of 320°C to 260°C. Therefore, in Comparative Example No. 38, the orientation of the η-Zn phase could not be guaranteed, and corrosion resistance in an acidic environment was insufficient.

[00107] In Comparative Example No. 39, the cooling rate became low in the bath temperature range up to 320°C. Therefore, in No. 39, the orientation of the η-Zn phase could not be guaranteed, and the corrosion resistance in an acidic environment was insufficient.

[00108] In Comparative Example No. 40, the cooling rate became excessive in the range of 320°C to 260°C. Therefore, in Comparative Example No. 40, the orientation of the η-Zn phase could not be guaranteed, and the corrosion resistance in an acidic environment was insufficient.

[00109] In Comparative Example No. 41, the temperature of the steel plate during immersion in the plating bath was higher than (bath temperature - 20)°C. Therefore, in No. 41, the orientation of the η-Zn phase could not be Petition 870250088812, dated 09 / 30 / 2025, page 40 / 50 / 36 guaranteed, and corrosion resistance in an acidic environment was insufficient.

[00110] In Comparative Example No. 46, the cooling rate became excessive in the range of 320°C to 260°C. Therefore, in No. 46, the orientation of the η-Zn phase could not be guaranteed, and the corrosion resistance in an acidic environment was insufficient.

[00111] In Comparative Example No. 49, the difference between the plate intrusion temperature and the bath temperature was greater than 40°C. Therefore, the external appearance of the plating was poor. Table 1] Type No. Components of the plating layer (% by mass) Remaining: Zn and impurities Zn Al Mg Sn Si Ca Ni Fe Other elements Type Total (%) Example 1 Remaining 6.0 3.0 0 0 0 0 0.05 - - Example 2 Remaining 11.0 3.0 0.06 0.1 0 0 0.05 Bi 0.005 Example 3 Remaining 11.0 3.0 0.06 0.1 0 0 0.05 La: 0.021, Ce: 0.050 0.071 Example 4 Remaining 10.0 4.5 0.01 0.1 0.04 0 0.05 V 0.009 Example 5 Remaining 10.0 5.0 0.01 0.2 0 0 0.08 - - Example 6 Remaining Example 7 Remaining 12.0 5.0 0.01 0.1 0 0 0.08 Pb 0.03 Example 8 Remaining 12.0 6.0 0.01 0.2 0 0 0.11 Zr 0.01 Example 9 Remaining 12.0 6.0 0.01 0.2 0 0 0.08 Co 0.008 Example 10 Remaining 13.0 5.0 0 0.2 0 0 0.12 - - Example 11 Remaining 13.0 5.0 0 0.2 0 0 0.11 La: 0.022, Ce: 0.050 0.072 Example 12 Remaining 15.0 5.0 0.01 0.2 0 0.001 0.22 Ag 0.01 Example 12 Remaining 17.0 5.0 0.01 0.2 0.04 0 0.22 Li 0.02 Example 13 Remaining 18.0 6.0 0 0.4 0.04 0 0.24 Sb 0.08 Example 14 Remaining 19.0 6.0 0.20 0.3 0.04 0.001 0.12 P 0.01 Example 15 Remaining 19.0 6.0 0.01 0.2 0.04 0 0.14 In 0.Example 16 Remaining 19.0 7.0 0.01 0.2 0.04 0.001 0.22 La: 0.020, Ce: 0.055 0.075 Example 17 Remaining 19.0 7.0 0.01 0.2 0.04 0.001 0.24 Mn 0.01 Example 18 Remaining 20.0 10.0 0.01 0.3 0.05 0 0.32 B 0.005 Example 19 Remaining 20.0 6.0 0.01 0.1 0.04 0 0.41 Mo 0.03 Example 20 Remaining 21.0 3.5 0 0.1 0.04 0 0.44 Sr 0.02 Example 21 Remaining 22.0 6.0 0.01 0.4 0.04 0 0.32 La 0.010 Example 22 Remainder 22.0 8.0 0.01 0.7 0.04 0 0.43 Ce 0.010, Petition 870250088812, dated 09 / 30 / 2025, page 41 / 50 / 36 Example 23 Remaining 22.0 4.0 0 0.1 0.01 0 0.33 Nb 0.02 Example 24 Remaining 24.0 3.0 0 0.1 0 0.001 0.25 - - Example 25 Remaining 22.0 4.0 0 0.1 0.01 0.012 0.43 - - Example 26 Remaining 23.0 8.0 0.01 0.7 0.04 0 0.51 Ti 0.01 Example 27 Remaining 23.0 15.0 0.01 0.5 0.04 0 0.60 Y 0.01 Example 28 Remaining 25.0 8.0 0.01 1.1 0.04 0.001 0.60 Cu 0.10 Example 29 Remaining 24.0 7.0 0.01 1.5 0.04 0 0.72 W 0.01 Example 30 Remaining 25.0 8.0 0.02 2.0 0.04 0 1.30 - - Example 31 Remaining 28.0 8.0 0.02 0.5 0.04 0 1.52 Cr 0.03 Example 32 Remaining 30.0 9.0 0.01 0.8 0.04 0 1.74 - - Comparative Example 33 Remaining 4.5 4.0 0 0 0 0 0.12 - - Comparative Example 34 Remaining 32.0 7.0 0 0.1 0 0 0.13 - - Comparative Example 35 Remaining 19.0 2.6 0 0.2 0.01 0 0.15 - - Comparative Example 36 Remaining 19.0 15.5 0 0 0.05 0 0.11 - - Comparative Example 37 Remaining 15.0 3.0 0 0 0.01 0 0.82 - - Comparative Example 38 Remaining 15.0 3.0 0 0 0.01 0 0.82 - - Comparative Example 39 Remaining 15.0 3.0 0 0 0.01 0 0.Example 84 - - Comparative Example 40 Remaining 15.0 3.0 0 0 0.01 0 0.82 - - Comparative Example 41 Remaining 24.0 3.0 0 0.4 0 0 0.51 - - Example 42 Remaining 20.0 7.0 0.01 0.1 0.11 0 0.42 - - Example 43 Remaining 22.0 6.0 0.01 0.4 0.04 0 0.34 - - Example 44 Remaining 21.0 7.5 0.01 0.4 0.12 0 0.43 - - Example 45 Remaining 21.0 8.0 0.01 0.5 1.01 0 0.44 - - Comparative Example 46 Remaining 15.0 3.0 Example 47 Remaining 19.0 6.7 1.00 0.2 0.07 0.001 0.22 - - Example 48 Remaining 30.0 7.0 0.01 0 0.04 0 14.72 - - Comparative Example 49 Remaining 18.0 5.5 0.01 0.2 0.04 0 0.21 - - Example 50 Remaining 19.0 7.0 0.01 0.2 0.04 0.001 0.22 - -, The underlined values ​​are outside the scope of the present invention. Petition 870250088812, dated 09 / 30 / 2025, page 42 / 50 / 36 [Table 2] Type No. Manufacturing conditions Bath temperature (°C) Coated layer adhesion quantity (g / m2) Inlet plate temperature (°C) Cooling rate at bath temperature up to 320°C (°C / s) Cooling gas flow at bath temperature up to 320°C (L / min / m2) Average cooling rate from 320 to 260°C (°C / s) Cooling gas flow at 320 to 260°C (L / min / m2) Example 1 460 45 420 15 5000 5 25000 Example 2 480 50 450 15 5000 5 25000 Example 3 480 50 460 15 5000 5 25000 Example 4 500 50 470 15 5000 5 Example 5: 500 50 480 15 5000 5 25000 Example 6: 530 50 510 15 5000 5 25000 Example 7: 530 50 510 15 1000 5 25000 Example 8: 530 45 510 15 1000 5 25000 Example 9: 530 45 495 15 1000 5 25000 Example 10: 530 45 510 15 1000 5 25000 Example 11: 530 45 510 15 5000 5 25000 Example 12: 530 15 505 15 5000 5 Example 13 530 45 505 15 5000 5 25000 Example 14 530 45 510 15 5000 5 25000 Example 15 530 45 510 15 1000 5 25000 Example 16 530 45 510 15 1000 5 25000 Example 17 530 45Example 18: 590 45, 570 15, 1000 5, 25000. Example 19: 540 45, 520 15, 1000 5, 25000. Example 20: 540 45, 500 20, 1000 5, 25000. Example 21: 540 55, 520 20, 1000 5, 25000. Example 22: 540 56, 520 20, 1000 5, 25000. Example 23: 540 60, 510 20, 5000 5, 25000. Example 24: 560 54, 540 20, 5000 5, 25000. Example 25: 540 Example 26: 550 80 530 20 1000 5 25000 Example 27: 550 35 530 20 1000 5 25000 Example 28: 550 35 520 20 1000 5 25000 Example 29: 550 55 530 20 1000 5 25000 Example 30: 550 200 530 20 1000 5 25000 Example 31: 550 45 525 20 1000 5 25000 Example 32: 550 50 530 20 1000 5 25000 Petition 870250088812, dated 09 / 30 / 2025, page 43 / 50 / 36 Comparative Example 33 450 50 430 15 5000 5 25000 Comparative Example 34 600 50 580 15 5000 5 25000 Comparative Example 35 540 50 505 15 5000 5 25000 Comparative Example 36 540 50 520 15 5000 5 25000 Comparative Example 37 520 50 500 15 6000 5 25000 Comparative Example 38 520 50 500 15 5000 5 20000 Comparative Example 39 520 50 490 10 5000 5 25000 Comparative Example 40 Example 41: 560 50 560 20 5000 5 25000 Example 42: 530 45 510 30 5000 5 30000 Example 43: 540 50 520 20 1000 5 25000 Example 44: 540 60 520 15 100 5 45000 Example 45: 540 60 520 20 1000 5 80000 Example 46: 520 60 500 15 5000 7 25000 Example 47: 530 45 505 15 1000 5 Example 25000 48 550 50 530 20 1000 5 55000 Comparative Example 49 530 15 485 15 5000 5 25000 Example 50 530 45 505 15 1000 2 25000 The underlined values ​​are outside the scope of preferred manufacturing conditions. Table 3] Type No. Plating Layer Performance XRD Surface Structure Mg2Sn Phase Acid Corrosion Resistance Simulated End Surface Corrosion Resistance I (002) / (I (101) + I (100)) Fraction of Lamellar Structure Area « / MgZn2 (%) Presence and Absence Example 1 0.5 0 Absent AA Example 2 0.5 1 Present A AA Example 3 0.5 1 Present AA AA Example 4 0.5 3 Present AA AA Example 5 0.6 6 Present AA AAA Example 6 1.1 7 Present AA AAA Example 7 1.5 6 Present AAA AAA Petition 870250088812, dated 09 / 30 / 2025, page 44 / 50 / 36 Example 8 1.7 7 Present AAA AAA Example 9 1.9 9 Absent AAA AA Example 10 1.9 9 Absent AAAA AA Example 11 1.2 10 Present AAA AAA Example 12 1.3 12 Present AAA AAA Example 13 1.0 14 Absent AA AA Example 14 1.4 22 Present AA AAA Example 15 8.5 23 Present AAA AAA Example 16 9.9 23 Present AAAA AAA Example 17 11.1 23 Present AAA AAA Example 18 13.1 56 Present AAA AAA Example 19 14.6 25 Present AAA AAA Example 20 17.8 0 Absent AA Example 21 19.2 26 Present AAA AAA Example 22 18.0 29 Present AAA AAA Example 23 0.6 0 Absent AA Example 24 0.6 0 Absent AA Example 25 0.5 0 Absent AA Example 26 19.4 29 Present AAA AAA Example 27 20.1 33 Present AAA AAA Example 28 18.5 35 Present AAA AAA Example 29 16.7 38 Present AAA AAA Example 30 15.6 39 Present AAA AAA Example 31 14.1 45 Present AAA AAA Example 32 16.6 70 Present AAA AAA Example Comparative 33 0.5 0 Absent BA Example Comparative 34 0.3 0 Absent BB Example Comparative 35 0.4 0 Absent BB Example Comparative 36 0.4 0 Absent B AA Example Comparative 37 0.3 0 Absent BA Example Comparative 38 0.3 0 Absent BA Example Comparative 39 0.3 0 Absent BA Example Comparative 40 0.2 0 Absent BA Example Comparative 41 0.3 0 Absent BA, Petition 870250088812, dated 09 / 30 / 2025, pages 45 / 50 / 36 Example 42 0.5 66 Present AA AAA Example 43 19.0 26 Present AAA AAA Example 44 18.1 28 Present AAA AAA Example 45 17.8 27 Present AAA AAA Comparative Example 46 0.5 0 Absent BA Example 47 10.4 23 Present AAA AAA Example 48 12.2 41 Present AAA AAA Comparative Example 49 Poor external appearance of plating Example 50 11.5 22 Present AAA AAA The underlined values ​​are outside the scope of the present invention. INDUSTRIAL APPLICABILITY

[00112] The plated steel material of the present description is exceptional in terms of resistance to sacrificial corrosion and resistance to corrosion in an acidic environment and is therefore highly applicable industrially. LIST OF REFERENCE SIGNS

[00113] 1 Plated steel material Steel material Plated layer Petition 870250088812, dated 09 / 30 / 2025, pages 46 / 50

Claims

1 / 2 CLAIMS 1. Plated steel material, characterized in that it comprises: a steel material; and a plating layer on the steel material, wherein the plating layer has a chemical composition containing, in terms of % by mass, Al: 6.0 to 30.0%, Mg: 3.0 to 15.0%, Fe: 0.01 to 15.00%, Si: 0 to 2.0%, Ca: 0 to 2.00%, one or two or more elements selected from a group of elements of Sb: 0 to 0.50%, Pb: 0 to 0.50%, Cu: 0 to 1.00%, Sn: 0 to 1.00%, Ti: 0 to 1.00%, Cr: 0 to 1.00%, Nb: 0 to 1.00%, Zr: 0 to 1.00%, Ni: 0 to 1.000%, Mn: 0 to 1.00%, Mo: 0 The composition of the coating consists of: 1.00%, Ag: 0 to 1.00%, Li: 0 to 1.00%, La: 0 to 1.000%, Ce: 0 to 1.000%, B: 0 to 0.500%, Y: 0 to 0.50%, P: 0 to 0.50%, Sr: 0 to 0.50%, Co: 0 to 0.500%, Bi: 0 to 0.500%, In: 0 to 0.50%, V: 0 to 0.500%, and W: 0 to 0.50%, in a total quantity of 0 to 5.0%, and the remainder: Zn and an impurity, and the plated layer has a diffraction intensity obtained from an X-ray diffraction measurement result.the diffraction intensity satisfying formula (1) below: 0.5 < I(002)Zn / {I(100)Zn + I(101)Zn} < 25.0 ••• (1) in formula (1), I(002)Zn represents a diffraction intensity of the η-Zn phase (002), I(100)Zn represents a diffraction intensity of the η-Zn phase (100) and I(101)Zn represents a diffraction intensity of the η-Zn phase (101).

2. Steel plated material according to claim 1, Petition 870250088812, dated 09 / 30 / 2025, page 47 / 50 2 / 2 characterized in that Al and Mg in the plated layer are Al: 10.0 to 25.0% and Mg: 4.5 to 15.0%, respectively.

3. Steel plated material according to claim 1 or 2, characterized in that Al and Mg in the plated layer are Al: 15.0 to 22.0% and Mg: 5.5 to 15.0%, respectively.

4. Steel plated material according to any one of claims 1 to 3, characterized in that a diffraction intensity of the plated layer obtained from an X-ray diffraction measurement result satisfies formula (2) below: 1.5 < I(002)Zn / {I(100)Zn + I(101)Zn} < 25.0 ••• (2).

5. Steel plated material according to any one of claims 1 to 4, characterized in that the area fraction of the [a / MgZm eutectic structure] contained in a surface structure of the plated layer in a plan view is 5 to 70%.

6. Steel plated material according to any one of claims 1 to 5, characterized in that the area fraction of the [a / MgZm eutectic structure] contained in a surface structure of the plated layer in a plan view is 10 to 70%.

7. Steel plated material according to any one of claims 1 to 6, characterized in that the Sn in the plated layer is Sn: 0.05 to 0.50% by mass, and a Mg2Sn phase is detected by the result of X-ray diffraction measurement of the plated layer.

8. Steel plated material according to any one of claims 1 to 7, characterized in that 0.005 to 0.500% in total of one or two of La and Ce are contained. Petition 870250088812, dated 09 / 30 / 2025, pp. 48 / 50

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