KR102043519B1 - Hot dip aluminium alloy plated steel sheet having excellent corrosion resistance and weldability, method for manufacturing the same - Google Patents
Hot dip aluminium alloy plated steel sheet having excellent corrosion resistance and weldability, method for manufacturing the same Download PDFInfo
- Publication number
- KR102043519B1 KR102043519B1 KR1020170177677A KR20170177677A KR102043519B1 KR 102043519 B1 KR102043519 B1 KR 102043519B1 KR 1020170177677 A KR1020170177677 A KR 1020170177677A KR 20170177677 A KR20170177677 A KR 20170177677A KR 102043519 B1 KR102043519 B1 KR 102043519B1
- Authority
- KR
- South Korea
- Prior art keywords
- steel sheet
- aluminum alloy
- layer
- weldability
- corrosion resistance
- Prior art date
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 95
- 239000010959 steel Substances 0.000 title claims abstract description 95
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 54
- 230000007797 corrosion Effects 0.000 title claims abstract description 37
- 238000005260 corrosion Methods 0.000 title claims abstract description 37
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 10
- 238000000034 method Methods 0.000 title claims description 17
- 238000007747 plating Methods 0.000 claims abstract description 101
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 84
- 239000000956 alloy Substances 0.000 claims abstract description 84
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 17
- 229910052742 iron Inorganic materials 0.000 claims abstract description 16
- 239000010410 layer Substances 0.000 claims description 117
- 238000002844 melting Methods 0.000 claims description 21
- 230000008018 melting Effects 0.000 claims description 21
- 239000002356 single layer Substances 0.000 claims description 10
- 238000001816 cooling Methods 0.000 claims description 9
- 238000000926 separation method Methods 0.000 claims description 4
- 229910052725 zinc Inorganic materials 0.000 claims description 4
- 238000000445 field-emission scanning electron microscopy Methods 0.000 claims 2
- 238000007654 immersion Methods 0.000 claims 1
- 230000000052 comparative effect Effects 0.000 description 32
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 29
- 229910015372 FeAl Inorganic materials 0.000 description 14
- 238000003466 welding Methods 0.000 description 14
- 229910000905 alloy phase Inorganic materials 0.000 description 10
- 229910001338 liquidmetal Inorganic materials 0.000 description 6
- 239000000203 mixture Substances 0.000 description 6
- 238000004458 analytical method Methods 0.000 description 5
- 238000002149 energy-dispersive X-ray emission spectroscopy Methods 0.000 description 5
- 239000012535 impurity Substances 0.000 description 5
- 238000009616 inductively coupled plasma Methods 0.000 description 5
- 229910018084 Al-Fe Inorganic materials 0.000 description 4
- 229910018192 Al—Fe Inorganic materials 0.000 description 4
- VEXZGXHMUGYJMC-UHFFFAOYSA-N Hydrochloric acid Chemical compound Cl VEXZGXHMUGYJMC-UHFFFAOYSA-N 0.000 description 4
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 4
- ZNEMGFATAVGQSF-UHFFFAOYSA-N 1-(2-amino-6,7-dihydro-4H-[1,3]thiazolo[4,5-c]pyridin-5-yl)-2-[5-[2-(2,3-dihydro-1H-inden-2-ylamino)pyrimidin-5-yl]-1,3,4-oxadiazol-2-yl]ethanone Chemical compound NC=1SC2=C(CN(CC2)C(CC=2OC(=NN=2)C=2C=NC(=NC=2)NC2CC3=CC=CC=C3C2)=O)N=1 ZNEMGFATAVGQSF-UHFFFAOYSA-N 0.000 description 3
- DEXFNLNNUZKHNO-UHFFFAOYSA-N 6-[3-[4-[2-(2,3-dihydro-1H-inden-2-ylamino)pyrimidin-5-yl]piperidin-1-yl]-3-oxopropyl]-3H-1,3-benzoxazol-2-one Chemical compound C1C(CC2=CC=CC=C12)NC1=NC=C(C=N1)C1CCN(CC1)C(CCC1=CC2=C(NC(O2)=O)C=C1)=O DEXFNLNNUZKHNO-UHFFFAOYSA-N 0.000 description 3
- NIPNSKYNPDTRPC-UHFFFAOYSA-N N-[2-oxo-2-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)ethyl]-2-[[3-(trifluoromethoxy)phenyl]methylamino]pyrimidine-5-carboxamide Chemical compound O=C(CNC(=O)C=1C=NC(=NC=1)NCC1=CC(=CC=C1)OC(F)(F)F)N1CC2=C(CC1)NN=N2 NIPNSKYNPDTRPC-UHFFFAOYSA-N 0.000 description 3
- AFCARXCZXQIEQB-UHFFFAOYSA-N N-[3-oxo-3-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)propyl]-2-[[3-(trifluoromethoxy)phenyl]methylamino]pyrimidine-5-carboxamide Chemical compound O=C(CCNC(=O)C=1C=NC(=NC=1)NCC1=CC(=CC=C1)OC(F)(F)F)N1CC2=C(CC1)NN=N2 AFCARXCZXQIEQB-UHFFFAOYSA-N 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 229910001335 Galvanized steel Inorganic materials 0.000 description 2
- 239000011248 coating agent Substances 0.000 description 2
- 238000000576 coating method Methods 0.000 description 2
- 239000008397 galvanized steel Substances 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 229910018137 Al-Zn Inorganic materials 0.000 description 1
- 229910018573 Al—Zn Inorganic materials 0.000 description 1
- 229910017813 Cu—Cr Inorganic materials 0.000 description 1
- 101000993059 Homo sapiens Hereditary hemochromatosis protein Proteins 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 239000012267 brine Substances 0.000 description 1
- KRVSOGSZCMJSLX-UHFFFAOYSA-L chromic acid Substances O[Cr](O)(=O)=O KRVSOGSZCMJSLX-UHFFFAOYSA-L 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- AWJWCTOOIBYHON-UHFFFAOYSA-N furo[3,4-b]pyrazine-5,7-dione Chemical compound C1=CN=C2C(=O)OC(=O)C2=N1 AWJWCTOOIBYHON-UHFFFAOYSA-N 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 239000010731 rolling oil Substances 0.000 description 1
- 150000003839 salts Chemical class 0.000 description 1
- 238000004088 simulation Methods 0.000 description 1
- HPALAKNZSZLMCH-UHFFFAOYSA-M sodium;chloride;hydrate Chemical compound O.[Na+].[Cl-] HPALAKNZSZLMCH-UHFFFAOYSA-M 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 238000004506 ultrasonic cleaning Methods 0.000 description 1
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/10—Alloys based on aluminium with zinc 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
- C23C2/12—Aluminium 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
-
- 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
- C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
- C23C2/29—Cooling or quenching
-
- 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
- C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
- C23C2/36—Elongated material
- C23C2/40—Plates; Strips
-
- 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
- C23C2/50—Controlling or regulating the coating processes
- C23C2/52—Controlling or regulating the coating processes with means for measuring or sensing
- C23C2/526—Controlling or regulating the coating processes with means for measuring or sensing for visually inspecting the surface quality of the substrate
-
- 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
- C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
- C23C28/02—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings only including layers of metallic material
- C23C28/023—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings only including layers of metallic material only coatings of metal elements only
-
- 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
- C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
- C23C28/02—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings only including layers of metallic material
- C23C28/028—Including graded layers in composition or in physical properties, e.g. density, porosity, grain size
-
- 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
- C23C30/00—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process
Abstract
본 발명은 내식성 및 용접성이 우수한 용융 알루미늄 합금 도금강판과 이를 제조하는 방법에 관한 것이다.
본 발명의 한가지 측면에 따른 도금강판은 강판 표면에 형성된 용융 알루미늄 합금 도금 피막으로 이루어지고, 상기 도금 피막은 강판과의 계면에 존재하는 계면 합금층과 상기 계면 합금층 상에 존재하는 도금 상층을 포함하고, 계면 합금층과 소지강판의 경계로부터 계면 합금층 방향으로 1㎛ 이내의 위치에 존재하는 상 중 Fe와 Al의 원자비가 1:2.8~1:3.3 사이의 비율을 가지는 상의 비율이 면적 기준으로 70% 이상인 내식성 및 용접성이 우수한 용융 알루미늄 합금 도금강판일 수 있다.The present invention relates to a hot-dip aluminum alloy plated steel sheet excellent in corrosion resistance and weldability and a method of manufacturing the same.
The plated steel sheet according to one aspect of the present invention consists of a molten aluminum alloy plated film formed on the surface of the steel sheet, the plated film includes an interfacial alloy layer present at the interface with the steel plate and an upper plating layer present on the interface alloy layer The ratio of phases having an atomic ratio between Fe and Al of 1: 2.8 to 1: 3.3 among the phases existing at a position within 1 μm from the boundary between the interface alloy layer and the base steel sheet in the direction of the interface alloy layer is based on the area. It may be a molten aluminum alloy plated steel sheet having excellent corrosion resistance and weldability of 70% or more.
Description
본 발명은 내식성 및 용접성이 우수한 용융 알루미늄 합금 도금강판과 이를 제조하는 방법에 관한 것이다.The present invention relates to a hot-dip aluminum alloy plated steel sheet excellent in corrosion resistance and weldability and a method of manufacturing the same.
용융 Al-Zn계 도금강판은 Zn 의 희생 방식성과 Al 의 높은 내식성이 양립 하고 있기 때문에, 다른 용융 아연 도금 강판에 비해 우수한 내식성을 나타낸다. Since molten Al-Zn-based galvanized steel sheet is compatible with sacrificial corrosion resistance of Zn and high corrosion resistance of Al, it exhibits excellent corrosion resistance compared to other hot dip galvanized steel sheets.
관련하여, 특허문헌 1은, Al: 25~75중량%, Mg: 0.1~10중량%, Si: 1~7.5중량%, Cr: 0.05~5중량%, 잔부 Zn 및 불가피한 불순물로 이루어지는 합금 도금을 실시하여 내식성을 향상시킨 기술을 개시하고 있다.In this regard, Patent Document 1 discloses an alloy plating consisting of Al: 25 to 75% by weight, Mg: 0.1 to 10% by weight, Si: 1 to 7.5% by weight, Cr: 0.05 to 5% by weight, balance Zn, and unavoidable impurities. The technique which performed and improved corrosion resistance is disclosed.
그러나 상기의 도금 성분계는 Cr 등 고융점 금속 첨가로 인한 도금욕 융점 상승으로, 도금욕 중 드로스 발생의 문제와 자동차용 기가급 강재에 적용시 재질 열화의 문제가 있으며, Al과의 고융점 합금상 미형성으로 인해 용접시 액상 금속 취화가 발생되는 등의 문제가 있다.However, the above-described plating component system has a problem of dross generation in the plating bath due to the addition of a high melting point metal such as Cr, a problem of dross generation in the plating bath, and a material deterioration when applied to a giga-grade steel for automobiles, and a high melting point alloy with Al. Due to the phase formation, there is a problem that liquid metal embrittlement occurs during welding.
또한, 도금욕에 따라서 소지강판과 도금층의 결합이 충분하지 못하여 도금층이 박리되는 등 도금 밀착성이 불량하다는 문제도 발생할 우려가 있다.In addition, there may be a problem in that the plating adhesion is poor, such as insufficient bonding between the base steel sheet and the plating layer depending on the plating bath.
본 발명의 여러 목적 중 하나는, 용접성 및 내식성이 우수한 용융 알루미늄 합금 도금강판을 제공하는 것이다.One of several objects of the present invention is to provide a molten aluminum alloy plated steel sheet excellent in weldability and corrosion resistance.
본 발명의 또다른 목적은 도금 밀착성이 우수한 용융 알루미늄 합금 도금 강판을 제공하는 것이다.Another object of the present invention is to provide a molten aluminum alloy plated steel sheet excellent in plating adhesion.
본 발명의 과제는 상술한 사항에 한정되지 아니한다. 본 발명의 추가적인 과제는 명세서 전반적인 내용에 기술되어 있으며, 본 발명이 속하는 기술분야에서 통상의 지식을 가지는 자라면 본 발명의 명세서에 기재된 내용으로부터 본 발명의 추가적인 과제를 이해하는데 아무런 어려움이 없을 것이다.The subject of this invention is not limited to the above-mentioned matter. Further objects of the present invention are described in the general description, and those skilled in the art will have no difficulty understanding the additional objects of the present invention from the contents described in the specification of the present invention.
본 발명의 한가지 측면에 따른 도금강판은 강판 표면에 형성된 용융 알루미늄 합금 도금 피막으로 이루어지고, 상기 도금 피막은 강판과의 계면에 존재하는 계면 합금층과 상기 계면 합금층 상에 존재하는 도금 상층을 포함하고, 계면 합금층과 소지강판의 경계로부터 계면 합금층 방향으로 1㎛ 이내의 위치에 존재하는 상 중 Fe와 Al의 원자비가 1:2.8~1:3.3 사이의 비율을 가지는 상의 비율이 면적 기준으로 70% 이상인 내식성 및 용접성이 우수한 용융 알루미늄 합금 도금강판일 수 있다.The plated steel sheet according to one aspect of the present invention consists of a molten aluminum alloy plated film formed on the surface of the steel sheet, the plated film includes an interfacial alloy layer present at the interface with the steel plate and a plating upper layer present on the interface alloy layer The ratio of phases having an atomic ratio between Fe and Al of 1: 2.8 to 1: 3.3 among the phases existing at a position within 1 μm from the boundary between the interface alloy layer and the base steel sheet in the direction of the interface alloy layer is based on the area. It may be a molten aluminum alloy plated steel sheet having excellent corrosion resistance and weldability of 70% or more.
본 발명의 다른 한가지 측면에 따르면, 강판 표면에 형성된 용융 알루미늄 합금 도금 피막으로 이루어지고, 상기 도금 피막은 강판과의 계면에 존재하는 계면 합금층과 상기 계면 합금층 상에 존재하는 도금 상층을 포함하고, 계면 합금층 중 Fe와 Al의 원자비가 1:2.2~1:2.7 사이의 비율을 가지는 상의 비율이 면적 기준으로 10% 이하인 내식성 및 용접성이 우수한 용융 알루미늄 도금강판이 제공될 수 있다.According to another aspect of the present invention, it is made of a molten aluminum alloy plated film formed on the surface of the steel sheet, the plated film includes an interfacial alloy layer present at the interface with the steel plate and a plating upper layer present on the interface alloy layer; In the interfacial alloy layer, a molten aluminum plated steel sheet having excellent corrosion resistance and weldability may be provided in which the ratio of the phase ratio of Fe and Al in the ratio of 1: 2.2 to 1: 2.7 is 10% or less on an area basis.
본 발명의 또다른 한가지 측면에 따르면, 강판 표면에 형성된 용융 알루미늄 합금 도금 피막으로 이루어지고, 상기 도금 피막은 강판과의 계면에 존재하는 계면 합금층과 상기 계면 합금층 상에 존재하는 도금 상층을 포함하고, 상기 계면합금층은 단층 구조이며, 계면 합금층의 두께 방향 중심부의 성분을 분석하였을 때, Fe와 Al의 원자비가 1:2.8~1:3.3 사이의 비율을 가지는 내식성 및 용접성이 우수한 용융 알루미늄 도금강판이 제공될 수 있다.According to another aspect of the present invention, it is made of a molten aluminum alloy plating film formed on the surface of the steel sheet, the plating film includes an interfacial alloy layer present at the interface with the steel sheet and a plating upper layer present on the interface alloy layer The interfacial alloy layer has a single layer structure, and when the components in the thickness direction of the interfacial alloy layer are analyzed, the molten aluminum having excellent corrosion resistance and weldability having an atomic ratio of Fe to Al of 1: 2.8 to 1: 3.3. Plated steel sheet may be provided.
본 발명의 또다른 일 측면은, 소지강판을 준비하는 단계; 상기 준비된 소지강판을 용융 알루미늄 합금 도금욕에 침지하여 도금하는 단계; 및 상기 도금 후 냉각하는 단계를 포함하고, 상기 도금욕의 온도는 도금욕 융점 + 30℃ 이하이고, 도금욕에서 배출된 소지강판의 표면 온도가 2초 이내에 도금욕 융점 온도 이하가 되도록 냉각하는 내식성 및 용접성이 우수한 용융 알루미늄 합금 도금강판의 제조방법에 관한 것이다.Another aspect of the invention, preparing a steel sheet; Plating the prepared steel sheet by immersing it in a molten aluminum alloy plating bath; And cooling after the plating, wherein the temperature of the plating bath is a melting point of the plating bath + 30 ° C. or less, and the cooling temperature is lowered to allow the surface temperature of the base steel sheet discharged from the plating bath to be below the melting temperature of the plating bath within 2 seconds. And it relates to a method for producing a molten aluminum alloy plated steel sheet excellent in weldability.
본 발명의 여러 효과 중 하나로서, 본 발명의 일 실시예에 따른 용융 알루미늄 합금 도금강판은 도금 강재는 용접성 및 내식성이 우수한 장점이 있다.As one of several effects of the present invention, the molten aluminum alloy plated steel sheet according to an embodiment of the present invention has the advantage that the plated steel is excellent in weldability and corrosion resistance.
도 1은 비교예 1의 도금 피막 단면을 관찰한 사진이다.
도 2는 발명예 2의 도금 피막 단면을 관찰한 사진이다.
도 3은 발명예 4의 용접 후 단면을 관찰한 사진이다.
도 4는 비교예 7의 용접 후 단면을 관찰한 사진이다.1 is a photograph observing a plated film cross section of Comparative Example 1. FIG.
2 is a photograph observing a plated film cross section of Inventive Example 2. FIG.
3 is a photograph observing a cross section after welding in Inventive Example 4. FIG.
4 is a photograph observing a cross section after welding in Comparative Example 7.
이하, 본 발명에 대해서 상세히 설명한다. 먼저, 본 발명의 일 측면인 내식성 및 용접성이 우수한 용융 알루미늄 합금 도금강판에 대해서 상세히 설명한다.EMBODIMENT OF THE INVENTION Hereinafter, this invention is demonstrated in detail. First, a molten aluminum alloy plated steel sheet excellent in corrosion resistance and weldability, which is an aspect of the present invention, will be described in detail.
본 발명의 일 측면인 용융 알루미늄 합금 도금강판은, 소지강판 및 용융 알루미늄 합금 도금 피막(이하, 도금 피막)을 포함한다. 상기 도금 피막은 소지강판의 일면 또는 양면에 형성될 수 있다. A molten aluminum alloy plated steel sheet which is one aspect of the present invention includes a base steel sheet and a molten aluminum alloy plated film (hereinafter, referred to as a plated film). The plating film may be formed on one surface or both surfaces of the steel sheet.
상기 도금 피막은 강판과의 계면에 존재하는 계면 합금층과 상기 계면 합금층 상에 존재하는 도금 상층으로 이루어진다. 통상, 계면 합금층 중 소지강판과 근접한 위치에는 Fe 함량이 높은 Fe2Al5 상이 층상으로 형성되나, 본 발명의 한가지 구현례에서는 계면 합금층 중 소지강판과 근접한 위치에 FeAl3 상이 형성된다.The plating film is composed of an interfacial alloy layer present at the interface with the steel sheet and an upper plating layer present on the interfacial alloy layer. In general, the Fe 2 Al 5 phase having a high Fe content is formed in a layer position at a position close to the base steel sheet in the interfacial alloy layer, but in one embodiment of the present invention, the FeAl 3 phase is formed at a position close to the base steel sheet in the interfacial alloy layer.
도 1은 종래 알루미늄 합금 도금강판의 계면 합금층을 모사한 것을 나타낸 것으로서, 후술하는 실시예 중 비교예 1의 계면 합금층을 주사전자현미경(Scanning Electron Microscope, SEM)으로 관찰한 것이다. 반면, 도 2는 후술하는 실시예 중 발명예 2의 알루미늄 합금 도금강판의 계면 합금층을 관찰한 주사전자현미경(Scanning Electron Microscope, SEM) 사진이다. FIG. 1 shows a simulation of an interfacial alloy layer of a conventional aluminum alloy plated steel sheet, and the interfacial alloy layer of Comparative Example 1 was observed by a scanning electron microscope (Scanning Electron Microscope, SEM). On the other hand, Figure 2 is a scanning electron microscope (Scanning Electron Microscope, SEM) photographs observed the interfacial alloy layer of the aluminum alloy plated steel sheet of the invention example 2 of the examples to be described later.
도 1에 나타낸 종래의 알루미늄 합금 도금강판의 계면 합금층의 경우, 계면 합금층이 복층으로 구성되어 있는 것을 알 수 있다. 이 중, 하부의 계면 합금층은 경질(hard)의 Fe-Al계 합금상인 Fe2Al5로 구성되며, 이러한 경질(hard)의 Fe-Al계 합금상은 점 용접시 액상 금속 취화 (Liquid Metal Embrittlement, LME) 를 유발하거나 도금층의 박리를 유발하는 문제가 있었다.In the case of the interface alloy layer of the conventional aluminum alloy plated steel sheet shown in FIG. 1, it turns out that an interface alloy layer is comprised by multiple layers. Among these, the lower interfacial alloy layer is composed of a hard Fe-Al alloy phase Fe 2 Al 5 , and this hard Fe-Al alloy phase is liquid metal embrittlement during spot welding (Liquid Metal Embrittlement) , LME) or a problem of causing peeling of the plating layer.
그러나 도 2의 나타낸 본 발명의 일 실시예에 따른 알루미늄 합금 도금강판의 경우 계면 합금층이 단층 구조를 가지는 것을 알 수 있으며, 이러한 단층의 계면 합금층은 FeAl3을 주성분으로 하는 것이다. 따라서, 계면 합금층 중 소지강판과 근접한 위치에서 Fe2Al5와 같은 경질의 Fe-Al계 합금상이 실질적으로 존재하지 아니하여, 점 용접시 액상 금속 취화 (Liquid Metal Embrittlement, LME) 의 발생을 효과적으로 방지할 수 있게 된다.However, in the case of the aluminum alloy plated steel sheet according to the embodiment of the present invention shown in FIG. 2, it can be seen that the interfacial alloy layer has a single layer structure, and the interfacial alloy layer of the single layer has FeAl 3 as a main component. Therefore, hard Fe-Al-based alloy phases such as Fe 2 Al 5 do not substantially exist in the position close to the base steel sheet in the interfacial alloy layer, thereby effectively generating liquid metal embrittlement (LME) during spot welding. It can be prevented.
본 발명의 제1 구현례에서 계면 합금층 중 소지강판과 근접한 위치에 FeAl3 상이 형성된다는 것은 계면 합금층과 소지강판의 경계로부터 합금층 방향으로 1㎛ 이내의 위치에 존재하는 상 중 FeAl3 상의 비율이 면적 기준으로 70% 이상인 경우를 의미한다.Being in the position close to hold the steel sheet of the surface alloy layer FeAl 3 image is formed in the first implementation example of the invention on the in-phase FeAl 3 present in position within the alloy layer 1㎛ direction from the boundary of the surface alloy layer and the steel sheet possessing This means that the ratio is 70% or more based on the area.
이때, 상기 계면 합금층은 단층 구조를 가질 수 있으며, 경우에 따라서는 2층 이상의 구조를 가질 수도 있으나, 계면 합금층 중 소지강판과 근접한 위치에는 FeAl3 상이 형성된다. 계면 합금층이 2층 이상의 구조를 가질 경우 형성된 모든 층에서 Al 함량이 FeAl3 상의 Al 함량 보다 높을 수 있다.In this case, the interfacial alloy layer may have a single layer structure, and in some cases, may have a structure of two or more layers, but FeAl 3 phase is formed at a position close to the base steel sheet of the interfacial alloy layer. When the interfacial alloy layer has a structure of two or more layers, the Al content may be higher than the Al content of the FeAl 3 phase in all the formed layers.
본 발명에서 FeAl3 상이라고 함은 Fe와 Al의 원자비(중량 기준의 Fe 함량/Fe의 원자량 : 중량 기준의 Al 함량/Al의 원자량)가 1:2.8~1:3.3 사이의 비율을 가지는 상을 의미한다. 또한, 본 발명에서 FeAl3 상이라고 함은 Fe와 Al 사이의 비율을 정의하기 위한 것으로서, 도금욕이나 소지강판 등에서 유래된 추가적인 성분들이 상기 FeAl3 상에 포함되는 것을 배제하는 것은 아니라는 점에 유의할 필요가 있다. FeAl3 상 외에 추가적으로 포함될 수 있는 성분들의 비제한적인 예로서는, Si, Mn 등을 들 수 있다.In the present invention, the FeAl 3 phase is a phase in which the atomic ratio of Fe and Al (Fe content by weight / atomic amount of Fe: atomic weight Al content / Al by atomic weight) has a ratio between 1: 2.8 and 1: 3.3. Means. In addition, the FeAl 3 phase in the present invention is intended to define the ratio between Fe and Al, it should be noted that the additional components derived from the plating bath or the base steel sheet, etc. do not exclude that the inclusion of the FeAl 3 phase. There is. Non-limiting examples of components that may be additionally included in addition to the FeAl 3 phase include Si, Mn and the like.
본 발명의 제2 구현례에 따르면, 계면 합금층 중 Fe2Al5 상의 함량의 비율이 면적 기준으로 10% 이하로 제한되며, 바람직하게는 5% 이하로 제한될 수 있다.According to the second embodiment of the present invention, the ratio of the content of the Fe 2 Al 5 phase in the interfacial alloy layer is limited to 10% or less based on the area, preferably to 5% or less.
본 발명에서 Fe2Al5 상이라 함은 Fe와 Al의 원자비가 1:2.2~1:2.7 사이의 비율을 가지는 상을 의미한다.In the present invention, the Fe 2 Al 5 phase means a phase having an atomic ratio of Fe and Al of 1: 2.2 to 1: 2.7.
이때, 상기 계면 합금층은 단층 구조를 가질 수 있으며, 경우에 따라서는 2층 이상의 구조를 가질 수도 있으나, 계면 합금층 중 소지강판과 근접한 위치에는 FeAl3 상이 형성된다. 계면 합금층이 2층 이상의 구조를 가질 경우 형성된 모든 층에서 Al 함량이 FeAl3 상의 Al 함량 보다 높을 수 있다(즉, Fe와 Al의 원자비가 1:2.8 보다 많도록 Al이 포함되는 것을 의미한다).In this case, the interfacial alloy layer may have a single layer structure, and in some cases, may have a structure of two or more layers, but FeAl 3 phase is formed at a position close to the base steel sheet of the interfacial alloy layer. If the interfacial alloy layer has a structure of two or more layers, the Al content may be higher than the Al content of the FeAl 3 phase in all the layers formed (that is, Al is included so that the atomic ratio of Fe and Al is greater than 1: 2.8). .
본 발명의 제3 구현례에 따르면, 상기 계면합금층은 실질적으로 단층으로 형성될 수 있으며, 계면 합금층의 두께 방향 중심부의 성분을 분석하였을 때, Al 함량이 FeAl3 상의 함량에 해당할 수 있다. 본 발명의 한가지 구현례에 따르면 상기 두께 방향 중심부의 성분은, 두께 방향 중심부에서 임의의 지점을 5개소 선택하고 그 지점을 EDS로 성분 분석하고 이들의 성분의 평균값을 계산함으로써 구해질 수 있다.According to the third embodiment of the present invention, the interfacial alloy layer may be substantially formed as a single layer, when analyzing the components of the central portion in the thickness direction of the interfacial alloy layer, the Al content may correspond to the content of the FeAl 3 phase. . According to one embodiment of the present invention, the components in the thickness direction center part can be obtained by selecting five arbitrary points in the thickness direction center part, analyzing the points by EDS, and calculating the average value of these components.
상술한 본 발명의 각 구현례들은 상호 다른 구현례들을 배척하는 것이 아니다. 각 구현례들은 상호 그 범위가 중복될 수도 있으나, 본 발명의 유리한 효과를 얻기 위하여 모든 구현례의 조건이 동시에 충족되어야 하는 것은 아니라는 점에 유의할 필요가 있다.Each of the embodiments of the present invention described above does not exclude mutually different embodiments. Each of the embodiments may overlap each other in scope, but it should be noted that not all of the conditions of the embodiments should be satisfied at the same time in order to obtain the advantageous effect of the present invention.
일 예에 따르면, 계면 합금층이 단층 구조를 갖는다는 것은, 용융 알루미늄 합금 도금강판을 두께 방향으로 절단한 후, 주사전자현미경(FE-SEM, Field Emission Scanning Electron Microscope)으로 3000 배율로 그 단면 사진을 촬영하였을 때, 계면 합금층 내 층 분리가 관찰되지 않는 것을 의미할 수 있다.According to one example, the interfacial alloy layer has a single layer structure, after cutting the molten aluminum alloy plated steel sheet in the thickness direction, and using a scanning electron microscope (FE-SEM, Field Emission Scanning Electron Microscope) at a 3000 magnification, the cross-sectional photograph When photographing, it may mean that no layer separation in the interfacial alloy layer is observed.
일 예에 따르면, 상기 도금 피막은 중량%로, Al: 50~90%, Zn: 2~35%, Si: 3~15% 및 Fe: 0.1~5%를 포함할 수 있다. 본 발명의 도금 피막은 도금 상층과 계면 합금층을 염산으로 모두 용해시킨 후, 얻어진 용액을 ICP(Inductively Coupled Plasma) 법을 이용하여 분석할 수 있으나, 분석 방법이 반드시 이러한 방법으로 제한되지는 않는다.According to one example, the plating film may include, by weight, Al: 50 to 90%, Zn: 2 to 35%, Si: 3 to 15%, and Fe: 0.1 to 5%. In the plating film of the present invention, after dissolving both the upper plating layer and the interfacial alloy layer with hydrochloric acid, the obtained solution can be analyzed using ICP (Inductively Coupled Plasma) method, but the analysis method is not necessarily limited to this method.
Al은 철과의 고융점 합금상 형성을 위해 첨가된다. 만약, 그 함량이 지나치게 낮을 경우, 고융점의 합금상 형성이 미흡하여 용접 액상 금속 취화가 발생할 우려가 있다. 따라서, Al 함량은 50중량% 이상일 수 있으며, 55중량% 이상 또는 60중량% 이상일 수도 있다. 다만, 그 함량이 과다할 경우, 단면 내식성이 열화될 우려가 있다 따라서, Al 함량은 90중량% 이하, 80중량% 이하인 또는 75중량% 이하일 수 있다.Al is added to form a high melting point alloy phase with iron. If the content is too low, high melting point alloy phase formation is insufficient, there is a fear that the welding liquid metal embrittlement occurs. Therefore, Al content may be 50 weight% or more, 55 weight% or more, or 60 weight% or more. However, when the content is excessive, the cross-sectional corrosion resistance may deteriorate. Therefore, the Al content may be 90 wt% or less, 80 wt% or less, or 75 wt% or less.
Zn은 단면 희생 방식성을 위해 첨가된다. 만약, 그 함량이 지나치게 낮을 경우, 충분한 단면 내식성 확보가 어려울 수 있다. 따라서, Zn 함량은 2중량% 이상인 것이 바람직하고, 10중량% 일 수 있으며, 20중량% 이상일 수도 있다. 다만, 그 함량이 과다할 경우, 용접시 액화취화 현상이 발생할 우려가 있다. 따라서, Zn 함량은 35중량%, 30중량% 이하 또는 25중량% 이하일 수 있다.Zn is added for cross-sectional sacrificial corrosion protection. If the content is too low, it may be difficult to secure sufficient cross-sectional corrosion resistance. Accordingly, the Zn content is preferably 2% by weight or more, 10% by weight, or 20% by weight or more. However, when the content is excessive, there is a risk of liquefied embrittlement phenomenon during welding. Thus, the Zn content can be 35% by weight, 30% by weight or less, or 25% by weight or less.
Si은 도금욕의 융점을 낮추고, 도금 밀착성을 향상시키기 위하여 첨가된다. 만약, 그 함량이 지나치게 낮을 경우, Al-Fe 합금상이 과도하게 형성되어 도금 밀착성이 열화될 수 있다. 따라서, Si 함량은 3중량% 이상, 5중량% 이상 또는 6중량% 이상일 수 있다. 다만, 그 함량이 지나치게 과다할 경우, 도금욕 융점이 상승하고, Al-Fe 합금상 형성이 과도하게 억제될 우려가 있다. 따라서, Si 함량은 15중량% 이하, 12중량% 이하 또는 10중량% 이하일 수 있다.Si is added to lower the melting point of the plating bath and to improve plating adhesion. If the content is too low, the Al-Fe alloy phase may be excessively formed to degrade plating adhesion. Thus, the Si content may be at least 3% by weight, at least 5% by weight or at least 6% by weight. However, when the content is excessively excessive, there is a fear that the plating bath melting point is increased and the Al-Fe alloy phase formation is excessively suppressed. Thus, the Si content may be up to 15 wt%, up to 12 wt% or up to 10 wt%.
Fe는 Al과 반응하여 용융점이 높은 Fe-Al 금속간화합물을 형성하여 LME를 억제한다. 만약, 그 함량이 지나치게 낮을 경우, Al-Fe 합금상이 거의 형성 되지 않아 LME가 발생될 수 있다. 따라서, Fe 함량은 0.1중량% 이상, 1중량% 이상 또는 3중량% 이상일 수 있다. 다만, 그 함량이 지나치게 과다할 경우, Al-Fe의 합금상이 과도하게 형성되어 도금밀착성이 열화될 우려가 있다. 따라서, Si 함량은 5중량% 이하, 4.5중량% 이하 또는 4중량% 이하일 수 있다.Fe reacts with Al to form a high melting point Fe-Al intermetallic compound to suppress LME. If the content is too low, Al-Fe alloy phase is hardly formed and LME may be generated. Thus, the Fe content may be at least 0.1% by weight, at least 1% by weight or at least 3% by weight. However, if the content is excessively excessive, there is a fear that the alloy phase of Al-Fe is excessively formed and the plating adhesion is deteriorated. Thus, the Si content may be up to 5 wt%, up to 4.5 wt% or up to 4 wt%.
상기 조성 이외의 나머지는 불가피한 불순물이다. 통상의 도금강판 제조과정에서는 원료 또는 주위 환경으로부터 의도되지 않는 불순물들이 불가피하게 혼입될 수 있으므로, 이를 배제할 수는 없다. 이들 불순물들은 본 기술분야에서 통상의 지식을 가진 자라면 누구라도 알 수 있는 것이기 때문에 그 모든 내용을 본 명세서에서 특별히 언급하지는 않는다.The rest other than the above composition is an unavoidable impurity. In the ordinary manufacturing process of the plated steel sheet, impurities that are not intended from the raw material or the surrounding environment may inevitably be mixed, and thus cannot be excluded. Since these impurities are known to those skilled in the art, not all of them are specifically mentioned in the present specification.
한편, 상기 조성 이외에 유효한 성분의 첨가가 배제되는 것은 아니며, 예를 들어, 도금 피막은 Mg: 0.5~5중량%를 더 포함할 수 있다.On the other hand, addition of an effective component other than the above composition is not excluded, for example, the plating film may further comprise Mg: 0.5 to 5% by weight.
Mg은 표면 및 단면 내식성 개선을 위해 첨가된다. 이러한 효과를 충분히 얻기 위해서는, 0.5중량% 이상, 1중량% 이상 또는 2중량% 이상 첨가할 수 있다. 다만, 그 함량이 과다할 경우, 용접시 액상 금속 취화가 발생될 우려가 있다. 따라서, Mg 함량은 5중량% 이하, 4중량% 이하 또는 3중량% 이하일 수 있다.Mg is added to improve surface and cross section corrosion resistance. In order to fully acquire such an effect, 0.5 weight% or more, 1 weight% or more, or 2 weight% or more can be added. However, when the content is excessive, there is a fear that liquid metal embrittlement occurs during welding. Thus, the Mg content may be up to 5 wt%, up to 4 wt% or up to 3 wt%.
일 예에 따르면, 계면 합금층에 포함된 Fe 함량은 45중량% 이하인 것이 바람직하다. 상기 계면 합금층의 Fe 함량을 측정하는 방법의 일예로, EDS(Energy Dispersive Spectroscopy)를 이용하여 점 분석하여 측정할 수 있다. 상기 계면 합금층에 포함된 Fe 함량이 45 중량%를 초과하는 값을 갖는 것은 계면 합금층 내 경질의 Fe-Al계 합금상이 존재한다는 것을 의미하며, 전술한 바와 같이, 이러한 경질의 Fe-Al계 합금상은 점 용접성 및 가공시 도금 밀착성을 열화시키는 문제점이 있는 바, 이러한 영역이 존재하지 않도록 관리함이 바람직하다.According to one example, the Fe content contained in the interfacial alloy layer is preferably 45% by weight or less. As an example of a method for measuring the Fe content of the interfacial alloy layer, it may be measured by point analysis using Energy Dispersive Spectroscopy (EDS). The Fe content included in the interfacial alloy layer having a value of more than 45% by weight means that there is a hard Fe-Al-based alloy phase in the interfacial alloy layer, as described above, such a hard Fe-Al-based Since the alloy phase has a problem of deteriorating the spot weldability and the plating adhesion during processing, it is preferable to manage such an area not to exist.
일 예에 따르면, 계면 합금층에 함유된 Si의 평균 함량은 도금 상층에 함유된 Si의 평균 함량의 2배 이상일 수 있고, 바람직하게는 3배 이상일 수 있으며, 보다 바람직하게는 7배 이상일 수 있고, 가장 바람직하게는 10배 이상일 수 있다. 만약, 계면 합금층에 함유된 Si의 평균 함량이 도금 상층에 함유된 Si의 평균 함량 대비 2배 미만일 경우 합금상이 과도하게 형성될 우려가 있다. According to one example, the average content of Si contained in the interfacial alloy layer may be at least two times, preferably at least three times, more preferably at least seven times, the average content of Si contained in the upper plating layer. Most preferably 10 times or more. If the average content of Si contained in the interfacial alloy layer is less than twice the average content of Si contained in the upper plating layer, there is a fear that the alloy phase is excessively formed.
한편, 도금 상층 및 계면 합금층에 함유된 Si의 평균 함량을 측정하는 구체적인 방법에 대해서는 특별히 한정하지 않으나, 예를 들면, 도금 상층에 함유된 Si의 평균 함량은 도금 상층을 크롬산으로 용해하여 습식분석(ICP)에 의해 측정할 수 있으며, 계면 합금층에 함유된 Si의 평균 함량은 염산으로 용해하여 습식분석(ICP)에 의해 측정할 수 있다.The specific method of measuring the average content of Si contained in the upper plating layer and the interfacial alloy layer is not particularly limited. For example, the average content of Si contained in the upper plating layer is wetted by dissolving the upper plating layer with chromic acid. It can be measured by (ICP), and the average content of Si contained in the interfacial alloy layer can be measured by wet analysis (ICP) by dissolving with hydrochloric acid.
일예로, 상기 도금 상층의 Si함량은 0.7~1 중량%이고, 계면 합금층에서의 Si 함량은 7~12 중량%인 것이 바람직하다.For example, the Si content of the upper plating layer is 0.7 to 1% by weight, and the Si content in the interfacial alloy layer is preferably 7 to 12% by weight.
일 예에 따르면, 계면 합금층은 7㎛ 이하 (0㎛ 제외)의 평균 두께를 가질 수 있으며, 바람직하게는 5㎛ 이하 (0㎛ 제외)의 평균 두께를 가질 수 있다. 만약, 계면 합금층의 평균 두께가 7㎛를 초과할 경우 가공시 도금밀착성이 열화되는 문제점이 있을 수 있다. 한편, 본 발명에서는 계면 합금층 평균 두께의 하한에 대해서는 특별히 한정하지 않으나, 만약 그 두께가 지나치게 얇을 경우, 용접시 LME 저항을 억제하지 못할 우려가 있으므로, 이를 고려하여 그 하한을 1㎛로 한정할 수는 있다.According to one example, the interfacial alloy layer may have an average thickness of 7 μm or less (excluding 0 μm), and preferably may have an average thickness of 5 μm or less (excluding 0 μm). If the average thickness of the interfacial alloy layer exceeds 7㎛ there may be a problem that the plating adhesion deteriorated during processing. In the present invention, the lower limit of the average thickness of the interfacial alloy layer is not particularly limited. However, if the thickness is too thin, there is a possibility that the LME resistance may not be suppressed during welding. There is a number.
다음으로, 본 발명의 용융 알루미늄 합금 도금강판을 제조하는 방법 중 일예에 대해서 상세히 설명한다. 본 발명의 용융 알루미늄 합금 도금강판은 다양한 방법으로 제조될 수 있으며, 그 제조방법은 특별히 제한되지 않는다. 다만, 바람직한 일예로써, 다음과 같은 방법에 의해 제조될 수 있다.Next, one example of the method for producing a molten aluminum alloy plated steel sheet of the present invention will be described in detail. The molten aluminum alloy plated steel sheet of the present invention can be produced by various methods, the production method is not particularly limited. However, as a preferred example, it may be prepared by the following method.
소지강판을 준비한다. 상기 소지강판은 그 종류를 특별히 한정하거나 제한되지 않으며, 본 발명이 속하는 기술분야에서 적용될 수 있는 것으로 인식되는 것이면 충분하다. Prepare your steel sheet. The steel sheet is not particularly limited or limited in kind, and it is sufficient that it is recognized that the present invention can be applied in the technical field to which the present invention belongs.
상기 소지강판을 용융 알루미늄 도금욕(이하, 도금욕)에 침지하여 도금을 행한다. 상기 도금욕의 조성은 일예로 중량%로, Al: 50~90%, Zn: 2~35%, Si: 3~15% 및 Fe: 0.1~5%일 수 있다. The base steel sheet is immersed in a molten aluminum plating bath (hereinafter referred to as a plating bath) to perform plating. The composition of the plating bath may be, for example, in weight%, Al: 50-90%, Zn: 2-35%, Si: 3-15%, and Fe: 0.1-5%.
한편, 상기 도금욕의 온도는 도금욕 온도는 소지강판의 물성에 영향을 줄 뿐만 아니라, 계면 합금층 구조에도 영향을 미치게 되며, 보다 구체적으로, 도금욕 온도가, 도금욕 융점 대비 30℃를 초과할 경우, 잔류오스테나이트나 마텐사이트와 같은 조직의 분해가 일어나 소지강판의 재질이 열화될 우려가 있을 뿐만 아니라, 도금욕에 인입된 소지강판의 표면에서 용융 알루미늄과의 합금화 반응으로 형성되는 Fe2Al5의 형성이 촉진되어 복층의 계면 합금층이 얻어질 우려가 있다. 따라서, 도금욕 온도는 도금욕 융점 + 30℃ 이하로 할 수 있으며, 도금욕 융점 + 25℃ 이하 또는 도금욕 융점 + 20℃ 이하로 제어할 수도 있다.On the other hand, the temperature of the plating bath not only affects the physical properties of the steel sheet, but also affects the interfacial alloy layer structure, and more specifically, the plating bath temperature is more than 30 ℃ compared to the melting point of the plating bath. In this case, the structure of the steel sheet may be degraded due to decomposition of a structure such as residual austenite or martensite, and Fe 2 formed by alloying with molten aluminum on the surface of the steel sheet introduced into the plating bath. Formation of Al 5 is accelerated, and there is a fear that a multilayer interfacial alloy layer is obtained. Therefore, the plating bath temperature can be set to the plating bath melting point + 30 ° C or less, and may be controlled to the plating bath melting point + 25 ° C or less or the plating bath melting point + 20 ° C or less.
상기 도금을 행한 후에 도금층을 냉각한다. 도금 후 냉각 또한 계면 합금층의 구조에 큰 영향을 미친다. 상기 냉각은 도금욕에서 배출된 강판 표면 온도가 5초 이내, 4초 이내, 또는 3초 이내에 도금욕 융점 온도 이하가 되도록 하는 것이 바람직하다. 도금층이 빠른 시간 내에 응고가 되지 않은 경우, 복층의 계면 합금층이 얻어지거나 Fe-Al 합금상이 지속적으로 성장되어 도금 밀착성이 열화될 수 있다. After the plating, the plating layer is cooled. Cooling after plating also greatly affects the structure of the interfacial alloy layer. The cooling is preferably such that the steel sheet surface temperature discharged from the plating bath is below the plating bath melting point temperature within 5 seconds, within 4 seconds, or within 3 seconds. If the plating layer is not solidified in a short time, a multi-layered interfacial alloy layer may be obtained or the Fe—Al alloy phase may be continuously grown to degrade plating adhesion.
한편, 도금욕 융점 온도 이하의 온도에서 냉각 속도에 대해서는 특별히 한정하지 않으나, 예를 들어, 도금 상층이 온전히 냉각되는 시점까지 5~20℃/sec의 속도로 냉각할 수 있다. 만약, 5℃/sec 미만일 경우 도금층이 탑롤 등에 흡착될 우려가 있고, 20℃/sec를 초과할 경우 표면에 파형형태의 물결무늬가 발생할 우려가 있다.On the other hand, the cooling rate at a temperature below the plating bath melting point temperature is not particularly limited. For example, the cooling rate can be cooled at a rate of 5 to 20 ° C./sec until the plating upper layer is completely cooled. If less than 5 ° C / sec, there is a fear that the plated layer is adsorbed on the top roll, etc., if it exceeds 20 ° C / sec there is a fear that the wave pattern of the wavy form on the surface.
이하, 실시예를 통하여 본 발명을 보다 구체적으로 설명한다. 다만, 하기하는 실시예는 본 발명을 예시하여 구체화하기 위한 것일 뿐, 본 발명의 권리범위를 제한하기 위한 것이 아니라는 점에 유의할 필요가 있다. 본 발명의 권리범위는 특허청구범위에 기재된 사항과 이로부터 합리적으로 유추되는 사항에 의하여 결정되는 것이기 때문이다.Hereinafter, the present invention will be described in more detail with reference to Examples. However, it should be noted that the following examples are only intended to illustrate the present invention and are not intended to limit the scope of the present invention. This is because the scope of the present invention is determined by the matters described in the claims and the matters reasonably inferred therefrom.
(실시예)(Example)
중량%로, C: 0.15%, Si: 1.5%, Mn: 2.5%, Cr: 0.4%, 나머지는 Fe 및 불가피한 불순물을 포함하는 두께 1.4㎜의 자동차용 기가급 강재(강도가 1GPa 이상인 강재를 의미함. 본 실시예에서 사용된 강재의 강도는 1.18GPa 이었음)를 소지강판으로 준비한 후, 상기 소지강판을 침지하고 초음파 세척하여 표면에 존재하는 압연유 등의 이물질을 제거하였다. 이후, 일반 용융도금 현장에서 강판의 기계적 특성 확보를 위하여 실시하는 750℃ 환원 분위기 열처리를 실시한 후, 하기 표 1과 같은 조성 및 온도를 가지는 도금욕에 침지하여 용융 알루미늄 합금 도금강판을 제조하였다.By weight, C: 0.15%, Si: 1.5%, Mn: 2.5%, Cr: 0.4%, the remainder is a car-grade automotive grade steel with a thickness of 1.4 mm containing Fe and unavoidable impurities (steel having a strength of 1 GPa or more) The strength of the steel used in the present example was 1.18 GPa), and then the steel plate was prepared, and the foreign material such as rolling oil on the surface was removed by immersing the body steel plate and ultrasonic cleaning. Then, after performing a 750 ℃ reducing atmosphere heat treatment performed to ensure the mechanical properties of the steel sheet in the general hot dip plating site, it was immersed in a plating bath having a composition and temperature as shown in Table 1 to produce a molten aluminum alloy plated steel sheet.
이후, 제조된 각각의 용융 알루미늄 합금 도금강판을 도금욕 융점 이하의 온도로 냉각하고, 가스 와이핑하여 도금 부착량을 편면당 70g/㎡으로 조절하였으며, 10℃/sec의 속도로 도금 상층이 완전히 응고되는 시점까지 냉각을 행하였다. 한편, 각각의 예에서, 도금욕에 배출된 용융 알루미늄 합금 도금강판의 온도가 도금욕 융점 이하가 되는데 걸린 시간(tm)을 하기 표 1에 함께 나타내었다.Thereafter, each of the molten aluminum alloy plated steel sheets produced was cooled to a temperature below the melting point of the plating bath, and the gas was wiped to adjust the coating amount to 70 g / m 2 per side, and the upper plating layer was completely solidified at a rate of 10 ° C./sec. Cooling was performed until it became. On the other hand, in each example, the time (t m ) taken for the temperature of the molten aluminum alloy plated steel sheet discharged to the plating bath to be below the plating bath melting point is shown together in Table 1 below.
이후, 제조된 각 용융 알루미늄 합금 도금강판을 판두께 방향으로 절단한 후, 주사전자현미경(FE-SEM)으로 3,000배율로 그 단면 사진을 촬영하여 계면 합금층 내 층 분리가 관찰되는지 여부를 관찰하고, 그 두께를 측정하였으며, 계면 합금층에 포함된 Fe 함량을 EDS(Energy Dispersive Spectroscopy)를 이용하여 점 분석하여 Fe 함량의 최대값을 측정하고, 전술한 습식분석(ICP)에 의해 도금 상층 및 계면 합금층 각각에 함유된 Si의 평균 함량을 측정하였다. 그 결과를 하기 표 2에 나타내었다.Subsequently, each of the manufactured molten aluminum alloy plated steel sheets was cut in the plate thickness direction, and then a cross-sectional photograph was taken at a magnification of 3,000 by scanning electron microscope (FE-SEM) to observe whether or not layer separation in the interfacial alloy layer was observed. The thickness was measured, and the Fe content contained in the interfacial alloy layer was analyzed by point analysis using EDS (Energy Dispersive Spectroscopy) to determine the maximum value of the Fe content, and the upper plating layer and the interface by the above-described wet analysis (ICP). The average content of Si contained in each of the alloy layers was measured. The results are shown in Table 2 below.
이후, 각각의 용융 알루미늄 합금 도금강판의 재질을 측정하고, 내식성과 용접성 및 도금 밀착성을 평가하였으며, 그 결과를 하기 표 3에 나타내었다.Then, the material of each molten aluminum alloy plated steel sheet was measured, and corrosion resistance, weldability, and plating adhesion were evaluated, and the results are shown in Table 3 below.
내식성 평가는 각 용융 알루미늄 합금 도금강판을 염수 분무 시험기에 장입하고, 5% 염수(온도 35℃, pH 6.8)를 시간당 2ml/80㎠ 분무하고, 장입 1200 시간 경과 후, 부식 생성물을 제거하고 소지강판에 형성된 최대 구멍 깊이를 측정하였다. 측정 결과 300㎛ 이하인 경우는 "우수", 300~600㎛인 경우는 "보통", 600㎛ 초과는 "불량"으로 평가하였다. To evaluate corrosion resistance, each molten aluminum alloy plated steel sheet was charged to a salt spray tester, 5% brine (temperature 35 ° C., pH 6.8) was sprayed 2 ml / 80 cm 2 per hour, and after 1200 hours of charging, the corrosion product was removed and the steel sheet The maximum hole depth formed in the was measured. In the case of 300 micrometers or less, as a result of a measurement, it evaluated as "excellent", and when it is 300-600 micrometers, it is "normal" and more than 600 micrometers evaluated as "defect".
용접성은 선단경 6mm인 Cu-Cr 전극을 사용하여 용접 전류 0.5kA를 흘려주며, 가압력 4.0kN의 조건 하 용접을 실시하였다. 용접 후, 주사전자현미경(FE-SEM)에 의해 그 단면에 형성된 LME 크랙의 길이를 측정하였다. 측정 결과, LME 크랙 길이가 150㎛이하인 경우 "우수", LME 크랙 길이가 150㎛ 초과 500㎛ 이하인 경우 "보통", LME 크랙 길이가 500㎛를 초과하는 경우 "불량"으로 평가하였다.The weldability was made to flow by welding current of 0.5 kA using the Cu-Cr electrode with a tip diameter of 6 mm, and welding was performed under the pressure of 4.0 kN. After welding, the length of the LME crack formed in the cross section was measured by the scanning electron microscope (FE-SEM). As a result of the measurement, it was evaluated as "good" when the LME crack length was 150 µm or less, "normal" when the LME crack length exceeded 150 µm and 500 µm or less, and "bad" when the LME crack length exceeded 500 µm.
한편 도금 밀착성 평가는 자동차 구조용 실러 D 타입을 175도에서 25분 유지하여 경화시킨 후 90도 굽힘 실험을 하였다. 시편 크기는 30*75㎜로 하였으며, 실러 도포 면적은 10*40mm, 두께는 10mm 이하로 하였다. 전단 접착 강도가 24.5Mpa 이상일 경우에는 '우수', 그 미만일 경우에는 '불량'으로 하였다.On the other hand, the evaluation of plating adhesion was conducted by holding the automobile structural sealer D type at 175 degrees for 25 minutes and curing, and then performing a 90 degree bending test. The specimen size was 30 * 75 mm, the sealer coating area was 10 * 40 mm, and the thickness was 10 mm or less. If the shear bond strength is 24.5 Mpa or more, 'excellent', and if less than that, it was set as 'poor'.
(℃)Plating bath melting point
(℃)
(℃)Plating bath temperature
(℃)
(sec)t m
(sec)
(㎛)thickness
(Μm)
(중량%)Fe content
(weight%)
(중량%)Si content
(weight%)
(중량%)Si content
(weight%)
도 1 및 2는 각각 비교예 1과 발명예 2의 단면을 주사전자현미경(FE-SEM, Field Emission Scanning Electron Microscope)으로 관찰한 사진이다. 도 1 및 2에 나타난 바와 같이, 비교예 1에서는 복층 구조를 가지고 있으나, 발명예 2에서는 단층구조를 이루는 것을 알 수 있다. 1 and 2 are photographs of the cross-sections of Comparative Example 1 and Inventive Example 2 observed with a scanning electron microscope (FE-SEM, Field Emission Scanning Electron Microscope), respectively. As shown in Figure 1 and 2, in Comparative Example 1 has a multilayer structure, it can be seen that in Inventive Example 2 forms a single layer structure.
한편, 도 3은 발명예 4의 용접 후, 주사전자현미경(FE-SEM)에 의해 그 단면을 관찰한 사진이고, 도 4는 비교예 7의 용접 후, 주사전자현미경 (FE-SEM)에 의해 그 단면을 관찰한 사진이다. 도 3 및 4를 참조하면, 본 발명에서 제안하는 조건을 모두 만족하는 발명예에서는 용접성이 효과적으로 개선되나, 비교예에서는 LME가 발생하는 것을 알 수 있다. On the other hand, Figure 3 is a photograph observing the cross section by a scanning electron microscope (FE-SEM) after welding of Inventive Example 4, Figure 4 is a scanning electron microscope (FE-SEM) after welding of Comparative Example 7 It is a photograph observing the cross section. 3 and 4, in the invention example that satisfies all the conditions proposed by the present invention, the weldability is effectively improved, it can be seen that the LME occurs in the comparative example.
상기 표 3의 결과에서 알 수 있듯이, 본 발명의 조건을 만족하는 발명예들은 모두 우수한 내식성, 용접성 및 도금 밀착성을 확보할 수 있었으나, 본 발명의 범위를 벗어난 비교예에서는 그렇지 않음을 알 수 있다.As can be seen from the results of Table 3, all the invention examples satisfying the conditions of the present invention was able to secure excellent corrosion resistance, weldability and plating adhesion, it can be seen that in the comparative example outside the scope of the present invention it is not.
Claims (16)
상기 도금 피막은 강판과의 계면에 존재하는 계면 합금층과 상기 계면 합금층 상에 존재하는 도금 상층을 포함하고,
계면 합금층과 소지강판의 경계로부터 계면 합금층 방향으로 1㎛ 이내의 위치에 존재하는 상 중 Fe와 Al의 원자비가 1:2.8~1:3.3 사이의 비율을 가지는 상의 비율이 면적 기준으로 70% 이상인 내식성 및 용접성이 우수한 용융 알루미늄 합금 도금강판.
Made of a molten aluminum alloy plating film formed on the surface of the steel sheet,
The plating film includes an interfacial alloy layer present at an interface with a steel plate and an upper plating layer present on the interfacial alloy layer,
Among the phases present at a position within 1 μm from the boundary between the interface alloy layer and the base steel sheet in the direction of the interface alloy layer, the proportion of phases having an atomic ratio between Fe and Al of 1: 2.8 to 1: 3.3 is 70% by area. Hot-dip aluminum alloy plated steel sheet with excellent corrosion resistance and weldability.
상기 도금 피막은 강판과의 계면에 존재하는 계면 합금층과 상기 계면 합금층 상에 존재하는 도금 상층을 포함하고,
계면 합금층 중 Fe와 Al의 원자비가 1:2.2~1:2.7 사이의 비율을 가지는 상의 비율이 면적 기준으로 10% 이하(0%는 제외) 인 내식성 및 용접성이 우수한 용융 알루미늄 합금 도금강판.
Made of a molten aluminum alloy plating film formed on the surface of the steel sheet,
The plating film includes an interfacial alloy layer present at an interface with a steel plate and an upper plating layer present on the interfacial alloy layer,
A hot-dip aluminum alloy plated steel sheet having excellent corrosion resistance and weldability in which the ratio of a phase having an atomic ratio of Fe and Al in the interfacial alloy layer between 1: 2.2 and 1: 2.7 is 10% or less (excluding 0%) based on the area.
The molten aluminum alloy plated steel sheet according to claim 1 or 2, wherein the interfacial alloy layer is excellent in corrosion resistance and weldability in a single layer structure.
상기 용융 알루미늄 합금 도금강판을 두께 방향으로 절단한 후, 주사전자현미경(FE-SEM, Field Emission Scanning Electron Microscope)으로 3,000 배율로 그 단면 사진을 촬영하였을 때, 상기 계면 합금층 내 층 분리가 관찰되지 않는 내식성 및 용접성이 우수한 용융 알루미늄 합금 도금강판.
The method of claim 3, wherein
After the molten aluminum alloy plated steel sheet was cut in the thickness direction, when the cross-sectional photograph was taken at a magnification of 3,000 by a scanning electron microscope (FE-SEM), no layer separation was observed in the interfacial alloy layer. Hot-dip aluminum alloy plated with excellent corrosion resistance and weldability.
The molten aluminum alloy according to claim 1 or 2, wherein the interfacial alloy layer is formed of two or more layers, and Al is included in the formed Al layer so that the atomic ratio of Fe and Al is greater than 1: 2.8 in all the formed layers. Plated steel sheet.
상기 도금 피막은 강판과의 계면에 존재하는 계면 합금층과 상기 계면 합금층 상에 존재하는 도금 상층을 포함하고,
상기 계면합금층은 단층 구조이며, 계면 합금층의 두께 방향 중심부의 성분을 분석하였을 때, Fe와 Al의 원자비가 1:2.8~1:3.3 사이의 비율을 가지는 내식성 및 용접성이 우수한 용융 알루미늄 합금 도금강판.
Made of a molten aluminum alloy plating film formed on the surface of the steel sheet,
The plating film includes an interfacial alloy layer present at an interface with a steel plate and an upper plating layer present on the interfacial alloy layer,
The interfacial alloy layer has a single layer structure, and when the components in the thickness direction of the interfacial alloy layer are analyzed, the molten aluminum alloy plating having excellent corrosion resistance and weldability having an atomic ratio between Fe and Al of 1: 2.8 to 1: 3.3 Grater.
상기 용융 알루미늄 합금 도금강판을 두께 방향으로 절단한 후, 주사전자현미경(FE-SEM, Field Emission Scanning Electron Microscope)으로 3,000 배율로 그 단면 사진을 촬영하였을 때, 상기 계면 합금층 내 층 분리가 관찰되지 않는 내식성 및 용접성이 우수한 용융 알루미늄 합금 도금강판.
The method of claim 6,
After the molten aluminum alloy plated steel sheet was cut in the thickness direction, when the cross-sectional photograph was taken at a magnification of 3,000 by a scanning electron microscope (FE-SEM), no layer separation was observed in the interfacial alloy layer. Hot-dip aluminum alloy plated with excellent corrosion resistance and weldability.
상기 도금 피막은 중량%로, Al: 50~90%, Zn: 2~35%, Si: 3~15% 및 Fe: 0.1~5%를 포함하는 내식성 및 용접성이 우수한 용융 알루미늄 합금 도금강판.
The method according to any one of claims 1, 2 and 6,
The plating film is a weight percent, Al: 50 to 90%, Zn: 2 to 35%, Si: 3 to 15% and Fe: 0.1 to 5% comprising a molten aluminum alloy plated steel sheet excellent in corrosion resistance and weldability.
상기 도금 피막은 Mg: 0.5~5%를 더 포함하는 내식성 및 용접성이 우수한 용융 알루미늄 합금 도금강판.
The method of claim 8,
The plating film is a molten aluminum alloy plated steel sheet excellent in corrosion resistance and weldability further comprises Mg: 0.5 ~ 5%.
상기 계면 합금층에 포함된 Fe 함량은 45 중량% 이하(0% 제외)인 내식성 및 용접성이 우수한 용융 알루미늄 합금 도금강판.
The method according to any one of claims 1, 2 and 6,
Fe content contained in the interfacial alloy layer is 45 wt% or less (excluding 0%) of the hot-dip aluminum alloy plated steel sheet excellent in corrosion resistance and weldability.
상기 계면 합금층에 포함된 Si 함량은 도금 상층에 포함된 Si 함량의 2배 이상, 13배 이하인 내식성 및 용접성이 우수한 용융 알루미늄 합금 도금강판.
The method according to any one of claims 1, 2 and 6,
Si content contained in the interfacial alloy layer is a molten aluminum alloy plated steel sheet excellent in corrosion resistance and weldability of 2 times or more, 13 times or less of the Si content contained in the upper plating layer.
상기 계면 합금층의 평균 두께는 7㎛ 이하(0은 제외)인 내식성 및 용접성이 우수한 용융 알루미늄 합금 도금강판.
The method according to any one of claims 1, 2 and 6,
Hot-dip aluminum alloy plated steel sheet excellent in corrosion resistance and weldability of the average thickness of the interfacial alloy layer is 7㎛ or less (excluding 0).
상기 준비된 소지강판을 중량%로, Al: 50~90%, Zn: 2~35%, Si: 3~15% 및 Fe: 0.1~5%를 포함하는 용융 알루미늄 합금 도금욕에 침지하여 도금하는 단계; 및
상기 도금 후 냉각하는 단계를 포함하고,
상기 도금욕의 온도는 도금욕 융점 + 30℃ 이하이고, 도금욕에서 배출된 소지강판의 표면 온도가 5초 이내에 도금욕 융점 온도 이하가 되도록 냉각하는 내식성 및 용접성이 우수한 용융 알루미늄 합금 도금강판의 제조방법.
Preparing a steel sheet;
Plating the prepared base steel sheet by weight in immersion in a molten aluminum alloy plating bath containing Al: 50 to 90%, Zn: 2 to 35%, Si: 3 to 15%, and Fe: 0.1 to 5% ; And
Cooling after the plating;
The temperature of the plating bath is the melting point of the plating bath + 30 ℃ or less, the production of molten aluminum alloy plated steel sheet excellent in corrosion resistance and weldability to cool so that the surface temperature of the base steel sheet discharged from the plating bath is below the plating bath melting point temperature within 5 seconds Way.
도금욕 융점 온도 이하에서의 냉각속도가 5~20℃/sec인 내식성 및 용접성이 우수한 용융 알루미늄 합금 도금강판의 제조방법.
The method of claim 13,
A method for producing a molten aluminum alloy plated steel sheet having excellent corrosion resistance and weldability at a cooling rate of 5 to 20 ° C./sec below the plating bath melting point temperature.
상기 도금욕은 Mg: 0.5~5%를 더 포함하는 내식성 및 용접성이 우수한 용융 알루미늄 합금 도금강판의 제조방법.
The method of claim 13,
The plating bath is Mg: 0.5 to 5% further comprising a method for producing a molten aluminum alloy plated steel sheet excellent in corrosion resistance and weldability.
Priority Applications (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| KR1020170177677A KR102043519B1 (en) | 2017-12-22 | 2017-12-22 | Hot dip aluminium alloy plated steel sheet having excellent corrosion resistance and weldability, method for manufacturing the same |
| EP18892672.9A EP3730664A4 (en) | 2017-12-22 | 2018-12-17 | Molten aluminum alloy-plated steel sheet having excellent corrosion resistance and weldability, and method for producing same |
| CN201880083264.4A CN111511955B (en) | 2017-12-22 | 2018-12-17 | Hot-dip aluminum alloy-coated steel sheet having excellent corrosion resistance and weldability, and method for producing same |
| PCT/KR2018/015998 WO2019124901A1 (en) | 2017-12-22 | 2018-12-17 | Molten aluminum alloy-plated steel sheet having excellent corrosion resistance and weldability, and method for producing same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| KR1020170177677A KR102043519B1 (en) | 2017-12-22 | 2017-12-22 | Hot dip aluminium alloy plated steel sheet having excellent corrosion resistance and weldability, method for manufacturing the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| KR20190076129A KR20190076129A (en) | 2019-07-02 |
| KR102043519B1 true KR102043519B1 (en) | 2019-11-12 |
Family
ID=66994098
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| KR1020170177677A KR102043519B1 (en) | 2017-12-22 | 2017-12-22 | Hot dip aluminium alloy plated steel sheet having excellent corrosion resistance and weldability, method for manufacturing the same |
Country Status (4)
| Country | Link |
|---|---|
| EP (1) | EP3730664A4 (en) |
| KR (1) | KR102043519B1 (en) |
| CN (1) | CN111511955B (en) |
| WO (1) | WO2019124901A1 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR102196682B1 (en) * | 2020-05-25 | 2020-12-30 | 주식회사 네오스라이트 | Molten aluminum plating heat dissipation plate PCB substrate for LED luminaire and manufacturing method thereof |
Family Cites Families (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1998026103A1 (en) * | 1996-12-13 | 1998-06-18 | Nisshin Steel Co., Ltd. | HOT-DIP Zn-Al-Mg COATED STEEL SHEET EXCELLENT IN CORROSION RESISTANCE AND SURFACE APPEARANCE AND PROCESS FOR THE PRODUCTION THEREOF |
| JP4136286B2 (en) * | 1999-08-09 | 2008-08-20 | 新日本製鐵株式会社 | Zn-Al-Mg-Si alloy plated steel with excellent corrosion resistance and method for producing the same |
| KR100456774B1 (en) * | 2002-01-05 | 2004-11-10 | 동부제강주식회사 | A manufacturing method of the Hot-Dip Aluminized Steel Sheet which has a excellent surface appearance |
| JP4584179B2 (en) * | 2006-04-13 | 2010-11-17 | Ｊｆｅ鋼板株式会社 | Method for producing hot-dip Zn-Al alloy-plated steel sheet with excellent corrosion resistance and workability |
| JP5476676B2 (en) * | 2008-04-22 | 2014-04-23 | 新日鐵住金株式会社 | Hot-pressed member and manufacturing method thereof |
| KR101008042B1 (en) * | 2009-01-09 | 2011-01-13 | 주식회사 포스코 | Aluminum Coated Steel Sheet with Excellent Corrosion Resistance and Hot Press Formed Article Using The Same and Manufacturing Method Thereof |
| US8911879B2 (en) | 2009-01-16 | 2014-12-16 | Nippon Steel & Sumitomo Metal Corporation | Hot-dip Zn—Al—Mg—Si—Cr alloy-coated steel material with excellent corrosion resistance |
| JP5430022B2 (en) * | 2011-12-12 | 2014-02-26 | Ｊｆｅスチール株式会社 | Al-based plated steel material and manufacturing method thereof |
| KR20140066020A (en) * | 2012-11-22 | 2014-05-30 | 현대제철 주식회사 | Hot-dip aluminium-magnesium-silicon based alloy coated steel sheet with excellent sacrificial protection and method of maunfacturing the same |
| CN106164323B (en) * | 2014-03-28 | 2019-01-11 | 新日铁住金株式会社 | Coated steel sheet containing quasicrystal |
| KR101569509B1 (en) * | 2014-12-24 | 2015-11-17 | 주식회사 포스코 | Hot press formed parts having less galling in the coating during press forming, and method for the same |
| RU2710813C1 (en) * | 2016-05-10 | 2020-01-14 | Ниппон Стил Корпорейшн | Hot-stamped steel |
-
2017
- 2017-12-22 KR KR1020170177677A patent/KR102043519B1/en active IP Right Grant
-
2018
- 2018-12-17 CN CN201880083264.4A patent/CN111511955B/en active Active
- 2018-12-17 WO PCT/KR2018/015998 patent/WO2019124901A1/en unknown
- 2018-12-17 EP EP18892672.9A patent/EP3730664A4/en active Pending
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR102196682B1 (en) * | 2020-05-25 | 2020-12-30 | 주식회사 네오스라이트 | Molten aluminum plating heat dissipation plate PCB substrate for LED luminaire and manufacturing method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| KR20190076129A (en) | 2019-07-02 |
| EP3730664A4 (en) | 2020-12-02 |
| CN111511955B (en) | 2023-04-14 |
| CN111511955A (en) | 2020-08-07 |
| EP3730664A1 (en) | 2020-10-28 |
| WO2019124901A1 (en) | 2019-06-27 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| EP2312005B1 (en) | Aluminum plated steel sheet for rapid heating hot-stamping, production method of the same and rapid heating hot-stamping method by using this steel sheet | |
| KR101353701B1 (en) | Galvanized steel sheet having excellent ultra low temperature adhesion property and method for manufacturing the same | |
| KR101721352B1 (en) | High strength steel plate with excellent delayed destruction resistance characteristics and low temperature toughness, and high strength member manufactured using same | |
| CA2778763C (en) | Hot-pressed member and method for producing the same | |
| JP4464720B2 (en) | High-strength hot-dip galvanized steel sheet and manufacturing method thereof | |
| CN110100038B (en) | Hot-dip aluminum-plated steel material having excellent corrosion resistance and workability, and method for producing same | |
| KR102284770B1 (en) | Steel sheet hot-dip-coated with zn-al-mg-based system having excellent workability and method for manufacturing same | |
| KR20200035740A (en) | Anti corrosive coated steel having good resistance against liquid metal embrittlement and coating adhesion | |
| KR102085223B1 (en) | Plated steel sheet | |
| KR102065287B1 (en) | Austenitic hot-dip aluminum coated steel sheet with excellent plating property and weldability, and a manufacturing method thereof | |
| KR102043522B1 (en) | Aluminum alloy coated steel sheet having improved resistance for liquid metal embrittlement and coating adhesion | |
| KR20110123768A (en) | Zinc based alloy coated steel having superior resistance to liquid metal embrittlement and cracking | |
| KR101585721B1 (en) | Galvanized steel having good weldabity and method for manufacturing the same | |
| KR102043519B1 (en) | Hot dip aluminium alloy plated steel sheet having excellent corrosion resistance and weldability, method for manufacturing the same | |
| KR102557220B1 (en) | plated steel | |
| KR20200095537A (en) | Hot-dip galvanized steel wire and its manufacturing method | |
| KR101284420B1 (en) | HOT DIP PLATED STEEL SHEET CONTAINING Al PLATING LAYER AND METHOD FOR MANUFACTURING THE SAME | |
| KR102311502B1 (en) | Aluminium alloy plate steel sheet having excellent formability and corrosion resistance and method for manufacturing the same | |
| US11898252B2 (en) | Aluminum-based alloy-plated steel sheet having excellent workability and corrosion resistance, and manufacturing method therefor | |
| CN116669896A (en) | Welded structural member having excellent crack resistance and method for manufacturing same | |
| JP2021501260A (en) | Manufacturing method of coated steel plate, two spot-welded metal plates and their use | |
| JP2021500474A (en) | Manufacturing method of coated steel sheet | |
| KR102175731B1 (en) | Alloyed aluminium coated steel sheet having excellent weldability and phosphating properties and method of manufacturing the same | |
| Keehan et al. | Understanding mechanical properties of novel high strength steel weld metals through high-resolution microstructural investigations | |
| JP2018145500A (en) | HIGH STRENGTH MOLTEN Zn-Al-Mg-BASED PLATED STEEL SHEET FOR AUTOMOBILE COMPONENT EXCELLENT IN FLEXURE PROCESSABILITY AND AUTOMOBILE COMPONENT USING THE SAME |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A201 | Request for examination | ||
| E902 | Notification of reason for refusal | ||
| AMND | Amendment | ||
| E601 | Decision to refuse application | ||
| AMND | Amendment | ||
| X701 | Decision to grant (after re-examination) | ||
| GRNT | Written decision to grant |