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WO2025121109A1 - Tôle d'acier plaquée à base de zinc-aluminium-magnésium fondu - Google Patents

Tôle d'acier plaquée à base de zinc-aluminium-magnésium fondu Download PDF

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Publication number
WO2025121109A1
WO2025121109A1 PCT/JP2024/040736 JP2024040736W WO2025121109A1 WO 2025121109 A1 WO2025121109 A1 WO 2025121109A1 JP 2024040736 W JP2024040736 W JP 2024040736W WO 2025121109 A1 WO2025121109 A1 WO 2025121109A1
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Prior art keywords
steel sheet
plating film
hot
dip
plating
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PCT/JP2024/040736
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English (en)
Japanese (ja)
Inventor
昌浩 吉田
章一郎 平
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JFE Steel Corp
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JFE Steel Corp
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Priority to JP2025504399A priority Critical patent/JPWO2025121109A1/ja
Publication of WO2025121109A1 publication Critical patent/WO2025121109A1/fr
Pending legal-status Critical Current
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C18/00—Alloys based on zinc
    • C22C18/04—Alloys based on zinc with aluminium as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/26—After-treatment

Definitions

  • the present invention relates to hot-dip Zn-Al-Mg plated steel sheets with excellent corrosion resistance and scratch resistance.
  • Hot-dip galvanized steel sheets have excellent corrosion resistance and have conventionally been widely used as rust-resistant steel sheets in the fields of automobiles, electrical machinery, building materials, and the like.
  • a hot-dip Zn-based plating coating is composed of an interfacial alloy layer present at the interface with the base steel sheet and a main layer present on the interfacial alloy layer, and exhibits superior corrosion resistance compared to cold-rolled steel sheets and hot-rolled steel sheets, mainly due to the sacrificial corrosion protection ability of the Zn present in the main layer against Fe.
  • the above-mentioned interface alloy layer contains as its constituents an Fe-Al alloy or an Fe-Zn alloy formed by the reaction between the Fe in the base steel sheet and the Zn or Al in the coating bath.
  • Patent Document 1 discloses a hot-dip Zn-Al-Mg plated steel sheet having a plating film composition of 4.0 to 10 wt % Al, 1.0 to 4.0 wt % Mg, and the remainder being Zn and unavoidable impurities.
  • Patent Document 2 discloses a hot-dip Zn-Al-Mg plated steel sheet having a plating film composition consisting of 2 to 19 wt % Al, 1.0 to 10 wt % Mg, 0.01 to 2 wt % Si, with the balance being Zn and unavoidable impurities, with the total content of Al and Mg being 20 mass % or less.
  • the plating coating of a general hot-dip Zn-Al-Mg plated steel sheet as disclosed in Patent Document 1 and Patent Document 2 has a problem in that the plating surface is more susceptible to scratches than a conventional hot-dip Zn plated steel sheet due to the presence of soft Al phases and Zn phases.
  • the present invention aims to provide a hot-dip Zn-Al-Mg plated steel sheet that combines high levels of corrosion resistance and scratch resistance.
  • the present inventors have found that it is important not only to control the concentrations of Zn, Al, Mg, and Si in the composition of the plating film of a hot-dip Zn-Al-Mg-plated steel sheet, but also to control the plating film structure, and in particular, that the hardness of MgZn2 formed in the plating film and its effect of stabilizing corrosion products are effective. They have found that it is possible to achieve both high levels of corrosion resistance and scratch resistance by controlling the amount of MgZn2 present in the main layer, specifically the area ratio, within a specific range when observing a cross section of the plating film in the thickness direction.
  • a hot-dip Zn-Al-Mg-plated steel sheet having a plating film consisting of an interfacial alloy layer existing at the interface with a base steel sheet and a main layer existing on the interfacial alloy layer,
  • the plating film has a composition containing 10 to 22 mass% Al, 0.01 to 2 mass% Si, and 3 to 10 mass% Mg, with the remainder being Zn and unavoidable impurities;
  • the hot-dip Zn-Al-Mg plated steel sheet characterized in that, when a cross section of the plating film is observed in a thickness direction, an area ratio of MgZn2 present in the main layer is 30% or more.
  • the hot-dip Zn-Al-Mg plated steel sheet according to 1 above characterized in that, when a cross section of the plating film is observed in a thickness direction, an area ratio of MgZn 2 having a portion exposed on the outermost plating surface among the observed MgZn 2 is 30% or more.
  • the hot-dip Zn-Al-Mg plated steel sheet according to 1 or 2 above characterized in that, when a cross section of the plating film is observed in a thickness direction, an area ratio of MgZn2 present within a thickness range of up to 50% from the surface of the main layer exceeds 50% of the observed MgZn2. 4.
  • the hot-dip Zn-Al-Mg plated steel sheet according to 1 or 2 above characterized in that, when a cross section of the plating film is observed in a thickness direction, the area ratio of the Al phase present within a thickness range of up to 50% from the surface of the main layer is less than 50% of the observed Al phase. 5.
  • the present invention provides hot-dip Zn-Al-Mg plated steel sheets that combine high levels of corrosion resistance and scratch resistance.
  • FIG. 1 is an enlarged schematic view of a cross section of a hot-dip Zn-Al-Mg plated steel sheet according to one embodiment of the present invention.
  • FIG. 2 is an enlarged schematic view of a cross section of a hot-dip Zn-Al-Mg plated steel sheet according to another embodiment of the present invention.
  • FIG. 2 is an enlarged schematic view of a cross section of a hot-dip Zn-Al-Mg plated steel sheet according to another embodiment of the present invention.
  • the hot-dip Zn-Al-Mg plated steel sheet of the present invention has a plating film 20 on a base steel sheet 10, and the plating film 20 comprises an interfacial alloy layer 22 present at the interface with the base steel sheet 10 and a main layer 21 present on the interfacial alloy layer.
  • the plating film 20 has a composition containing 10 to 22 mass % Al, 0.01 to 2 mass % Si, 3 to 10 mass % Mg, with the remainder being Zn and unavoidable impurities.
  • Zn the main component of the plating film
  • the plating layer is composed of elements with low specific gravity such as Al and Mg, so that Zn must be the main component in terms of atomic composition ratio as well. Therefore, the Zn content in the plating film must be 60 mass% or more, and preferably 70 mass% or more.
  • the upper limit of the Zn content is the content that is the remainder other than elements other than Zn and impurities.
  • Al in the plating film is an essential element for forming an Al phase in the main layer and obtaining excellent corrosion resistance.
  • the Al content of the plating film exceeds 5 mass%, an Al phase can be formed in the plating film, and the amount of Al phase formed increases with an increase in the Al content.
  • the Al content in the plating film may be 10 mass% or more. Therefore, the lower limit of the Al concentration is set to 10 mass%.
  • the Al concentration in the plating film increases, the sacrificial corrosion protection tends to deteriorate. Therefore, the upper limit of the Al concentration needs to be 22 mass% or less.
  • the Al content in the plating film is preferably 12 to 20 mass %, and more preferably 15 to 19 mass %.
  • the Si in the plating film is used to suppress the abnormal growth of the Fe-Al interfacial alloy layer that is generated mainly at the interface with the base steel sheet, and to ensure the workability of the plating film.
  • the base steel sheet is immersed in a molten Zn-Al-Mg plating bath containing the Si, the Fe on the surface of the base steel sheet reacts with the Al and Si in the bath to form an Fe-Al and/or Fe-Al-Si intermetallic compound layer at the interface between the base steel sheet and the plating film.
  • the Si content in the plating film must be 0.01 mass% or more.
  • the Si content in the plating film exceeds 2 mass%, not only will the effect of suppressing the growth of the interfacial alloy layer described above saturate, but the presence of excess Si in the plating film will also promote corrosion, so the Si content is set to 2 mass% or less.
  • Mg in the plating film has a function of stabilizing the corrosion products formed during corrosion, and is an essential element for obtaining excellent corrosion resistance.
  • the Mg content in the plating film needs to be 3 mass% or more, and to obtain a more reliable effect, it is preferable that the Mg content is 5 mass% or more.
  • the Mg content in the plating film exceeds 10 mass %, the plating film becomes hard and brittle, and the workability deteriorates, so the upper limit of the Mg content is set to 10 mass %.
  • the Mg content in the plating film is preferably 5 to 8 mass %, and more preferably 6 to 8 mass %.
  • the plating film contains unavoidable impurities.
  • the unavoidable impurities include Fe.
  • This Fe is inevitably contained in the plating film as a result of dissolution of the steel sheet or bath-immersed equipment into the plating bath, and as a result of being supplied by diffusion from the base steel sheet when the interfacial alloy layer is formed.
  • the Fe content in the plating film is usually about 0.1 to 0.5 mass%.
  • the plating film preferably further contains, as necessary, one or more elements selected from the group consisting of B, Ca, Ti, V, Cr, Mn, Co, Ni, Sr, In, Sn, Sb, Ce, Pb and Bi in a total amount of 0.1 to 5 mass %.
  • elements selected from the group consisting of B, Ca, Ti, V, Cr, Mn, Co, Ni, Sr, In, Sn, Sb, Ce, Pb and Bi in a total amount of 0.1 to 5 mass %.
  • the plating film is composed of an interface alloy layer 22 present at the interface with the base steel sheet 10 and a main layer 21 present on the interface alloy layer 22.
  • the cross sections of the base steel plate 10, the main layer 21 and the interface alloy layer 22 are shown diagrammatically for the convenience of explanation, and the actual shapes, dimensions, etc. differ from those shown in Figures 1 to 3.
  • the interfacial alloy layer is formed in the plating process by the reaction of the base steel sheet with bath components such as Zn, Al, Mg, and Si in the plating bath, and is generally an Fe-Al and/or Fe-Al-Si intermetallic compound.
  • the base steel sheet may be pre-plated with Ni, Fe, or the like before the plating process in order to ensure wettability.
  • Ni-Al and/or Fe-Ni-Al intermetallic compounds containing Ni are formed as the interface alloy layer.
  • the interfacial alloy layer exists with an average thickness of 0.1 to 1 ⁇ m, a stable main layer can be formed on the interfacial alloy layer.
  • the average thickness is less than 0.1 ⁇ m, the interfacial alloy layer may not be formed over the entire plating film, i.e., the base steel sheet and the plating bath may not react, which may result in a stable plating adhesion and film formation.
  • the average thickness exceeds 1 ⁇ m, the interfacial alloy layer may crack during processing, causing the plating to peel off. Therefore, it is preferable that the average thickness of the interfacial alloy layer is 0.1 to 1 ⁇ m.
  • the plating bath components that were not consumed in the formation of the interface alloy layer 22 are solidified in the main layer, and thus mainly an Al phase, a Zn phase, and MgZn2 are formed.
  • the Al phase is a necessary structure for obtaining stable and excellent corrosion resistance, and when observing a cross section of the plating film in the thickness direction, the area ratio occupied by the Al phase is preferably 30% or more, and more preferably 40% or more.
  • the area ratio of MgZn2 present in the main layer 21 is 30% or more. Since MgZn 2 present in the main layer 21 has the function of preferentially dissolving in the initial stage when the plating film corrodes and stabilizing the formed corrosion product, the preferential dissolution of MgZn 2 in the initial stage of corrosion of the plating film 20 allows stable corrosion products to be formed early, and the corrosion rate of the plating film can be reduced. In addition, since the MgZn 2 is a hard intermetallic compound, the presence of the MgZn 2 in the plating main layer can improve the scratch resistance of the plating film.
  • the area ratio of MgZn2 present in the main layer 21 is preferably 40% or more, and more preferably 50% or more.
  • the area ratio of the MgZn 2 having a portion exposed on the outermost plating surface among the observed MgZn 2 is preferably 30% or more, more preferably 40% or more.
  • the area ratio of MgZn 2 having a portion exposed on the surface of the plating film 20 is made by making the area ratio of MgZn 2 having a portion exposed on the plating surface among the observed MgZn 2 30% or more, it is possible to achieve both corrosion resistance and scratch resistance at a higher level.
  • the area ratio of the MgZn 2 present in the main layer 21 within 50% of the thickness range from the surface of the main layer 21 is preferably more than 50%, and more preferably 60% or more.
  • the presence of a large amount of MgZn 2 on the surface side of the plating film 20 can further suppress surface scratches.
  • the area ratio of the MgZn 2 present in the thickness range from 50% of the surface of the main layer 21 is more than 50%, so that both corrosion resistance and scratch resistance can be achieved at a higher level.
  • the Al phase formed in the main layer is a structure necessary for obtaining stable excellent corrosion resistance, and when a cross section of the plating film is observed in the thickness direction, the area ratio occupied by the Al phase is preferably 30% or more, and more preferably 40% or more. Furthermore, in order to obtain the effect of improving corrosion resistance brought about by the Al phase, it is sufficient that the Al phase occupies a certain proportion in the main layer 21, and there is no limitation on the distribution location in the main layer.
  • the area ratio of the Al phase present within a thickness range of up to 50% from the surface of the main layer 21 is less than 50%, as shown in Fig. 3.
  • the method for observing the cross section of the plating film 20 in the thickness direction is not particularly limited as long as it is a method that can observe the distribution state of the MgZn2 and Al phases in the main layer 21.
  • the cross section can be observed and measured by SEM-EDX (energy dispersive X-ray analysis using a scanning electron microscope).
  • the coating weight of the plating film is preferably 30 to 300 g/ m2 per side.
  • the coating weight of the plating film is 30 g/ m2 or more, sufficient corrosion resistance is obtained for applications requiring long-term corrosion resistance, such as building materials, while when the coating weight of the plating film is 300 g/m2 or less , excellent corrosion resistance can be achieved while suppressing the occurrence of plating cracks during processing.
  • the coating weight of the plating film is more preferably 50 to 150 g/ m2 .
  • the amount of plating adhesion can be calculated, for example, by dissolving and peeling off a specific area of the plating film in a mixture of hydrochloric acid and hexamethylenetetramine as specified in JIS H 0401:2013, and calculating the difference in the weight of the steel sheet before and after peeling. To determine the amount of plating adhesion per side using this method, the non-target side is sealed with tape so that the plated surface is not exposed, and then the dissolution described above is carried out.
  • a plating film 20 is formed on a base steel sheet 10, but an intermediate layer or a coating film can also be further formed on the plating film, if necessary.
  • the type of the coating film and the method for forming the coating film are not particularly limited and can be appropriately selected depending on the required performance.
  • the coating film can be formed by a method such as roll coater coating, curtain flow coating, spray coating, etc. After coating the coating material containing an organic resin, the coating film can be formed by heating and drying the coating film by means of hot air drying, infrared heating, induction heating, etc.
  • the intermediate layer is not particularly limited as long as it is a layer formed between the plating film of the hot-dip Zn-Al-Mg-plated steel sheet and the coating film.
  • examples include a chemical conversion coating film and a primer such as an adhesive layer.
  • the chemical conversion coating film can be formed, for example, by a chromate treatment or a chromium-free chemical conversion treatment in which a chromate treatment liquid or a chromium-free chemical conversion coating liquid is applied, and then dried at a steel sheet temperature of 80 to 300°C without rinsing with water.
  • These chemical conversion coating films may be single-layered or multi-layered, and in the case of multi-layered films, multiple chemical conversion treatments may be performed sequentially.
  • the method for producing the hot-dip Zn-Al-Mg plated steel sheet of the present invention is not particularly limited.
  • the plating film of the hot-dip Zn-Al-Mg plated steel sheet obtained by the present invention has a composition generally equivalent to that of the plating bath. Therefore, the present invention includes a step of forming the plating film on the base steel sheet using a plating bath whose composition is controlled to contain 10-25 mass% Al, 0.01-2 mass% Si, 3-10 mass% Mg, with the remainder being Zn and unavoidable impurities.
  • the step of forming the plating film is not particularly limited except for the composition of the plating bath described above.
  • the steel sheet can be produced by cleaning, heating, and immersing the base steel sheet in a coating bath in a continuous hot-dip galvanizing facility.
  • recrystallization annealing or the like is performed to control the structure of the base steel sheet itself, and heating in a reducing atmosphere such as a nitrogen-hydrogen atmosphere is effective in preventing oxidation of the steel sheet and reducing a small amount of oxide film present on the surface.
  • the temperature of the plating bath is not particularly limited, but is preferably in the range of (melting point + 20°C) to 550°C.
  • the reason why the lower limit of the bath temperature is set to the melting point + 20° C. is that the bath temperature needs to be equal to or higher than the solidification point in order to perform hot-dip plating, and by setting the temperature to the melting point + 20° C., solidification due to a local drop in the bath temperature of the plating bath is prevented.
  • the reason why the upper limit of the bath temperature is set to 550° C. is that if the bath temperature exceeds 550° C., rapid cooling of the plating film becomes difficult, and there is a risk that the interfacial alloy layer formed between the plating film and the steel sheet becomes thick.
  • the method for controlling the area ratio of MgZn2 in the main layer to 30% or more is not particularly limited.
  • it can be formed by adding MgZn2 to a plating bath and performing hot-dip plating, or by spraying MgZn2 powder on the surface of the steel sheet where the plating has not solidified immediately after the hot-dip plating process.
  • the method for controlling the area ratio of MgZn2 having a portion exposed on the outermost coating surface to 30% or more among the observed MgZn2 can be formed by a method of spraying MgZn2 powder on the surface of a steel sheet where the coating has not yet solidified immediately after hot-dip coating. Furthermore, there is no particular limitation on the method for controlling the area ratio of MgZn2 existing within a thickness range of 50% from the surface of the main layer to exceed 50%.
  • it can be formed by a method of manufacturing a Zn-Al-Mg-based plated steel sheet by a normal hot-dip plating process, and then subjecting the steel sheet to a second hot-dip plating process in a hot-dip Zn-Al-Mg plating bath containing MgZn2 , or by a method of spraying MgZn2 powder on the surface of a steel sheet where the plating has not yet solidified immediately after the hot-dip plating process.
  • the base steel sheet constituting the Zn-Al-Mg-plated steel sheet of the present invention is not particularly limited, and a cold-rolled steel sheet, a hot-rolled steel sheet, or the like can be used as appropriate depending on the required performance and specifications.
  • the base steel sheet is also not particularly limited.
  • the method for obtaining the base steel sheet is not particularly limited.
  • the hot-rolled steel sheet one that has been subjected to a hot rolling process and a pickling process can be used, and in the case of the cold-rolled steel sheet, it can be manufactured by further adding a cold rolling process.
  • a pre-plated steel sheet may also be used as the base steel sheet.
  • the pre-plated steel sheet is plated, for example, by an electrolytic treatment method or a displacement plating method.
  • the base steel sheet may be immersed in a sulfate bath or a chloride bath containing metal ions of various pre-plating components to perform electrolytic treatment.
  • the displacement plating method the base steel sheet may be immersed in an aqueous solution containing metal ions of various pre-plating components and having a pH adjusted with sulfuric acid to cause displacement precipitation of metal.
  • a representative example of a pre-plated steel sheet is a Ni pre-plated steel sheet.
  • Examples 1-2 (Manufacturing method A:) A cold-rolled steel sheet having a thickness of 0.8 mm, manufactured by a conventional method, was used as a base steel sheet, and annealing and plating were performed using a hot-dip plating simulator manufactured by Rhesca Corporation to produce hot-dip Zn-Al-Mg plated steel sheet samples 1 and 2 under the conditions shown in Table 1.
  • Table 1 shows the composition and bath temperature of the plating bath used in the production of the hot-dip Zn-Al-Mg plated steel sheets, and the composition and coating weight of the plating film of each sample.
  • Table 1 shows the composition and bath temperature of the plating bath used in the production of the hot-dip Zn-Al-Mg plated steel sheets, as well as the composition and coating weight of the plating film of each sample.
  • Example 10 (Manufacturing method C:) A 0.8 mm thick cold-rolled steel sheet manufactured by conventional methods was pre-plated with Ni and used as the base steel sheet. This was annealed and hot-dip plated in a hot-dip plating simulator manufactured by Rhesca Corporation, and then powdered MgZn2 (average particle size: 2 ⁇ m or less) was sprayed onto the plated surface before the plating solidified to produce sample 10 of hot-dip Zn-Al-Mg plated steel sheet with the conditions shown in Table 1.
  • the Ni pre-plating treatment was performed using a plating bath with a concentration of NiSO4.6H2O of 300g/L, a concentration of H3BO3 of 40g/L, a concentration of Na2SO4 of 100g/L, and a pH of 2.7, under conditions of a bath temperature of 60°C and a current density of 50A/ dm2 , with the Ni deposition weight controlled to be 1g/ m2 .
  • a plating film with the composition shown in Table 1 was obtained by appropriately adjusting the deposition weight of the hot-dip Zn-Al-Mg-based plating and the deposition weight of the sprayed MgZn2 , a plating film with the composition shown in Table 1 was obtained.
  • Table 1 shows the composition and bath temperature of the plating bath used in the production of the hot-dip Zn-Al-Mg plated steel sheets, as well as the composition and coating weight of the plating film of each sample.
  • Table 1 show that the samples of the present invention have a good balance of corrosion resistance and scratch resistance compared to the samples of the comparative examples.
  • the present invention provides hot-dip Zn-Al-Mg plated steel sheets that combine high levels of corrosion resistance and scratch resistance.
  • Base steel sheet 20 Plating film 21: Main layer 22: Interface alloy layer

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Coating With Molten Metal (AREA)

Abstract

Le but de la présente invention est de fournir une tôle d'acier plaquée à base de zinc-aluminium-magnésium fondu qui présente une résistance à la corrosion et une résistance aux rayures élevées.　Afin d'atteindre ce but, la présente invention divulgue une tôle d'acier plaquée à base de zinc-aluminium-magnésium fondu comprenant un film de placage (20) formé à partir d'une couche d'alliage d'interface (22) et d'une couche principale (21), la couche d'alliage d'interface (22) étant présente à côté d'une tôle d'acier de base (10) en tant qu'interface, et la couche principale (21) étant présente sur la couche d'alliage d'interface (22). La tôle d'acier plaquée à base de zinc-aluminium-magnésium fondu est caractérisée en ce que le film de placage (20) contient de 10 à 22 % en masse d'Al, de 0,01 à 2 % en masse de Si et de 3 à 10 % en masse de Mg, le reste étant du Zn et des impuretés inévitables, et que le pourcentage de la zone de MgZn2 présente dans la couche principale (21) est de 30 % ou plus lorsqu' observée en coupe transversale prise dans la direction de l'épaisseur du film de placage (20).
PCT/JP2024/040736 2023-12-04 2024-11-15 Tôle d'acier plaquée à base de zinc-aluminium-magnésium fondu Pending WO2025121109A1 (fr)

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JP2023-204929 2023-12-04
JP2023204929 2023-12-04

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Publication number Priority date Publication date Assignee Title
WO2018139620A1 (fr) * 2017-01-27 2018-08-02 新日鐵住金株式会社 Matériau d'acier plaqué
JP2021172878A (ja) * 2020-04-30 2021-11-01 日本製鉄株式会社 加工性と耐食性に優れる溶融Ｚｎ−Ａｌ−Ｍｇ系めっき鋼材
WO2022080004A1 (fr) * 2020-10-16 2022-04-21 日本製鉄株式会社 Feuille d'acier plaquée de zn par immersion à chaud
WO2022107837A1 (fr) * 2020-11-18 2022-05-27 日本製鉄株式会社 Matériau d'acier plaqué
WO2024048646A1 (fr) * 2022-08-30 2024-03-07 日本製鉄株式会社 Matériau d'acier plaqué
JP2024519995A (ja) * 2022-03-31 2024-05-21 ヒュンダイ スチール カンパニー 加工性および耐食性に優れためっき鋼材
WO2024185849A1 (fr) * 2023-03-07 2024-09-12 日本製鉄株式会社 Matériau d'acier plaqué

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2018139620A1 (fr) * 2017-01-27 2018-08-02 新日鐵住金株式会社 Matériau d'acier plaqué
JP2021172878A (ja) * 2020-04-30 2021-11-01 日本製鉄株式会社 加工性と耐食性に優れる溶融Ｚｎ−Ａｌ−Ｍｇ系めっき鋼材
WO2022080004A1 (fr) * 2020-10-16 2022-04-21 日本製鉄株式会社 Feuille d'acier plaquée de zn par immersion à chaud
WO2022107837A1 (fr) * 2020-11-18 2022-05-27 日本製鉄株式会社 Matériau d'acier plaqué
JP2024519995A (ja) * 2022-03-31 2024-05-21 ヒュンダイ スチール カンパニー 加工性および耐食性に優れためっき鋼材
WO2024048646A1 (fr) * 2022-08-30 2024-03-07 日本製鉄株式会社 Matériau d'acier plaqué
WO2024185849A1 (fr) * 2023-03-07 2024-09-12 日本製鉄株式会社 Matériau d'acier plaqué

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